Post on 11-Sep-2021
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Introduction
Introduction
Data Covered
The series focuses on light metal ternary systems and includes phase equilibria of importance for alloydevelopment, processing or application, reporting on selected ternary systems of importance to industriallight alloy development and systems which gained otherwise scientific interest in the recent years.
General
The series provides consistent phase diagram descriptions for individual ternary systems. Therepresentation of the equilibria of ternary systems as a function of temperature results in spacial diagramswhose sections and projections are generally published in the literature. Phase equilibria are described interms of liquidus, solidus and solvus projections, isothermal and pseudobinary sections; data on invariantequilibria are generally given in the form of tables.
The world literature is thoroughly and systematically searched back to the year 1900. Then, thepublished data are critically evaluated by experts in materials science and reviewed. Conflicting informationis commented upon and errors and inconsistencies removed wherever possible. It considers those, and onlythose data, which are firmly established, comments on questionable findings and justifies re-interpretationsmade by the authors of the evaluation reports.
In general, the approach used to discuss the phase relationships is to consider changes in state and phasereactions which occur with decreasing temperature. This has influenced the terminology employed and isreflected in the tables and the reaction schemes presented.
The system reports present concise descriptions and hence do not repeat in the text facts which canclearly be read from the diagrams. For most purposes the use of the compendium is expected to be self-sufficient. However, a detailed bibliography of all cited references is given to enable original sources ofinformation to be studied if required.
Structure of a System Report
The constitutional description of an alloy system consists of text and a table/diagram section which areseparated by the bibliography referring to the original literature (see Fig. 1). The tables and diagrams carrythe essential constitutional information and are commented on in the text if necessary.
Where published data allow, the following sections are provided in each report:
Literature Data
The opening text reviews briefly the status of knowledge published on the system and outlines theexperimental methods that have been applied. Furthermore, attention may be drawn to questions which arestill open or to cases where conclusions from the evaluation work modified the published phase diagram.
Binary Systems
Where binary systems are accepted from standard compilations reference is made to these compilations.In other cases the accepted binary phase diagrams are reproduced for the convenience of the reader. Theselection of the binary systems used as a basis for the evaluation of the ternary system was at the discretionof the assessor.
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Introduction
Solid Phases
The tabular listing of solid phases incorporates knowledge of the phases which is necessary or helpfulfor understanding the text and diagrams. Throughout a system report a unique phase name and abbreviationis allocated to each phase.
Phases with the same formulae but different space lattices (e.g. allotropic transformation) aredistinguished by:
– small letters (h), high temperature modification (h2 > h1)(r), room temperature modification(1), low temperature modification (l1 > l2)
– Greek letters, e.g., , '– Roman numerals, e.g., (I) and (II) for different pressure modifications.In the table “Solid Phases” ternary phases are denoted by * and different phases are separated by
horizontal lines.
Heading
Literature Data
Binary Systems
Solid Phases
Pseudobinary Systems
Invariant Equilibria
Liquidus, Solidus, Solvus Surfaces
Isothermal Sections
Miscellaneous
Miscellaneous
Isothermal Sections
Liquidus, Solidus, Solvus Surfaces
Invariant Equilibria
Pseudobinary Systems
Solid Phases
Binary Systems
Text
References
Tables anddiagrams
Temperature-Composition Sections
Temperature-Composition Sections
Thermodynamics
Materials Properties and Applications
Thermodynamics
Materials Properties and Applications
Fig. 1: Structure of a system report
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Introduction
Pseudobinary Systems
Pseudobinary sections describe equilibria and can be read in the same way as binary diagrams. The notationused in pseudobinary systems is the same as that of vertical sections, which are reported under“Temperature-Composition Sections”.
Invariant Equilibria
The invariant equilibria of a system are listed in the table “Invariant Equilibria” and, where possible, aredescribed by a constitutional “Reaction Scheme” (Fig. 2).
The sequential numbering of invariant equilibria increases with decreasing temperature, one numberingfor all binaries together and one for the ternary system.
Equilibria notations are used to indicate the reactions by which phases will be– decomposed (e- and E-type reactions)– formed (p- and P-type reactions)– transformed (U-type reactions)For transition reactions the letter U (Übergangsreaktion) is used in order to reserve the letter T to denote
temperature. The letters d and D indicate degenerate equilibria which do not allow a distinction accordingto the above classes.
Liquidus, Solidus, Solvus Surfaces
The phase equilibria are commonly shown in triangular coordinates which allow a reading of theconcentration of the constituents in at.%. In some cases mass% scaling is used for better data readability(see Figs. 3 and 4).
In the polythermal projection of the liquidus surface, monovariant liquidus grooves separate phaseregions of primary crystallization and, where available, isothermal lines contour the liquidus surface (seeFig. 3).
Isothermal Sections
Phase equilibria at constant temperatures are plotted in the form of isothermal sections (see Fig. 4).
Temperature – Composition Sections
Non-pseudobinary T-x sections (or vertical sections, isopleths, polythermal sections) show the phasefields where generally the tie lines are not in the same plane as the section. The notation employed for thelatter (see Fig. 5) is the same as that used for binary and pseudobinary phase diagrams.
Thermodynamics
Experimental ternary data are reported in some system reports and reference to thermodynamicmodelling is made.
Notes on Materials Properties and Applications
Noteworthy physical and chemical materials properties and application areas are briefly reported if theywere given in the original constitutional and phase diagram literature.
Miscellaneous
In this section noteworthy features are reported which are not described in preceding paragraphs. Theseinclude graphical data not covered by the general report format, such as lattice spacing – composition data,p-T-x diagrams, etc.
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Introduction
Fig
ure
2:
T
ypic
al r
eact
ion s
chem
e
Ag-T
lT
l-B
iB
i-A
gA
g-T
l-B
i
(Tl)
(h)
(T
l)(r
),(A
g)
23
4d
1l
(A
g)
+ (
Bi)
26
1e 5
(Ag
) +
(T
l)(h
) +
Tl 3
Bi
L +
Tl 3
Bi
(A
g)
+ (
Tl)
(h)
28
9U
1
l (
Ag
)+(T
l)(h
)
29
1e 3
l (
Tl)
(h)+
Tl 3
Bi
30
3e 1
l (
Bi)
+T
l 2B
i 3
20
2e 7
l T
l 3B
i+T
l 2B
i 3
19
2e 8
(Tl)
(h)
Tl 3
Bi+
(Tl)
(r)
14
4e 9
L (
Ag
) +
Tl 3
Bi
29
4e 2
(max
)
L (
Ag
) +
(T
l)(h
)
28
9e 4
(min
)
L (
Ag
) +
Tl 2
Bi 3
20
7e 6
(max
)
(Ag
)+(B
i)+
Tl 2
Bi 3
L (
Ag)+
(Bi)
+T
l 2B
i 31
97
E1
(Ag
)+(T
l)(r
)+T
l 3B
i
(Tl)
(h)
Tl 3
Bi
+ (
Tl)
(r),
(Ag
)1
44
D1
(Ag
)+T
l 3B
i+T
l 2B
i 3
L (
Ag
)+T
l 3B
i+T
l 2B
i 31
88
E2
seco
nd b
inar
y
eute
ctic
rea
ctio
nfi
rst
bin
ary e
ute
ctic
rea
ctio
n
(hig
hes
t te
mper
ature
)te
rnar
y m
axim
um
reac
tion
tem
per
atu
re
of
26
1°C
mo
no
var
iant
equil
ibri
um
sta
ble
do
wn
to
lo
w
tem
per
ature
s
seco
nd
tern
ary
eute
ctic
reac
tion
equat
ion o
f eu
tect
oid
reac
tion a
t 144°C
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Introduction
20
40
60
80
20 40 60 80
20
40
60
80
A B
C Data / Grid: at.%
Axes: at.%
δ700
p1
500
400
400°C
γ
300
U e1
700
500
β(h)
400
300
E
300
α400
e2
500°C isotherm, temperature is usualy in °C
liquidus groove to decreasing temperatures
estimated 400°C isotherm
limit of known region
ternary invariantreaction
binary invariantreaction
primary γ-crystallization
20
40
60
80
20 40 60 80
20
40
60
80
Al B
C Data / Grid: mass%
Axes: mass%
L+γ
γ+β(h)
L+γ+β(h)
β(h)
L+β(h)
L
L+α
α
phase field notation
estimated phase boundary
tie line
three phase field (partially estimated)
experimental points(occasionally reported)
limit of known region
phase boundary
γ
Fig. 3: Hypothetical liquidus surface showing notation employed
Fig. 4: Hypothetical isothermal section showing notation employed
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Introduction
References
The publications which form the bases of the assessments are listed in the following manner:[1974Hay] Hayashi, M., Azakami, T., Kamed, M., “Effects of Third Elements on the Activity of Lead
in Liquid Copper Base Alloys” (in Japanese), Nippon Kogyo Kaishi, 90, 51-56 (1974) (Experimental,Thermodyn., 16)
This paper, for example, whose title is given in English, is actually written in Japanese. It was publishedin 1974 on pages 51- 56, volume 90 of Nippon Kogyo Kaishi, the Journal of the Mining and MetallurgicalInstitute of Japan. It reports on experimental work that leads to thermodynamic data and it refers to 16 cross-references.
Additional conventions used in citing are:# to indicate the source of accepted phase diagrams* to indicate key papers that significantly contributed to the understanding of the system.Standard reference works given in the list “General References” are cited using their abbreviations and
are not included in the reference list of each individual system.
60 40 200
250
500
750
A 80.00B 0.00C 20.00
A 0.00B 80.00C 20.00Al, at.%
Tem
pera
ture
, °C
L
32.5%L+β(h)
β(r) - room temperature
β(r)
L+α+β(h)
α+β(h)
α
L+α
phase field notation
concentration ofabscissa element
alloy compositionin at.%
β(h)
modification
β(h) - high temperaturemodification188
temperature, °C
Fig. 5: Hypothetical vertical section showing notation employed
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Introduction
General References
[C.A.] Chemical Abstarts - pathways to published research in the world's journal and patentliterature - http://www.cas.org/
[Curr.Cont.] Current Contents - bibliographic multidisciplinary current awareness Web resource - http://www.isinet.com/products/cap/ccc/
[E] Elliott, R.P., Constitution of Binary Alloys, First Supplement, McGraw-Hill, New York(1965)
[G] Gmelin Handbook of Inorganic Chemistry, 8th ed., Springer-Verlag, Berlin [H] Hansen, M. and Anderko, K., Constitution of Binary Alloys, McGraw-Hill, New York
(1958) [L-B] Landolt-Boernstein, Numerical Data and Functional Relationships in Science and
Technology (New Series). Group 3 (Crystal and Solid State Physics), Vol. 6, Eckerlin, P.,Kandler, H. and Stegherr, A., Structure Data of Elements and Intermetallic Phases (1971);Vol. 7, Pies, W. and Weiss, A., Crystal Structure of Inorganic Compounds, Part c, KeyElements: N, P, As, Sb, Bi, C (1979); Group 4: Macroscopic and Technical Properties of
Matter, Vol. 5, Predel, B., Phase Equilibria, Crystallographic and Thermodynamic Data of
Binary Alloys, Subvol. a: Ac-Au ... Au-Zr (1991); Springer-Verlag, Berlin. [Mas] Massalski, T.B. (Ed.), Binary Alloy Phase Diagrams, ASM, Metals Park, Ohio (1986) [Mas2] Massalski, T.B. (Ed.), Binary Alloy Phase Diagrams, 2nd edition, ASM International,
Metals Park, Ohio (1990) [P] Pearson, W.B., A Handbook of Lattice Spacings and Structures of Metals and Alloys,
Pergamon Press, New York, Vol. 1 (1958), Vol. 2 (1967) [S] Shunk, F.A., Constitution of Binary Alloys, Second Supplement, McGraw-Hill, New York
(1969) [V-C] Villars, P. and Calvert, L.D., Pearson's Handbook of Crystallographic Data for
Intermetallic Phases, ASM, Metals Park, Ohio (1985) [V-C2] Villars, P. and Calvert, L.D., Pearson's Handbook of Crystallographic Data for
Intermetallic Phases, 2nd edition, ASM, Metals Park, Ohio (1991)
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Al–Cu–Fe
Aluminium – Copper – Iron
Cui Ping Wang, Xing Jun Liu, Liming Zhang, Kiyohito Ishida
Literature Data
Critical evaluation of constitutional data in the Al-Cu-Fe system has been done by [1991Leg] covering the
then known literature. The present evaluation updates and amends this work within the same evaluation
program. The investigations on the phase equilibria in the Al-rich portion have been carried out by
[1924Fue, 1925Got, 1928Arc, 1928Gwy, 1932Yam, 1933Rol, 1934Fue, 1939Bra2, 1939Nis, 1940Fin,
1940Hun, 1940Shi, 1940Wie, 1941Bro, 1948Sha, 1950Phr, 1952Han, 1954Phi, 1984Ben, 1992Gay1,
1992Gay2, 1992Zak, 1993Fau1, 1993Fau2, 2000Yok1, 2000Yok2, 2000Yok3, 2001Ros], and two reviews
have been presented by [1961Phi] and [1976Mon]. The Cu-rich equilibria have been studied by [1938Nis,
1939Bra1, 1941Yut] and [1952Haw] and the Fe-rich equilibria by [1939Bra1]. The effect of small amount
of Fe on the phase equilibria in the Al-Cu alloys was reported by [2001Liu], and that of Cu on site
occupancy and diffusion behavior in the Al-Fe alloys was studied by [1997And, 2002Ban] and [1998Akd],
respectively. [1997Oht] determined the liquid/solid equilibria in the Cu-Fe side on the basis of
thermodynamic calculation and diffusion couple technique, and the extensive investigation of [1997Oht]
was continued by [1998Wan], in which solid/solid equilibria and an order-disorder transition of the bcc
phase are included. More recently, [2002Zha, 2003Zha1, 2003Zha2, 2003Zha3, 2003Zha4] carried out
detailed experimental investigations of the phase equilibria in the Al-rich portion around the icosahedral
quasicrystalline phase region on the basis of the techniques of differential thermal analysis, magnetothermal
analysis, scanning electron microscopy and X-ray diffraction. [2003Mie] presented a thermodynamic
assessment for the phase equilibria in the Cu-Fe side portion.
The different fields of crystallization are proposed by [1939Bra2] and [1971Pre], but in [1939Bra2] the
phase 1 is missing and in [1971Pre] the compositions given are not in good agreement with their published
diagram. General studies about the system have been proposed by [1935Bos, 1936Bra, 1940Bra, 1955Tur,
1956Spe, 1969LeM, 1972Miu, 1972Pro, 1973Kow, 1975Wac, 1978Pan1, 1981Bre] and [1987Str]. In
particular, in the past decade, enormous investigations on crystal structure and physical and mechanical
properties of icosahedral quasicrystalline phase have been performed by [1991Aud1, 1991Aud2, 1991Bes,
1991Che1, 1991Che2, 1991Fau, 1991Jan, 1991Men, 1991Lei, 1991Liu1, 1991Liu2, 1991Qui, 1991Wu,
1991Zha, 1992Che1, 1992Che2, 1992Eib, 1992Mat, 1992Nas, 1993Ban, 1993Bes, 1993Lee, 1993Men,
1993Was, 1994Bes, 1994Fre1, 1994Fre2, 1994Law, 1994Lef, 1995Div, 1996Qui, 1997Div, 1997Ham,
1997Pop, 1997Ros, 1997She, 1998Dun, 1998Ma, 2000Bou, 2000Dun, 2000Gre1, 2000Gre2, 2000Jon,
2000Nak, 2000Sha, 2000Ste, 2000Uch, 2001Bar, 2001Cai, 2001Gui, 2001Jon, 2001Sur, 2001Guo,
2002Hir, 2002Gre, 2002Kra, 2002Sha].
Binary Systems
The Al-Cu binary system was reviewed by [1985Mur], and has been adopted from [1994Mur] with
modification of [1998Liu], where it is found that earlier reported phase 0 does not exist, and the earlier
reported two-phase equilibrium ( 0+ 1) was determined as second order reaction 1- 0 in the composition
range of 62-68 at.% Cu. The Al-Fe and Cu-Fe binary systems have been accepted from [1993Kat] and
[2001Tur], respectively.
Solid Phases
Data on all solid phases are given in Table 1. The existence of a stable single icosahedral quasicrystalline
phase ( i) has been reported for the first time by [1987Tsa1] and [1987Tsa2] and later on by a series of
research groups [1988Bou, 1988Hir, 1988Ish, 1988Tsa, 1989Dev, 1989Don, 1989Eba]. The formation
range of the icosahedral phase found by [1987Tsa1] is close to the composition range of a ternary phase
discovered by [1939Bra2] and referred to as phase (about 20 to 26 at.% Cu and 12 to 13 at.% Fe) the
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Al–Cu–Fe
structure of which was left unidentified. [1990Cal] has demonstrated that the phase is indeed the
icosahedral phase. Following [1990Fau1, 1991Fau], the composition range of the icosahedral phase is
around Fe12.5Cu25.5Al62. [1939Bra2, 1989Don, 1990Fau1, 2000Yok1, 2000Yok2] and [2003Zha1] agree
that the icosahedral i phase formation proceeds following a peritectic reaction.
There is also a general agreement that the Al-Cu-Fe icosahedral phase corresponds to an F type structure
which can be seen as an ordered F superstructure of the primitive six dimensional (6D) hypercubic lattice
[1988Ish, 1989Dev, 1989Eba] and exists as a single phase stable at 800°C. At lower temperatures (about
600°C) the structure strongly depends on the composition of the alloy. For compositions around
Fe12.5Cu25.5Al62 the icosahedral phase is perfect, without phasons and without any modification even after
annealing for 4 days at 500°C.
For compositions different but close to this domain, either a modulated structure appears [1991Aud1] or
even a transformation towards periodic phases (rhombohedral) [1990Den]. Further investigations of crystall
structure with an emphasis of phase transition and thermal stability of Al-Cu-Fe quasicrystalline in bulk and
layer states have been carried out by many groups on the basis of experiment and theory [1991Aud1,
1991Aud2, 1991Bes, 1991Che, 1991Dub, 1991Eib, 1991Fau, 1991Jan, 1991Lei, 1991Liu1, 1991Liu2,
1991Men, 1991Wu, 1991Zha, 1992Che1, 1992Che2, 1992Eib, 1992Hay, 1992Lu, 1992Mat, 1992Nas,
1993Ban, 1993Lee, 1993Men, 1993Nas, 1993Was, 1994Bes, 1994Fre1, 1994Fre2, 1994Law, 1994Lef,
1995Div, 1996Log, 1996Qui, 1997Div, 1997Ham, 1997Pop, 1997Ros, 1997She, 1998Dun, 1998Ma,
1999Rot, 2000Bou, 2000Dun, 2000Gre1, 2000Gre2, 2000Jon, 2000Nak, 2000Sha, 2000Ste, 2000Uch,
2001Cai, 2001Gui, 2001Guo, 2001Qia, 2002Gre, 2002Kra, 2002Sha].
Large grains with an average size of 0.2 mm were obtained by [1987Tsa2] and [1990Cal]. Further
replacement of Cu by Al in (Fe15Cu20-xAl65+x) alloys was said to reveal a three-phase structure of (Al)+
FeAl3+FeCu2Al7 [1988Tsa].
Pseudobinary Systems and Temperature – Composition Sections
The section Al3Fe-Al2Cu was reported by [1928Arc] as a pseudobinary system, however, this section is not
exactly pseudobinary [1928Arc, 1990Fau2]. Some pseudobinary phase diagrams along the composition
lines of the Cu35Al65 - Fe20Cu15Al65, Fe1.5Cu30Al68.5 - Fe1.5Cu40Al58.5, Fe3Cu30Al67 - Fe3Cu40Al57 and
Fe5Cu30Al65 - Fe5Cu40Al55 were determined by [2000Yok1, 2000Yok2], which show that the primary
crystal from the melt is the phase, and then i phase is formed by a peritectic reaction. [2000Yok1 and
2000Yok2] only focused on the two-phase (L+ i) region, and did not give detailed information. In addition,
it was found that some phase equilibria do not follow the phase equilibria rules.
More recently, [2003Zha2] reported a series of vertical phase diagrams, including the pseudobinary systems
along the Fe22.8Al77.2-Cu57.5Al42.5 (Fig. 1), Cu10Al90 - Fe20Cu30Al50 (Fig. 2), Cu37.5Al62.5 - Fe20Cu21Al59
(Fig. 3), Fe14.5Al85.5 - Fe3.5Cu50Al46.5 (Fig. 4) and the vertical section diagrams with 25 at.% Cu, 5 at.%
Fe, 7.5 at.% Fe, 10 at.% Fe, and 12 at.% Fe (Figs. 5-9). In the investigations of [2002Zha, 2003Zha2], the
phase equilibria of the i phase and other related phases are precisely described, and the icosahedral phase
is formed via a peritectic reaction (L+ + i) at 882°C, the shrinkage of the phase field with decreasing
temperature gives an indication of the compositional influence on the stability of the icosahedral phase.
[1939Bra1, 1939Bra2, 1971Pre] reported the existence of slightly distorted structures of the phase. In
Fig. 1 [2003Zha2] shows them as two phases, labeled as 1 and 2, based on of the results of [1939Bra1,
1939Bra2 and 1971Pre]. However, none of the authors [1939Bra1, 1939Bra2, 1971Pre, 2003Zha1,
2003Zha2, 2003Zha3] studied these structures in details.
[2003Zha2] did not distinguish between 1 and 2 except for the vertical section shown in Fig. 3, where
these two phases are distinguished. This is mainly concluded from their existence in the binary Al-Cu
system and supported by a few DTA and MTA measurements. According to this section a ternary reaction
corresponding to the 1 and 2 transition occurs at a temperature between ~595 and 565°C, involving liquid
phase. Below this temperature only 2 should exist. However, [2003Zha1, 2003Zha2, 2003Zha3] did not
consider this fact in the reaction scheme and in other vertical sections and used as notation in all figures.
Further investigations would be required to clarify phase equilibria involving different modifications of the
phase, as well as the 1 and 2 phases.
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Al–Cu–Fe
It should be noted that the vertical sections presented here from [2003Zha2] are not always coherent with
the accepted binary systems.
[1998Wan] presented the calculated vertical section diagrams of 5, 10, and 15 mass% Al with a
consideration of the ordered structure of the bcc phase ( Fe), as shown in Figs. 10-12, which indicate that
the B2 ordered phase ( ) is not formed in the 5 mass% Al vertical sections. However, the metastable and
stable A2/B2 ordering reaction (( Fe)/ ) appears in the 10 and 15 mass% Al vertical sections,
respectively; and the miscibility gap of the B2 phase ( ) also appears in 15 mass% Al vertical section.
Invariant Equilibria
Two partial reaction schemes in the Cu-rich and Al-rich corners were proposed by [1938Nis] (Fig. 13), and
[1954Phi, 2003Zha3], respectively. In the Al-rich corner [2003Zha3] presented a detailed Scheil reaction
scheme including solid state reactions, where 13 four-phase equilibria, three three-phase eutectic equilibria,
four three-phase peritectic equilibria, and two three-phase eutectoid reactions are included (Fig. 14). In the
Cu-rich portion the invariant reactions related to the 0 phase are revised, as shown in Fig. 13, because
[1998Liu] reported that no 0 phase exists at high temperature in the Al-Cu system. The reaction at 1048°C,
given as L+T ( Fe)+Cu3Al by [1938Nis], where the phase T was considered to be a ternary compound, is
not compatible as a transition type reaction with the other equilibria, but should be a peritectic type
L+( Fe)+( Fe) Cu3Al.
The invariant reactions are listed in Table 2.
Liquidus Surface
Polythermal projections of the liquidus surface are proposed in Figs. 15 and 16 for the Cu- and Al- rich
corners, respectively. Figure 17 shows combined projection of liquidus surface with tie lines of the
four-phase equilibria based on the works of [1991Leg] and [2003Zha1]. The ternary phase 4, close to i,
is omitted in these figures. A partial liquidus surface diagram in the Al-rich portion and the formation
temperature of i phase is presented by [2000Yok1, 2000Yok2], which is in basic agreement with that
reported by [2003Zha1], who constructed the liquidus surface in the Al-rich portion, as shown in Fig. 16,
where 12 four-phase equilibria with the liquid phase exist.
Isothermal Sections
Figure 18 shows the Al-rich part of the isothermal section at room temperature obtained by [1991Fau] by
combining experimental results of [1990Cal] with previous literature data in the range of compositions
around the icosahedral i phase, in which 4 is not shown. Furthermore, [1992Gay1 and [1992Gay2]
determined the isothermal phase diagrams at temperatures from 550-800°C in the Al-rich region using
scanning electron microscopy and energy dispersive spectroscopy. This study indicates that the B2 ordered
phase ( ) has considerably greater solubility of Cu than previously reported, extending from AlFe to the
composition of about Fe5Cu45Al50. A schematic section at 680°C in the vicinity of the icosahedral region
was determined by [1993Gra] with a combination of the results of [1992Gay1, 1939Bra1]. The results of
[1993Gra] show that at 680°C, three crystalline phases surround the icosahedral region: the monoclinic
phase, the ordered simple cubic ( ) phase and ordered tetragonal 2 phase. [2001Ros] constructed the
isothermal section at 850°C. [1997Oht] has studied the solid/liquid equilibria in the Cu-Fe portion using
diffusion couple method. [1998Wan] performed the experimental determination and thermodynamic
calculation of the phase equilibria in the Cu-Fe side portion with a special attention for A2/B2 ordering
transition. There exists an order-disorder A2/B2 transition in this system, and a stable B2 phase ( ) is
formed over a wide range of compositions from the Al-Fe binary system to the Al-Cu binary system at
800-1000°C (Figs. 19-24). It is interesting to note that a miscibility gap of the bcc phase ( ) was divided
into A2+A2 (( Fe)+Cu3Al), A2+B2 (Cu3Al+ ) and B2+B2 (( (1)+ ( (2)) two-phase regions. [2003Zha3]
determined isothermal sections at 800, 700, 645, 620, 617, 600, 592 and 560°C using SEM/EDS methods
together with structural investigations, as shown in Figs. 25-32, in which the i icosahedral quasicrystalline
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Al–Cu–Fe
phase was found to be in equilibrium with three phases (L, and ) at 800°C, four phases (L, , 2 and )
at 700°C, three phases ( 2, and ) at 645°C, four phases ( 2, two , 3 and ) at 620°C, and four phases
( 2, , 3 and ) below 560°C.
Thermodynamics
[1993Saa1, 1993Saa2] reported the enthalpy of formation of the i, 2, and phases using differential
thermal analysis. It is shown that the heat formation of the 2 and i phases are of the same order of
magnitude, although the value of 2 is slightly higher than that of the i phase. [1994Was] theoretically
constructed the free energy function for quasicrystalline phase to investigate the phase transition.
[1992Wan] determined specific heat of phason-strained quasicrystals, and [1997Las] reported the
low-temperature specific heat (0.1<T<10K) of several quasicrystals, and [1999Wan] measured the heat
capacities of two Fe12.5Cu25Al62.5 samples containing icosahedral quasicrystals and B2 structure,
respectively, by means of a high-precision automatic adiabatic calorimeter over the temperature range of
75-385 K. [1999Hol] measured the melting entropy by differential thermal analysis, and pointed out that
the entropy of mixing plays an important role in the stabilization of the quasicrystalline phase. The
thermodynamic assessments of the Al-Cu-Fe system have been performed by [1997Oht, 1998Wan,
2003Mie] within the framework of the CALPHAD method. [1997Oht] calculated the liquid/solid phase
equilibria in the Cu-Fe side portion using regular solution model for the liquid, fcc ( Fe) and bcc phases.
[1998Wan] extended the work of [1997Oht] to make a thermodynamic assessment of the Al-Cu-Fe ternary
system, in which the thermodynamic assessments of Al-Fe [1998Ohn], Al-Cu [1998Liu] and Cu-Fe
[1995Che] binary systems are adopted, and two-sublattice model is used to describe the free energy of the
bcc ( ) phase in order to describe the A2/B2 ordering reaction. In [1998Wan] thermodynamic assessment
is focused on the phase equilibria at Cu-Fe side, and a prediction of the phase equilibria in Al-rich portion
is given, and the ternary compounds are not included. Recently, a thermodynamic description of the phase
equilibria at the Cu-Fe side was made by [2003Mie], where the ordering of the bcc phase was not
considered.
Notes on Materials Properties and Applications
Considerable investigations were focused on the electronic transport properties of quasicrystals [1990Kle,
1992Chi, 1993Dre, 1992Lin, 1992Poo, 1994Tra, 1995Tra, 1999Bra, 1999Rot, 2000Bel1, 2000Bel2,
2000Bil, 2000Bra1, 2000Bra2, 2000Gre1, 2000Gre2, 2000Hab, 2000Lan1, 2000Mad, 2000Miz, 2000Pre,
2000Rap, 2000Smo, 2000Zha]. Other properties such as mechanical properties [2000Wan, 2000Tre,
2000Wu2, 2002Dub], corrosion behavior [2000Rue], oxidation behavior [2000Weh], creep behavior
[2000Gia] were studied. The magnetic behavior of Cu-rich Al-Cu-Fe alloys in the solid and liquid states has
been discussed and reviewed by [1975Wac, 1978Pan1] and [1978Pan2]. The magnetic properties of
mechanically alloyed nanocrystalline phase was also reported by [1999Tor] and [2001Kim] and the
tribological properties of sintered bulk icosahedral samples were studied by [2000Bru].
Recently, some investigations have been performed on the technological application of quasicrystals by
means of coatings and composites, and a review was reported by [2000Dub]. [2000Fle] and [2000Lan2,
2002Fik] have studied the quasicrystalline coatings by plasma spraying process. [2000Lee1] and [2000Blo]
developed composite materials for metal/quasicrystal and polymer/quasicrystal, by means of gas-atomized
process, respectively.
Miscellaneous
The icosahedral quasicrystalline phase was found to coexist in rapidly quenched Fe15Cu20Al65 alloys with
a crystalline bcc-Mg32(Al,Zn)49 type phase [1988Che]. The effect of iron on the precipitation hardening of
Al-Cu-Fe alloys has been studied by means of hardness tests, dilatation, electrical resistivity and yield
strength measurements [1940Fin] and by X-ray powder diffraction analysis [1940Hun]; due to the
formation of ternary constituents, iron was found to remove Cu from Al-base alloys and thus to effectively
suppress the ageing of Al-Cu alloys [1940Fin] and [1940Hun]. [1972Pro] examined the iron effect (up to
5
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Al–Cu–Fe
12% Fe) on the transformation of the supersaturated Cu3Al phase. A solution of 0.5% aqueous hydrofluoric
acid was shown to be a useful universal etchant to reveal the microstructure of iron containing Al-base
alloys [1973Kow]. The influence of silicon on the phase equilibria and formability of the icosahedral
quascrystalline phase have been studied in the quaternary Al-Cu-Fe-Si system by DTA, X-ray and
microstructural analysis [1986Gul, 1987Che, 1987Zak, 2000Lee2].
Some investigations on phase formation of icosahedral phase were carried out by mechanical alloying
process [2000Sri, 2001Bar, 2001Muk, 2002Bar, 2002Tch]. Solidification behavior of quasicrystal phase
was studied by [1994Hol, 1996Zha, 1996Gru, 1998Hol, 1998Vol, 2002Yok]. Laser sputtering technique
was used to study the surface of quasicrystal [2002Mel] and to synthesis Al-base icosahedral
quasicrystalline powder [2000Nic]. The melting behavior of Bi and Pb nanoparticles embedded in Al-Cu-Fe
icosahedral matrix by rapid solidification were reported by [2001Sin, 2000Sin]. A study on the effect of
pressure on Al-Cu-Fe icosahedral phase was performed by [1999Pon]. [2000Bu] investigated the reaction
between Al-Cu-Fe quasicrystal phase and nitrogen oxides at high temperature, and indicated that the
quasicrystalline Al-Cu-Fe powder has a high capacity for the decomposition of nitrogen oxides at high
temperature. [2000Wu1] and [2000Wu2] investigated the surface microstructure of surface deformed areas
of Al-Cu-Fe icosahedral quasicrystal using electron microscopy.
References
[1924Fue] Füss, V., “On the Constitution of Ternary Al-Alloys” (in German), Z. Metallkd., 16, 24-25
(1924) (Equi. Diagram, Experimental, 5)
[1925Got] Goto, M., Mishma, T., “Studies on Several Aluminium Alloys” (in Japanese), Nippon
Kogyo Kwai Shi, 41, 1-21 (1925) (Equi. Diagram, Experimental)
[1928Arc] Archer, R.S., Fink, W.L., “Correspondence on Gwyer's Paper”, J. Inst. Met., 40, 350-358
(1928) (Equi. Diagram, Experimental, *, 2)
[1928Gwy] Gwyer, A.G.C., Phillips, H.W.L., Mann, L., “Alloys of Aluminium with Copper-Silicon
and Iron”, J. Inst. Met., 40, 297-350 (1928) (Equi. Diagram, Experimental, *, 34)
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1932Yam] Yamaguchi, K., Nakamura, I., “Constitution of Aluminium-Base Al-Cu-Fe Alloys” (in
Japanese), Rikagaku Kenkyusho Iho, 11, 815-833 (1932) (Equi. Diagram, Experimental, *,
5)
[1933Rol] Roll, F., “The Influence of Aluminium and Cobalt on the Miscibility Gap of the Iron-Copper
System in the Solid State” (in German), Z. Anorg. Allg. Chem., 216, 133-137 (1933)
(Experimental, 8)
[1934Fue] Füss, V., “Special Metallography of Aluminium and of its Alloys,
Aluminium-Iron-Copper” (in German), Berlin, translated by Anderson, R.J., Sherwood
Press Inc., Cleveland 1936, 116-123 and 207-219 (1934) (Review, 5)
[1935Bos] Bosshard, M., “Diffusion Research as a Means for the Simple Detection of Compound
Formation Between Alloy Constituents in Ternary and Polynary Systems” (in German),
Aluminium, 17, 477-481 (1935) (Experimental, 1)
[1936Bra] Bray, J.L., Carrythers, M.E., Heyer, R.H., “Coefficient of Equivalence of Iron with Respect
to Aluminium in Aluminium Bronze”, Trans. AIME., 122, 337-348 (1936) (Experimental,
6)
[1938Nis] Nishimura, H., Hisatsune, C., “The Constitution of the Alloys of Copper-Rich Cu-Al-Fe
System” (in Japanese), Nippon Kinzoku Gakkaishi (Trans. Jpn. Inst. Met.,), 2, 597-604
(1938) (Experimental, *, 5)
[1939Bra1] Bradley, A.J., Goldschmidt, H.J., “An X-Ray Study of Slowly Cooled
Iron-Copper-Aluminium Alloys. Part I. Alloys Rich in Iron and Copper”, J. Inst. Met., 65,
389-401 (1939) (Experimental, Crys. Structure, *, 10)
6
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Al–Cu–Fe
[1939Bra2] Bradley, A.J., Goldschmidt, H.J., “An X-Ray Study of Slowly Cooled
Iron-Copper-Aluminium Alloys. Part II. Alloys Rich in Aluminium”, J. Inst. Met., 65,
403-418 (1939) (Experimental, Crys. Structure,*, 6)
[1939Nis] Nishimura, H., “An Investigation of Super-Duralumin (Effect of Iron)” (in Japanese),
Nippon Kinzoku Gakkaishi (Trans. Jpn. Inst. Met.), 3, 420-424 (1939) (Experimental, *, 10)
[1940Bra] Bradley, A.J., Bragg, W.L., Sykers, C., “Researches into the Structure of Alloys”, J. Iron
Steel Inst., London, 63-156 (1940) (Equi. Diagram, Experimental, Review, *, 2)
[1940Fin] Fink, W.L., Smith, D.W., Willey, L.A., “Precipitation Hardening of High Purity Binary and
Ternary Aluminum-Copper Alloys”, Amer. Soc. Metals: Age Hardening of Metals, 31-55
(1940) (Experimental, 11)
[1940Hun] Hunsicker, H.Y., “Precipitation Hardening Characteristics of High Purity
Aluminum-Copper and Aluminum-Copper-Iron Alloys”, Amer. Soc. Metals: Age
Hardening of Metals, 56-81 (1940) (Crys. Structure, Experimental, 28)
[1940Shi] Shinoda, G., “X-Ray Studies on the Age-Hardening of Super-Duralumin. Part II” (in
Japanese), Nippon Kinzoku Gakkaishi (Trans. Jpn. Inst. Met.), 4, 347-349 (1940) (Crys.
Structure, Experimental, 3)
[1940Wie] Wiehr, H., “On the Systems Aluminium-Copper-Silicon and Aluminium-Copper-Iron” (in
German), Dissertation, Alum. Arch., 31, 5-14 (1940) (Crys. Structure, Experimental, 14)
[1941Bro] Brown, R.H., Fink, W.L., Hunter, M.S., “Measurement of Irreversible Potentials as a
Metallurgical Research Tool”, Trans. AIME, 143, 115-122 (1941) (Experimental, 14)
[1941Yut] Yutaka, A., “The Equilibrium Diagram of the Iron-Bearing Aluminium-Bronzes” (in
Japanese), Nippon Kinzoku Gakkaishi (Trans. Jpn. Inst. Met.), 5, 136-157 (1941) (Equi.
Diagram, Experimental, *, 26)
[1948Sha] Sharma, A.S., “Metallography of Commercial Alloys of the Duralumin Type, Part II”,
Trans. Indian Inst. Met., 1(1), 30-44 (1948) (Experimental, 9)
[1950Phr] Phragmen, G., “On the Phases Occurring in Alloys of Aluminium with Copper, Magnesium,
Manganese, Iron and Silicon”, J. Inst. Met., 77, 489-552 (1950) (Equi. Diagram,
Experimental, #, *, 67)
[1952Han] Hanemann, H., Schrader, A., “Ternary Alloys of Aluminium - Examples for the
Crystallization in Ternary Systems”, in “Atlas Metallographicus” (in German), Verlag
Stahleisen, Düsseldorf, 3(2), 70-73, (1952), Tafel 6-8 (Equi. Diagram, Review, 14)
[1952Haw] Haworth, J.B., Hume-Rothery, W., “The Effect of Four Transition Metals on the / Brass
Type of Equilibrium”, Philos. Mag., VII, 43, 613-629 (1952) (Experimental, 23)
[1953Sch] Schubert, K., Poesler, U., Kluge, M., Anderko, K., Haerle, L., “Crystallographic Results on
Phases with Strong Correlations” (in German), Naturwissenschaften, 40, 437 (1953) (Crys.
Structure, Experimental, 3)
[1954Phi] Phillips, H.W.L., “On the Constitution of Alloys of Aluminium, Copper and Iron”, J. Inst.
Met., 82, 197-212 (1954) (Equi. Diagram, Experimental, #, *, 21)
[1955Tur] Turkin, V.D., Bakhvalova, R.G., “The Phase Diagram Al-Cu-Fe” (in Russian), Issled.
Splavov Tsvet. Metallov, 1, 98-105 (1955) (Equi. Diagram, Experimental, 0)
[1956Bow] Bown, M.G., Brown, P.J., “The Structure of FeCu2Al7 and T(CoCuAl)”, Acta Crystallogr.,
9, 911-914 (1956) (Crys. Structure, 12)
[1956Spe] Sperry, P.R., “The Intermetallic Phases in 2024 Aluminum Alloys”, Trans. Am. Soc. Met.,
48, 904-918 (1956) (Experimental, 11)
[1958Bro] Brown, P.J., “A Crystallographic Investigation of the Structures of some Intermetallic
Compounds”, Thesis, Univ. Cambridge, England, 1-158 (1958) (Crys. Structure,
Experimental, 70)
[1961Bla] Black, P.J., Edwards, O.S., Forsyth, J.B., “The Structure of (AlCuFe)”, Acta Crystallogr.,
14, 993-998 (1961) (Crys. Structure, Experimental, 17)
[1961Phi] Phillips, H.W.L., “Equilibrium Diagrams of Al-Alloy Systems”, in “Information Bulletin
25”, Aluminium Development Association, London, 49-53 (1961) (Equi. Diagram,
Review, 0)
7
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Al–Cu–Fe
[1969LeM] Le Maitre, F., “Phase Transformation of Cupro-Aluminum Alloys” (in French),
Cuivres-Laitons-Alliages, 107, 8-21 (1969) (Experimental, 10)
[1971Pre] Prevarskiy, A.P., “Study of the Fe-Cu-Al System”, Russ. Metall., (4), 154-156 (1971),
translated from Izvest. Akad. Nauk SSSR. Met., (4), 220-222 (1971) (Equi. Diagram,
Experimental, 11)
[1972Miu] Miura, I., Hamanaka, H., “Mechanical Properties and Thermal Stabilities of Al-CuAl2-Si,
Al-CuAl2-NiCu3Al6 and Al-CuAl2-FeCu2Al7 Ternary Eutectic Composites” (in Japanese),
Nippon Kinzoku Gakkai Shi, 36, 1224-1231 (1972) (Experimental, Phys. Prop., Mechan.
Prop., 14)
[1972Pro] Prowans, S., Wysiecki, M., “Effect of Fe on the Structure and the Phase Transformation of
Al Bronzes. Part II” (in Polish), Arch. Hutn., 17, 379-393 (1972) (Experimental, Crys.
Structure, 25)
[1973Cor] Corby, R.N., Black, P.J., “The Structure of FeAl2 by Anomalous Dispersion Methods”, Acta
Crystallogr., B29, 2669-2677 (1973) (Crys. Structure, Experimental, 31)
[1973Kow] Kowatschewa, R., Dafinowa, R., Kamenowa, Z., Momtschilov, E., “Metallographic
Determination of Intermetallic Compounds in Aluminium Alloys” (in German), Prakt.
Metallogr., 10, 131-143 (1973) (Experimental, Crys. Structure, 9)
[1975Wac] Wachtel, E., Pantasis, A., “Magnetic Behaviour of Cu-Rich Cu-Al-Fe Alloys in the Solid
and Liquid State” (in German), Z. Metallkd., 66, 172-178 (1975) (Experimental, Magn.
Prop., 19)
[1976Mon] Mondolfo, L.F., “Al-Cu-Fe”, in “Aluminum Alloys: Structure and Properties”,
Butterworths, London, 491-493 (1976) (Equi. Diagram, Review, Crys. Structure, Phys.
Prop., 30)
[1978Pan1] Pantasis, A., Wachtel, E., “Constitution and Magnetic Properties of Solid and Liquid
Al-Cu-Fe Alloys” (in German), Z. Metallkd., 69, 50-59 (1978) (Equi. Diagram,
Experimental, Magn. Prop., Crys. Structure, 26)
[1978Pan2] Pantasis, A., Wachtel, E., “Magnetic Moment in Liquid Fe0.25-Cu-Al Alloys and the
Transition from the Magnetic to the Non-Magnetic State”, J. Magnt. Magn. Mater., 9,
264-269 (1978) (Experimental, Magn. Prop., 20)
[1981Bre] Brezina, P., “Heat Treatment of Complex Aluminium Bronzes”, Int. Met. Rev., 27, 77-120
(1981) (Experimental, Review, 210)
[1984Ben] Bennett, D.A., Kirkwood, D.H., “Phase Equilibria Between Solid Aluminium and Liquid in
Al-Cu and Al-Cu-Fe Systems”, Met. Sci., 18, 17-21 (1984) (Experimental, Equi. Diagram,
15)
[1985Mur] Murray, J.L., “The Al-Cu System”, Int. Met. Rev., 30, 211-233 (1985) (Equi. Diagram,
Review, 230)
[1986Gul] Guldin, I.T., Zakharov, A.M., Arnold, A.A., “The Effect of Fe and Si on the Liquidus
Temperature and Phase Composition of an Al-Alloy with 40% Cu” (in Russian), Izv. Vyss.
Uchebn. Zaved., Tsvetn. Metall., (4), 90-95 (1986) (Equi. Diagram, Experimental, 8)
[1987Che] Chernova, E.P., Guldin, I.T., Zakharov, A.M., Arnold, A.A., “Polythermal Sections of the
Al-Cu-Fe-Si System in the Concentration Range of Anodic Deposits of the Electrolytic
Refining of Aluminium” (in Russian), Izv. Vyss. Uchebn. Zaved., Tsvetn. Metall., (4), 70-75
(1987) (Equi. Diagram, Experimental, 4)
[1987Str] Streltsov, F.N., Klimov, V.M., “Influence of Aluminum on the Solution of Iron in Liquid
Copper”, Russ. Metall., (2), 33-39 (1987), translated from Izv. Akad. Nauk SSSR, Met., (2),
32-38 (1987) (Experimental, 17)
[1987Tsa1] Tsai, A.P., Inoue, A., Masumoto, T., “Preparation of a New Al-Cu-Fe Quasicrystal with
Large Grain Sizes by Rapid Solidification”, J. Mater. Sci. Lett., 6, 1403-1405 (1987) (Crys.
Structure, Equi. Diagram, Experimental, 11)
[1987Tsa2] Tsai, A.P., Inoue, A., Masumoto, T., “A Stable Quasicrystal in Al-Cu-Fe System”, Japan.
J. Appl. Phys., 26, L1505-L1507 (1987) (Crys. Structure, Experimental, 8)
8
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Al–Cu–Fe
[1987Zak] Zakharov, A.M., Guldin, J.T., Arnold, A.A., “Effect of Si on Phase Equilibria in Alloys of
the Al-Cu-Fe System with 40% Cu and 0-10% Fe” (in Russian), Izv. Vyss. Uchebn. Zaved.,
Tsvetn. Metall., (2), 55-58 (1987) (Equi. Diagram, Experimental, 4)
[1988Bou] Bouchet-Fabre, B., Laridjani, M., Chenoufi, A., Dixmier, J., “X-Ray Study of the
Quasi-Crystalline Structure of Al-Cu-Fe Alloys”, in “Proc. ILL/CODEST Workshop on
Quasicrystalline Materials”, Janot, Ch., Dubois, J.M. (Eds.), Grenoble, 136-147, World
Scientific, Singapore (1988) (Crys. Structure, Experimental, 6)
[1988Che] Cheng, Y., Hui, M., Wu, X., Yang, D., Chen, X., Li, F., “R-Phase and Icosahedral Phase in
Al-Fe-Cu Alloy”, Chin. Phys. Lett., 5(12), 529-532 (1988) (Crys. Structure, Equi. Diagram,
6)
[1988Hir] Hiraga, K., Zhang, B.P., Hirabayashi, M., Inoue, A., Masumoto, T., “Highly Ordered
Icosahedral Quasicrystal of Al-Cu-Fe Alloy Studied by Electron Diffraction and
High-Resolution Electron Microscopy”, Japan. J. Appl. Phys., 27, L951-L953 (1988)
(Crys. Structure, Experimental, 6)
[1988Ish] Ishimasa, T., Fukano, Y., Tsuchimori, M., “Quasicrystal Structure in Al-Cu-Fe Annealed
Alloy”, Philos. Mag. Lett., 58, 157-165 (1988) (Crys. Structure, Experimental, 16)
[1988Ray] Raynor, G.V., Rivlin, V.G., “Phase Equilibria in Iron Ternary Alloys”, in “The Institute of
Metals”, London, 42 (1988) (Equi. Diagram, Review, 6)
[1988Tsa] Tsai, A.P., Inoue, A., Masumoto, T., “New Quasicrystals in Al65Cu20M15 (M = Cr, Mn or
Fe) Systems Prepared by Rapid Solidification”, J. Mater. Sci. Lett., 7, 322-326 (1988)
(Crys. Structure, Experimental, 17)
[1989Dev] Devaud-Rzepski, J., Quivy, A., Calvayrac, Y., Cornier-Quiquandon, M., Gratias, D.,
“Antiphase Domains in Icosahedral Al-Cu-Fe Alloy”, Philos. Mag. B, B60, 855-869 (1989)
(Crys. Structure, Experimental, 18)
[1989Don] Dong, C., De Boissieu, M., Dubois, J.M., Pannetier, J., Janot, C., “Real-Time Study of the
Growth of Al-Cu-Fe Quasicrystals”, J. Mater. Sci. Lett., 8, 827-830 (1989) (Equi. Diagram,
Experimental, 12)
[1989Eba] Ebalard, S., Spaepen, F., “The Body-Centered-Cubic-Type Icosahedral Reciprocal Lattice
of the Al-Cu-Fe Quasi-Periodic Crystal”, J. Mater. Res., 4, 39-43 (1989) (Crys. Structure,
12)
[1990Cal] Calvayrac, Y., Quivy, A., Bessiere, M., Lefebvre, S., Cornier-Quiquandon, M. and Gratias,
D., “Icosahedral AlCulFe Alloys: Towards Ideal Quasicrystals”, J. Phys. (France), 51,
417-431 (1990) (Crys. Structure, Experimental, 25)
[1990Den] Denoyer, F., Heger, G., Lambert, M., Audier, M., Guyot, P., “X-Ray and TEM Studies of
Al-Fe-Cu Dodecahedral Particles: Characterization of their Microcrystalline State of
Pseudo-Icosahedral Symmetry”, J. Phys. (France), 51, 651-660 (1990) (Crys. Structure,
Experimental, 14)
[1990Fau1] Faudot, F., Quivy, A., Calvayrac, Y., Gratias, D., Harmelin, M., “About the Al-Cu-Fe
Icosahedral Phase Formation”, “Rapidly Quenched Materials”, 7th Intern. Conf.,
Stockholm, 1990 (Equi. Diagram, Experimental, Crys. Structure, 14)
[1990Fau2] Faudot, F., Harmelin, M., Legendre, B., “The Al3Fe-Al2Cu Section in the Al-Cu-Fe
System” (in French), paper presented at 16emes Journrees d'Etude des Equilibres entre
Phases, Marseille, March 1990, 123-124 (Equi. Diagram, #, 4)
[1990Kle] Klein, T., Gozlan, A., Berger, C., Cyrot-Lackmann, F., Calvayrac, Y., Quivy, A.,
“Anomalous Transport Properties in Pure AlCuFe Icosahedral Phases of High Structural
Quality”, Europhys. Lett., 13(2), 129-134 (1990) (Experimental, Crys. Structure, Phys.
Prop., 18)
[1991Aud1] Audier, M., Brechet, Y., de Boissieu, M., Guyot, P., Janot, C., Dubois, J.M., “Perfect and
Modulated Quasicrystals in the System Al-Fe-Cu”, Philos. Mag. B, 63(6), 1375-1393
(1991) (Crys. Structure, Experimental, 29)
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Al–Cu–Fe
[1991Aud2] Audier, M., “Reversible Icosahedral-Rhombohedral Transition via a Modulated Icosahedral
State”, Int. Workshop Methods Struct. Anal. of Modulated Struct. and Quasicrystals
Lekeitio-Bilbao, Spain, 555-571 (1991) (Crys. Structure, Experimental, 29)
[1991Bes] Bessiere, M., Lefebvre, S., Quivy, A., Devaud-Rzepski, J., Calvayrac, Y., “High Resolution
Bragg Peak Profiles of Al62.3Cu25.3Fe12.4 Icosahedral Alloy: A New Type of
Morphological Transformation”, Int. Workshop Methods Struct. Anal. of Modulated Struct.
and Quasicrystals Lekeitio-Bilbao, Spain, 587-592 (1991) (Crys. Structure, Experimental,
Phys. Prop., 9)
[1991Che] Chen, L., Chen, X., “A Study of a Stable Aluminum-Copper-Iron Quasicrystal in Solid and
Liquid State”, Phys. Status Solidi B, 169(1), 15-21 (1992) (Equi. Diagram, Experimental, 9)
[1991Che1] Cheng, Y.F., Hui, M.J., Li, F.H., “An Intermediate State between the Decagonal and
Monoclinic Phases in an Al-Cu-Fe Alloy”, Philos. Mag. Lett., 64(3), 129-132 (1991) (Crys.
Structure, Experimental, 18)
[1991Che2] Cheng, Y.F., Hui, M.J., Li, F.H., “A New Commensurate Phase and its Ralated
Incommensurate Phase in Al-Cu-Fe Alloy”, Philos. Mag. Lett., 63(1), 49-55 (1991) (Crys.
Structure, Experimental, 20)
[1991Dub] Dubois, J.M., Dong, C., Janot, C., de Boissieu, M., Audier, M., “The Reversible
Crystal-Quasicrystal Transitions in Icosahedral Aluminum-Copper-Iron Alloys”, Phase
Transitions, 32(1-4), 3-28 (1991) (Crys. Structure, Experimental, 34)
[1991Eib] Eibschutz, M., Lines, M.E., Chen, H.S., Thiel, F.A., “Structure Difference Between i and T
Phases of Al-Cu-Co and Al-Cu-Fe Observed by Moessbauer Effect”, Phys. Rev. B, 46(1),
491-495 (1992) (Experimental, Moessbauer, Review, 27)
[1991Fau] Faudot, F., Quivy, A., Calvayrac, Y., Gratias, D., Harmelin, M., “About the Al-Cu-Fe
Icosahedral Phase Formation”, Mater. Sci. Eng. A, 133, 383-387 (1991) (Equi. Diagram,
Experimental, 14)
[1991Jan] Janot, C., Audier, M., de Boissieu, M., Dubois, J.M., “Al-Cu-Fe Quasi-Crystals:
Low-Temperature Unstability via a Modulation Mechanism”, Europhys. Lett., 14(4),
355-360 (1991) (Equi. Diagram, Experimental, 27)
[1991Leg] Legendre, B., Harmelin, M., “Aluminium – Copper – Iron”, MSIT Ternary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 10.14601.1.20, (1991) (Crys. Structure, Equi.
Diagram, Assessment, 71)
[1991Lei] Lei, T., Henley, Ch.L., “Equilibrium Faceting Shape of Quasicrystals at Low Temperatures:
Cluster Model”, Philos. Mag. B, 63(3), 677-685 (1991) (Calculation, Crys. Structure, 33)
[1991Liu1] Liu, W., Köster, U., “Decomposition of Icosahedral Quasicrystals in Al-Cu-Fe Alloys” (in
German), Z. Metallkd., 82(10), 790-798 (1991) (Crys. Structure, Equi. Diagram,
Experimental, 29)
[1991Liu2] Liu, W., Köster, U., Müller, F., Rosenberg, M., “Quasicrystalline and Crystalline Phases in
Aluminum-Copper-Iron-Chromium (Al65Cu20(Fe,Cr)15) Alloys”, Phys. Status Solidi A,
132(1), 17-34 (1992) (Crys. Structure, Experimental, 29)
[1991Men] Menguy, N., Audier, M., “Stability and Instability of the Different Phases in the
Rhombohedral-Icosahedral Transition of an Al-Fe-Cu Alloy”, Int. Workshop Methods
Struct. Anal. of Modulated Struct. and Quasicrystals Lekeitio-Bilbao, 572-586 (1991)
(Crys. Structure, Experimental, 16)
[1991Qui] Quilichini, M., Hennion, B., Heger, G., Lefebvre, S., Quivy, A., “Inelastic Neutron
Scattering by Quasicrystals”, Int. Workshop Methods Struct. Anal. of Modulated Struct. and
Quasicrystals, Lekeitio-Bilbao, Spain, 600-606 (1991) (Experimental, Thermodyn., 9)
[1991Wu] Wu, L., Xiao, J., Chen, Z., “A TEM Study of Crystalline Phases in the Rapidly Solidified
Al65Cu20Fe15 Alloys”, J. Cent.-South Inst. Min. Metall. (China), 22(1), 60-64 (1991) (Crys.
Structure, Experimental, 5)
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Al–Cu–Fe
[1991Zha] Zhang, Z., Li, N.C., Urban, K., “A Quasicrystalline Transition State in an Annealed
Al65Cu20Fe15 Alloy”, J. Mater. Res., 6(2), 366-370 (1991) (Crys. Structure, Experimental,
17)
[1992Che1] Cheng, Y.F., Li, F.H., “An Attempt to Describe One-Dimensional Incommensurate
Composite Structure as Phason-Defected One-Dimensional Quasiperiodic Structure”, Acta
Crystallogr., Sect. A: Found. Crystallogr., 48, 796-804 (1992) (Calculation, Crys.
Structure, Theory, 17)
[1992Che2] Chen, Z., Jiang, X., Wang, Y., Zhou, D., “The Constitution of Multicomponent
Quasicrystalline Alloys”, J. Mater. Sci. Lett., 11(22), 1493-1495 (1992) (Crys. Structure,
Experimental, 5)
[1992Chi] Chien, C.L., Lu, M., “Three States of Al65Cu20Fe15: Amorphous, Crystalline, and
Quasicrystalline”, Phys. Rev. B, 45(22), 12793-12796 (1992) (Crys. Structure,
Experimental, 22)
[1992Eib] Eibschutz, M., Lines, M.E., Chen, H.S., Thiel, F.A., “Structure Difference Between i and T
Phases of Al-Cu-Co and Al-Cu-Fe Observed by Moessbauer Effect”, Phys. Rev. B, 46(1),
491-495 (1992) (Experimental, Moessbauer, Review, 27)
[1992Gay1] Gayle, F.W., Sharpiro, A.J., Biancaniello, F.S., Boettinger, W.J., “The Al-Cu-Fe Phase
Diagram: 0-25 at.% Iron and 50-75 at.% Aluminum - Equilibria Involving the Icosahedral
Phase”, Metall. Trans. A, 23A(9), 2409-2417 (1992) (Abstract, Equi. Diagram,
Experimental, 21)
[1992Gay2] Gayle, F.W., “Phase Equilibria at 550°C in the Al-Cu-Fe System: 50 to 70 at.% Al, 0 to 9
at.% Fe”, J. Phase Equilib., 13(6), 619-622 (1992) (Crys. Structure, Experimental, 12)
[1992Hay] Hayzelden, C., Spaepen, F., “Kinetics of the Icosahedral-to-Approximant Transformation
in Aluminum-Copper-Iron”, Mater. Res. Soc. Symp. Proc., 205, 183-188 (1992) (Crys.
Structure, Kinetics, Experimental)
[1992Lin] Lin, S.T., Jiang, I. M., Cheng, H.Y., Chen, Y.C., Chou, L.S., “Electric and Magnetic
Properties of Al65Cu20(Fe(1-x)Mnx)15 Quasicrystals with x = 0.0, 0.2, 0.4, and 0.6”, J. Phys.:
Condens. Matter, 4(3), 735-746 (1992) (Crys. Structure, Electr. Prop., Equi. Diagram,
Experimental, Magn. Prop., 31)
[1992Lu] Lu, M., Chien, C.L., “Aluminum-Copper-Iron (Al65Cu20Fe15) in Amorphous, Crystalline
and Quasicrystalline States”, Hyperfine Interact., 71(1-4), 1525-15299 (1992) (Crys.
Structure, Experimental)
[1992Mat] Matsubara, E., Waseda, Y., “Structural Study of Icosahedral Al65Cu20Tm15 Alloys
(Tm=Fe, Ru and Os) by Anomalous X-ray Scattering Method”, Met. Abstr. Light Metals
and Alloys, 25, 174 (1992) (Crys. Structure, Experimental, 0)
[1992Nas] Nasu, S., Miglierini, M., Ishihara, K.N., Shingu, P.H., “Transformation from Icosahedral
Quasicrystalline to Amorphous Structure in Al65Cu20Fe15”, J. Phys. Soc. Jpn., 61(10),
3766-3772 (1992) (Crys. Structure, Experimental, 20)
[1992Poo] Poon, S.J., “Electronic Properties of Quasicrystals an Experimental Review”, Adv. Phys.,
41(4), 303-363 (1992) (Crys. Structure, Experimental, Phys. Prop., Review, 223)
[1992Wan] Wang, K. Scheidt, C., Garoche, P., Calvayrac, Y., “Specific-Heat Measurements of
Phason-Strained Quasicrystalline Aluminum-Iron-Copper (AlFeCu)”, J. Phys. I, 2(8),
1553-1557 (1992) (Crys. Structure, Experimental)
[1992Zak] Zakharov, A.M., Guldin, I.T., Arnold, A.A., Matsenko, Yu.A., “Phase Equilibria in
Multicomponent Aluminum Systems with Copper, Iron, Silicon, Manganese and
Titanium”, Metalloved. Obrab. Tsvetn. Splavov: To 90 Anniversary of Academician A.A.
Bochvar Birthday. RAN. Inst. Metall. M, 6-17 (1992) (Equi. Diagram, Experimental, 14)
[1993Ban] Bancel, P.A., “Phason-Induced Transformations of Icosahedral Al-Cu-Fe”, Philos. Mag.
Lett., 67(1), 43-49 (1993) (Crys. Structure, Equi. Diagram, Experimental, 10)
[1993Bes] Bessiere, M., Lefebvre, S., Lee, H., Colella, R., Motsch, T., Denoyer, F., “Feasibility of
Phase Determination in Quasicrystals and Microcrystals by Means of Multiple Bragg
Scattering”, Z. Kristallogr., 209, 390-394 (1994) (Crys. Structure, Experimental, 14)
11
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[1993Dre] Drews, A.R., Rubinstein, M.,Stauss, G.H., Bennett, L.H., Swartzendruber, L.J., “NMR,
Magnetism and Mossbauer Effect in Icosahedral Al63Cu24.5Fe12.5 - a Thermodynamically
Stable Quasi-Periodic Alloy”, J. Alloys Compd., 190, 189-195 (1993) (Experimental,
Moessbauer, Thermodyn., Magn. Prop., 15)
[1993Fau1] Faudot, F., Harmelin, M., “The Al-Cu-Fe Phase Diagram: Liquidus Surface and Equilibria
Involving the Quasicrystalline Icosahedral Phase and its Approximants”, Calorim. Therm.
Anal., 24, 121-124 (1993) (Crys. Structure, Experimental , Equi. Diagram)
[1993Fau2] Faudot F., “Phase Diagram Al-Cu-Fe. Al-Rich Region and Region of Icosahedral Phases”,
Annal. Chim. Sci. Mat.(France), 18(7), 445-456 (1993) (Equi. Diagram, Experimental, 31)
[1993Gra] Gratias, D., Calvayrac, Y., Devaud-Rzepski, J., Faudot, F., Harmelin, M., Quivy, A.,
Bancel, P.A., “The Phase Diagram and Structures Of the Ternary Al-Cu-Fe System in the
Vicinity of the Icosahedral Region”, J. Non-Cryst. Solids, 153-154, 482-488 (1993) (Crys.
Structure, Equi. Diagram, Review, 18)
[1993Kat] Kattner, U.R., Burton, B.P., “Aluminum-Iron”, in “Phase Diagrams of Binary Iron Alloys”,
ASM, Metals Park, OH, 12-28 (1993) (Crys. Structure, Equi. Diagram, Review, Magn.
Prop., Thermodyn., 99)
[1993Lee] Lee, B.H., Colella, R., “Phase Determination of X-Ray Reflection in a Quasicrystal” , Acta
Crystallogr., A49, 600-605 (1993) (Crys. Structure, Experimental, 15)
[1993Men] Menguy, N., de Boissieu, M., Guyot, P., Audier, M., Elkaim, E., Lauriat, J.P., “Single
Crystal X-Ray Study of a Modulated Icosahedral AlCuFe Phase”, J. Phys. I, 3, 1953-1968
(1993) (Calculation, Crys. Structure, Experimental, 33)
[1993Nas] Nasu, S., Miglierini, M., Ishihara, K.N., Shingu, P.H., “Transformation from Icosahedral
Quasicrystalline to Amorphous Structure in Al65Cu20Fe15”, Met. Abstr. Light Metals and
Alloys, 26, 155 (1993) (Crys. Structure, Experimental, 0)
[1993Saa1] Saadi, N., Harmelin, M., Faudot, F., Legendre, B., “Enthalpy of Formation of the
Al0.63Co0.25Fe0.12 Icosahedral Phase”, J. Non-Cryst. Solids, 153-154, 500-503 (1993)
(Equi. Diagram, Experimental, Thermodyn., 14)
[1993Saa2] Saadi, N., Harmelin, M., Legendre, B., “Determination of the Formation Enthalpy of
Crystalline and Quasicrystalline Phases of the Al-Cu-Fe System by Solution Calorimetry”,
J. Chim. Phys., 90(2), 355-366 (1993) (Crys. Structure, Experimental, Thermodyn., 21)
[1993Was] Waseda, A., Araki, K., Kimura, K., Ino, H., “Quasicrystals and Approximants in the
Al-Co-(Fe, Ru) and Al-Pd-Mn Systems”, J. Non-Cryst. Solids, 153-154, 635-639 (1993)
(Crys. Structure, Equi. Diagram, Experimental, 19)
[1994Bes] Bessiere, M., Lefebvre, S., Lee, H., Colella, R., Motsch, T., Denoyer, F., “Feasibility of
Phase Determination in Quasicrystals and Microcrystals by Means of Multiple Bragg
Scattering”, Z. Kristallogr., 209, 390-394 (1994) (Crys. Structure, Experimental, 14)
[1994Fre1] Freiburg, C., Grushko, B., Melchers, M., Reichert, W., “Structure of (Al,Cu)13Fe4 with
Cu-Contents of 0, 2 and 4 at. percent”, Mater. Sci. Forum, 166-169, 455-460 (1994)
(Experimental, Crys. Structure, 7)
[1994Fre2] Freiburg C., Grushko B., “An Al13Fe4 Phase in the Al-Cu-Fe Alloy System.”, J. Alloys
Compd., 210, 149-152 (1994) (Crys. Structure, Experimental, 18)
[1994Hol] Holland-Moritz, D., Herlach, D.M., Grushko, B., Urban, K., “Phase Selection in
Undercooled Melts of Al-Cu-Co And Al-Cu-Fe Quasi-Crystal-Forming Alloys”, Mater.
Sci. Eng. A, 181(1-2), 766-770 (1994) (Equi. Diagram, Experimental, Kinetics, Mechan.
Prop., 19)
[1994Law] Lawther, D.W., Dunlap, R.A., “Positron-Annihilation Study of Equilibrium Defects in
Al-Cu-Fe Face-Centered-Icosahedral Quasicrystals”, Phys. Rev. B, 49(5), 3183-3189
(1994) (Crys. Structure, Experimental, Phys. Prop., Thermal Conduct., 65)
[1994Lef] Lefebvre, S., Bessiere, M., Calvayrac, Y., Itie, J.P., Polian, J.P., Sadoc, A., “Icosahedral and
Approximant Structures of AlCuFe Phases: A Study by Diffraction at High Pressure”,
Mater. Sci. Forum, 166-169, 449-454 (1994) (Crys. Structure, Experimental, 11)
12
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)”, in “Phase Diagrams of Binary Copper
Alloys”, Subramanian, P.R., Chakrabati, D.J., Laughlin D.E., (Eds.), ASM International,
Materials Park, OH, 18-42 (1994) (Equi. Diagram, Crys. Structure, Thermodyn., Review,
226)
[1994Tra] Trambly de Laissardiere, G.; Fujiwara, T., “Electronic Structure and Conductivity in a
Model Approximant of the Icosahedral Quasicrystal Al-Cu-Fe”, Phys. Rev. B, 50(9),
5999-6005 (1994) (Calculation, Crys. Structure, Phys. Prop., 34)
[1994Was] Waseda, A., Kimura, K., Ino, H., “Free Energy Analysis for the Phase Transition Of
Quasicrystals and Phase Diagram Of The Al-Cu-Fe System”, Mater. Sci. Eng. A, 181/
182(1-2), 762-765 (1994) (Calculation, Equi. Diagram, Experimental, Thermodyn., 11)
[1995Che] Chen, Q., Jin, Z., “The Fe-Cu System: A Thermodynamic Evaluation”, Metall. Mater.
Trans. A, 26A, 417-426 (1995) (Calculation, Thermodyn., Assessment, Equi. Diagram, 55)
[1995Div] Divinski, S.V., Larikov, L.N., “Modulated Quasicrystal Structure”, Philos. Mag. Lett.,
72(5), 345-351 (1995) (Calculation, Theory, 27)
[1995Tra] Trambly de Laissardiere, G., Nguyen Manh, D., Magaud, L., Julien, J.P., Cyrot-Lackmann,
F., Mayou, D., “Electronic Structure and Hybridization Effects in Hume-Rothery Alloys
Containing Transition Elements”, Phys. Rev. B, 52(11), 7920-7933 (1995) (Calculation,
Crys. Structure, Electr. Prop., 64)
[1996Gru] Grushko, B., Wittenberg, R., Holland-Moritz, D., “Solidification of Al-Cu-Fe Alloys
Forming Icosahedral Phase”, J. Mater. Res., 11(9), 2177-2185 (1996) (Experimental, 31)
[1996Log] Lograsso, T.A., Delaney, D.W., “Preparation of Large Single Grains of the Quasicrystalline
Icosahedral Al-Cu-Fe Phase”, J. Mater. Res., 11(9), 2125-2127 (1996) (Crys. Structure,
Experimental, 12)
[1996Qui] Quiquandon, M., Quivi, A., Devaud, J., Faudot, F., Lefebvre, S., Bessiere, M., Calvayrac,
Y., “Quasicrystal and Approximat Structures in the Al-Cu-Fe System”, J. Phys.: Condensed
Matter, 8(15), 2487-2512 (1996) (Crys. Structure, Equi. Diagram, Experimental, 29)
[1996Zha] Zhang F.X., Wang W.K., “Phase Formation Behavior in Undercooled
Quasicrystal-Forming Al-Cu-Fe Alloy Melts”, Mater. Sci. Eng. A, 205, 214-220 (1996)
(Crys. Structure, Experimental, 27)
[1997And] Anderson, I.M., “Alchemi Study of Site Distributins of 3d-Transition Metals in B2-Ordered
Iron Aluminides”, Acta Mater., 45(9), 3897-3909 (1997) (Calculation, Crys. Structure,
Experimental, Theory, 26)
[1997Div] Divakar, R., Sundararaman, D., Raghunathan, V.S., “Al-Cu-Fe Quasicrystals: Stability and
Microstructure”, Prog. Cryst. Growth Charact., 34, 263-269 (1997) (Crys. Structure,
Experimental, 18)
[1997Ham] Hamada, E., Oshima, N., Suzuki, T., Sato, K., Kanazawa, I., Nakata, M., Takeuchi, S.,
“Positron Annihilation Studies of Icosahedral AlCuRu and AlCuFe Alloys”, Mater. Sci.
Forum, 255-257, 451-453 (1997) (Experimental, Crys. Structure, 16)
[1997Las] Lasjaunias, J.C., Calvayrac, Y., Yang, H., “Investigation of Elementary Excitation in
AlCuFe Quasicrystals by Means of Low-Temperature Specific Heat”, J. Phys. I, 7, 959-976
(1997) (Electr. Prop., Equi. Diagram, Experimental, Thermodyn., 48)
[1997Oht] Ohtani, H., Suda, H., Ishida, K., “Solid/Liquid Equilibria in Fe-Cu Based Ternary Systems”,
ISIJ Int., 37(3), 207-216 (1997) (Calculation, Equi. Diagram, Experimental, Review,
Thermodyn., 47)
[1997Pop] Popescu, R., Macovei, D., Manciu, M., Zavaliche, F., Fratiloiu, D., Jianu, A., Devenyi, A.,
Manaila, R., Xie, R., Hu, T., Orton, B.R., Cernik, R.J., Tang, C.C., “The Au-Substituted
Al-Cu-Fe Icosahedral Phase: Evidence for Bond Hybridization”, J. Phys.: Condens. Matter,
9, 7523-7540 (1997) (Crys. Structure, Experimental, 28)
[1997Ros] Rosas, G., Perez, R., “Crystalline and Quasicrystalline Phases in AlCuFe and AlCuFeCr
Alloys”, J. Mater. Sci., 32, 2403-2409 (1997) (Equi. Diagram, Experimental, 12)
13
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[1997She] Shen, Z., Pinhero, P.J., Lograsso, T.A., Delaney, D.W., Jenks, C.J., Thiel, P.A., “The
Five-Fold Surface of Quasicrystalline AlCuFe: Preparation and Characterization with
LEED and AES”, Surf. Sci., 385, L923-L929 (1997) (Crys. Structure, Experimental, 39)
[1998Akd] Akdeniz, M.V., Mekhrabon, A.O., “The Effect of Substitutional Impurities on the Evolution
of Fe-Al Diffusion Layer”, Acta Mater., 46(4), 1185-1192 (1998) (Calculation,
Thermodyn., 55)
[1998Dun] Duneau, M., Audier, M., “Structural Characteristics of Pentagonal Al-Fe-Cu Phases”,
Philos. Mag. A, 77(3), 675-688 (1998) (Crys. Structure, Experimental, 9)
[1998Hol] Holland-Moritz, D., Schroers, J., Herlach, D.M., Grushko, B., Urban, K., “Undercooling
and Solidification Behaviour of Melts of the Quasicrystal-Forming Alloys Al-Cu-Fe and
Al-Cu-Co”, Acta Mater., 46, 1601-1615 (1998) (Equi. Diagram, Experimental, 44)
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-Rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264, 201-208 (1998) (Equil. Diagram,
Experimental, 25)
[1998Ma] Ma, X.L., Rüdiger, A., Liebertz, H.; Köster, U.; Liu, W., “A New Structural Variant of
-Al3O4 and its Orientation Relationship with the Cubic -Al4Cu9”, Scr. Mater., 39(6),
707-714 (1998) (Crys. Structure, Experimental, 16)
[1998Ohn] Ohnuma, I., Ikeda, O., Kainuma, K., Sundman, B., Ishida, K., ”Phase Separation Induced
by Interaction between Chemical and Magnetic Ordering in BCC Phase in Fe-Al Binary
System”, CALPHAD XXVII, Beijing, P.R.China, 17-22 May, 1998, 4, (1998) (Thermodyn.,
Calculation, Assessment)
[1998Vol] Voltz, C., Bletry, J., Audier, M., “Drop Tube Solidification of Al-Cu-Fe Quasicrystalline
Phase”, Philos. Mag. A, 77(6), 1351-1366 (1998) (Crys. Structure, Equi. Diagram,
Experimental, 28)
[1998Wan] Wang, C.P., Liu, X.J., Ohnuma, I., Kainuma, R., Hao, S.M., Ishida, K., “Ordering and Phase
Separation of the BCC Phase in the Fe-Cu-Al System”, Z. Metallkd., 89(12), 828-835
(1998) (Crys. Structure, Equi. Diagram, Experimental, Thermodyn., #, *, 18)
[1999Bra] Brand, R.A., Pelloth, J., Hippert, F., Calvayrac, Y., “Correlations in the Electronic
Properties of AlCuFe Quasicrystals and High-Order Approximants: Fe’(57) Moessbauer,
and Al’(27) and Cu’(65) Nuclear Magnetic Resonance Studies”, J. Phys.: Condens. Matter,
11, 7523-7543 (1999) (Crys. Structure, Experimental, Moessbauer, Review, 51)
[1999Hol] Hollamd-Moritz, D., Lu, I.-R., Wilde, G., Schroers, J., Grushko, B., “Melting Entropy of
Al-Based Quasicrystals”, J. Non-Cryst. Solids, 250-252, 829-832 (1999) (Experimental,
Thermodyn., 17)
[1999Pon] Ponkratz, U., Nicula, R., Jianu, A., Burkel, E., “Quasicrystals Under Pressure: a
Comparison Between Ti-Zr-Ni and Al-Cu-Fe Icosahedral Phases”, J. Non-Cryst. Solids,
250-252, 844-848 (1999) (Crys. Structure, Experimental, 20)
[1999Rot] Roth, C., Schwabe, G., Knöfler, R., Zavaliche, F., Madel, O., Haberkern, R., Häussler, P.,
“A Detailed Comparison Between the Amorphous and the Quasicrystalline State of
Al-Cu-Fe”, J. Non-Cryst. Solids, 250-252, 869-873 (1999) (Equi. Diagram, Experimental,
12)
[1999Tor] Toro, J.A., Torre, L.M.A., Riveiro, J.M., “Spin-Glass-Like Behavior in Mechanically
Alloyed Nanocrystalline Fe-Al-Cu”, Phys. Rev. B, 60(18), 12918-12923 (1999) (Crys.
Structure, Experimental, Magn. Prop., 27)
[1999Wan] Wang, L., Tan, Z.C., Zhang, J.B., Meng, S.H., Zhang, L.M., Zhou, Q.G., Dong, C., “Heat
Capacities of Al62.5Cu25Fe12.5 Quasicrystals and B2 Related Crystals”, Thermochim. Acta,
331, 21-25 (1999) (Crys. Structure, Experimental, Thermodyn., 9)
[2000Bel1] Belin-Ferre, E., Dubois, J-M., Fournee, V., Brunet, P., Sordelet, D.J., Zhang, L.M., “About
the Al 3p Density of States in Al-Cu-Fe Compounds and its Relation to the Compound
Stability and Apparent Surface Energy of Quasicrystals”, Mater. Sci. Eng. A, 294-296,
818-821 (2000) (Crys. Structure, Experimental, 20)
14
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[2000Bel2] Belin-Ferre, E., Fournee, V., Dubois, J.M., “Al 3p Occupied States in Al-Cu-Fe
Intermetallics and Enhanced Stability of the Icosahedral Quasicrystal”, J. Phys.: Condens.
Matter, 12, 8159-8177 (2000) (Crys. Structure, Equi. Diagram, Experimental, 32)
[2000Bil] Bilusic, A., Smontara, A., Lasjaunias, J.C., Ivkov, J., Calvauras, Y., “Thermal and
Thermoelectric Properties of Icosahedral Al62Cu25.5Fe12.5 Quasicrystal”, Mater. Sci. Eng.
A, 294-296, 711-714 (2000) (Crys. Structure, Experimental, Phys. Prop., 21)
[2000Blo] Bloom, P.D., Baikerikar, K.G., Otaigbe, J.U., Sheares, V.V., “Development of Novel
Polymer/Quasicrystal Composite Materials”, Mater. Sci. Eng. A, 294-296, 156-159 (2000)
(Crys. Structure, Experimental, Mechan. Prop., Phys. Prop., 10)
[2000Bou] Boudard, M., Letoublon, A., Boissieu, M., Ishimasa, T., Mori, M., Elkaim, E., Lauriat, J.P.,
“Phase Transition and Diffuse Scattering Studies in the Al-Cu-Fe Ternary System”, Mater.
Sci. Eng. A, 294-296, 217-220 (2000) (Crys. Structure, Experimental, 19)
[2000Bra1] Brand, R.A., Voss, J., Calvayrac, Y., “Phason-Dynamics Studied by Quasielastic
Moessbauer Scattering in i-Al-Cu-Fe Quasicrystals”, Mater. Sci. Eng. A, 294-296, 666-669
(2000) (Calculation, Crys. Structure, Experimental, Moessbauer, 27)
[2000Bra2] Brand, R.A., Coddens, G., Chumakov, A.I., Dianoux, A.J., Calvayrac, Y., “The Phonon
Density of States in the Archetypical Icosahedral Quasicrystal Al62Cu25.5Fe12.5”, Mater.
Sci. Eng. A, 294-296, 662-665 (2000) (Calculation, Crys. Structure, Experimental, 17)
[2000Bru] Brunet, P., Zhang, L.M., Sordelet, D.J., Besser, M.; Dubois, J-M., “Comparative Study of
Microstructural and Tribological Properties of Sintered, Bulk Icosahedral Samples”, Mater.
Sci. Eng. A, 294-296, 74-78 (2000) (Crys. Structure, Experimental, Phys. Prop., 6)
[2000Bu] Bu, J., Rhee, H.-K., Shen, Y.Z., Shin, K.S., “Decomposition of NO on the Surface of
Al-Cu-Fe Quasicrystal at High Temperature”, J. Mater. Sci. Lett., 20, 1165-1167 (2000)
(Crys. Structure, Experimental, 16)
[2000Dub] Dubois, J-M., “New Prospects from Potential Applications of Quasicrystalline Materials”,
Mater. Sci. Eng. A, 294-296, 4-9 (2000) (Crys. Structure, Experimental, Phys. Prop.,
Review, 38)
[2000Dun] Duneau, M., “Covering Clusters in the Katz-Gratias Model of Icosahedral Quasicrystals”,
Mater. Sci. Eng. A, 294-296, 192-198 (2000) (Calculation, Crys. Structure, Experimental,
34)
[2000Fle] Fleury, E., Lee, S.M., Kim, W.T., Kim, D.H., “Effect of Air Plasma Spraying Parameters
on the Al-Cu-Fe Quasicrystalline Coating Layer”, J. Non-Cryst. Solids, 278, 194-204
(2000) (Crys. Structure, Experimental, Phys. Prop., 28)
[2000Gia] Giacometti, E.; Baluc, N.; Bonneville, J., “Creep Behavior of Icosahedral Al-Cu-Fe”,
Mater. Sci. Eng. A, 294-296, 777-780 (2000) (Crys. Structure, Experimental, 18)
[2000Gre1] Grenet, T., Giroud, F., Loubet, C., Joulaud, J.L., Capitan, M., “Real Time Study of the
Quasicrystal Formation in Annealed Al-Cu-Fe Metallic Multilayers”, Mater. Sci. Eng. A,
294-296, 838-841 (2000) (Crys. Structure, Experimental, 12)
[2000Gre2] Grenet, T., Giroud, F., “Observation of 2D Quantum Interference Effect in Quasicrystalline
i-Al-Cu-Fe Thin Films”, Mater. Sci. Eng. A, 294-296, 576-579 (2000) (Crys. Structure,
Electr. Prop., Experimental, 10)
[2000Hab] Haberkern, R., Khedhri, K., Madel, C., Haussler, P., “Electronic Transport Properties of
Quasicrystalline Thin Films”, Mater. Sci. Eng. A, 294-296, 475-480 (2000) (Crys. Structure,
Experimental, Phys. Prop., 18)
[2000Jon] Jono, M., Matsuo, Y., Ishii, Y., “A Phason Strain in an Al-Cu-Fe Icosahedral Quasicrystal”,
Mater. Sci. Eng. A, 294-296, 680-684 (2000) (Crys. Structure, Experimental, 8)
[2000Lan1] Landauro, C.V., Solbrig, H., “Temperature Dependence of the Electronic Transport in
Al-Cu-Fe Phases”, Mater. Sci. Eng. A, 294-296, 600-603 (2000) (Calculation, Crys.
Structure, 20)
[2000Lan2] Lang, C.I., Sordelet, D.J., Besser, M.F., Shechtman, D., Biancaniello, F.S., Gonzales, E.J.,
“Quasicrystalline Coatings: Thermal Evolution of Structure and Properties”, J. Mater. Res.,
15(9), 1894-1904 (2000) (Equi. Diagram, Experimental, Mechan. Prop., Phys. Prop., 41)
15
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[2000Lee1] Lee, S.M., Jung, J.H., Fleury, E., Kim, W.T., Kim, D.H., “Metal Matrix Composites
Reinforced by Gas-Atomised Al-Cu-Fe Powders”, Mater. Sci. Eng. A, 294-296, 99-103
(2000) (Calculation, Crys. Structure, Experimental, Mechan. Prop., 9)
[2000Lee2] Lee, S.M., Kim, B.H., Kim, S.H., Fleury, E., Kim, W.T., Kim, D.H., “Effect of Si Addition
on the Formability of the Icosahedral Quasicrystalline Phase in an Al65Cu20Fe15 Alloy”,
Mater. Sci. Eng. A, 294-296, 93-98 (2000) (Crys. Structure, Experimental, Mechan. Prop.,
11)
[2000Mad] Madel, C., Schwalbe, G., Haberkern, R., Haussler, P., “Hume-Rothery Effect in Amorphous
and Quasicrystalline Al-Cu-Fe”, Mater. Sci. Eng. A, 294-296, 535-538 (2000) (Crys.
Structure, Experimental, Phys. Prop., 11)
[2000Miz] Mizutani, U., “Electron Transport Mechanism in the Pseudogar System: Quasicrystals,
Approximants and Amorphous Alloys”, Mater. Sci. Eng. A, 294-296, 464-469 (2000) (Crys.
Structure, Experimental, 23)
[2000Nak] Nakano, H., Sato, Y., Matsuo, S., Ishimasa, T., “Development of 3D Visualization System
for the Study of Physical Properties of Quasicrystals”, Mater. Sci. Eng. A, 294-296, 542-547
(2000) (Crys. Structure, Experimental, Phys. Prop., 29)
[2000Nic] Nicula, R., Jianu, A., Grigoriu, C., Barfels, T., Burkel, E., “Laser Ablation Synthesis of
Al-Based Icosahedral Powders”, Mater. Sci. Eng. A, 294-296, 86-89 (2000) (Crys.
Structure, Experimental, Mechan. Prop., 12)
[2000Pre] Prekul, A.F., Kuzmin, N.Yu., Shchegolikhina, N.J., “Thermal Activation of Carriers and
Characteristic Features of the Electronic Structure of Quasicrystalline Systems”, Mater. Sci.
Eng. A, 294-296, 527-530 (2000) (Crys. Structure, Experimental, Phys. Prop., 7)
[2000Rap] Rapp, O., “Electronic Transport Properties of Quasicrystals: the Unique Case of the
Magnetoresistance”, Mater. Sci. Eng. A, 294-296, 458-463 (2000) (Crys. Structure,
Experimental, Magn. Prop., Phys. Prop., 24)
[2000Rue] Rüdiger, A., Köster, U., “Corrosion Behavior of Al-Cu-Fe Quasicrystals”, Mater. Sci. Eng.
A, 294-296, 890-893 (2000) (Crys. Structure, Experimental, 5)
[2000Sin] Singh, A., Tsai, A.P., “The Nature of Lead-Quasicrystal Interfaces and its Effect on the
Melting Behavior of Lead Nanoparticles Embedded in Quasicrystalline Matrices”, Mater.
Sci. Eng. A, 294-296, 160-163 (2000) (Crys. Structure, Experimental, 12)
[2000Sha] Shalaeva, E.V., Prekul, A.F., “Structural State of -Solid Solution in Quenched
Quasicrystal-Forming Alloys of Al61Cu26Fe13”, Phys. Status Solidi A, 180, 411-425 (2000)
(Crys. Structure, Equi. Diagram, Experimental, 32)
[2000Smo] Smontara, A., Lasjaunias, J.C., Paulsen, C., Bilusic, A., Calvayras, Y., “Low-Temperature
Thermal Conductivity of Icosahedral Al63Cu25Fe12 and Al62Cu25.5Fe12.5 Quasicrystals”,
Mater. Sci. Eng. A, 294-296, 706-710 (2000) (Crys. Structure, Experimental, Phys. Prop.,
Thermal Conduct., 14)
[2000Sri] Srinivas, V., Barua, P., Murty, B.S., “On Icosahedral Phase Formation in Mechanically
Alloyed Al70Cu20Fe10”, Mater. Sci. Eng. A, 294-296, 65-67 (2000) (Crys. Structure,
Experimental, 11)
[2000Ste] Steurer, W., “The Quasicrystal-to-Crystal Transformation. I. Geometrical Principles”,
Z. Kristallogr., 215, 323-334 (2000) (Calculation, Crys. Structure, 44)
[2000Tre] Trefilov, V.I., Mil’man, Yu.V., Lotsko, D.V., Belous, A.N., Cgugunova, S.I., Timofeeva,
I.I., Bykov, A.I., “Studies of Mechanical Properties of Quasicrystalline Al-Cu-Fe Phase by
the Indentation Technique”, Dokl. Phys., 45(8), 363-366 (2000) (Experimental, Mechan.
Prop., 15)
[2000Uch] Uchiyama, H., Takahashi, Y., Sato, K., Kanazawa, I., Kimura, K., Komori, F., Suzuki, R.,
Ohdaira, T., Tamura, R., Takeuchi, S., “Stable Quasicrystals Studied by Means of the Slow
Positron Beam”, Nucl. Instrum. Methods Phys. Res. / B, B171, 245-250 (2000) (Crys.
Structure, Equi. Diagram, Experimental, 21)
16
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[2000Wan] Wang, R., Yang, W., Gui, J., Urban, K., “Dislocation Mechanism of High-Temperature
Plastic Deformation of Al-Cu-Fe and Al-Pd-Mn Icosahedral Quasicrystals”, Mater. Sci.
Eng. A, 294-296, 742-747 (2000) (Crys. Structure, Experimental, 18)
[2000Weh] Wehner, B.I., Köster, U., Rudiger, A., Pieper, A., Sordelet, D.J., “Oxidation of Al-Cu-Fe
and Al-Pd-Mn Quasicrystals”, Mater. Sci. Eng. A, 294-296, 830-833 (2000) (Crys.
Structure, Experimental, 16)
[2000Wu1] Wu, J.S., Brien, V., Brunet, P., Dong, C., Dubois, J.M., “Scratch-Induced Surface
Microstructures on the Deformed Surface of Al-Cu-Fe Icosahedral Quasicrystals”, Mater.
Sci. Eng. A, 294-296, 846-849 (2000) (Crys. Structure, Experimental, 8)
[2000Wu2] Wu, J.S., Brien, V., Brunet, P., Dong, C., Dubois, J.M., “Electron Microscopy Study of
Scatch-Induced Surface Microstructures in an Al-Cu-Fe Icosahedral Quasicrystal”, Philos.
Mag. A, 80(7), 1645-1655 (2000) (Crys. Structure, Experimental, 51)
[2000Yok1] Yokoyama, Y., Note, R., Fukaura, K., Sunada, H., Hiraga, K., Inoue, A., “Growth of a
Single Al64Cu23Fe13 Icosahedral Quasicrystal Using the Czochralski Method and
Annealing Removal of Strains”, Mater. Trans. , JIM, 41(11), 1583-1588 (2000) (Equi.
Diagram, Experimental, 14)
[2000Yok2] Yokoyama, Y., Fukaura, K., Sunada, H., “Preparation of Large Grained Al64Cu23Fe13
Icosahedral Quasicrystal Directly From the Melt”, Mater. Trans., JIM, 41(1), 668-674
(2000) (Equi. Diagram, Experimental, 15)
[2000Yok3] Yokoyama, Y., Fukaura, K., Sunada, H., Note, R., Hiraga, K., Inoue, A., “Production of
Single Al64Cu23Fe13 Icosahedral Quasicrystal with the Czochralski Method”, Mater. Sci.
Eng. A, 294-296, 68-73 (2000) (Equi. Diagram, Experimental, 11)
[2000Zha] Zhang, L.M., Brunet, P., Zhang, H.C., Dong, C., Dubois, J.M., “Influence of Valence
Electron Concentration over the Friction Behaviors of Quasicrystal and B2-Type
Approximants in Al-Cu-Fe Ternary System”, Tribol. Lett., 8, 233-236 (2000) (Equi.
Diagram, Experimental, Mechan. Prop., 11)
[2001Bar] Barua, P., Murty, B.S., Srinivas, V., “Mechanical Alloying of Al-Cu-Fe Elemental
Powders”, Mater. Sci. Eng. A, 304-306, 863-866 (2001) (Equi. Diagram, Experimental, 13)
[2001Cai] Cai, T., Shi, F., Shen, Z., Gierer, M., Goldman, A.I., Kramer, M.J., Jenks, C.J., Lograsso,
T.A., Delaney, D.W., Thiel, P.A., van Hove, M.A., “Structural Aspect of the Fivefold
Quasicrystalline Al-Cu-Fe Surface from STM and Dynamical LEED Studies”, Surf. Sci.,
495, 19-34 (2001) (Crys. Structure, Experimental, 44)
[2001Jon] Jono, M., Matsuo, Y., Yamamoto, K., Ishii, Y., “X-Ray Diffraction Study of a Phason Strain
in an Al-Cu-Fe Icosahedral Quasicrystal”, Philos. Mag. A, 8(11), 2577-2590 (2001) (Crys.
Structure, Experimental, 18)
[2001Liu] Liu, X.J., Wang, C.P., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Stability Among the
(A1), (A2), and (D83) Phases in the Cu-Al-X System”, J. Phase Equilib., 22, 431-438
(2001) (Equi. Diagram, Experimental, 14)
[2001Gui] Gui, J., Wang, J., Wang, R., Wang, D., Liu, J., Chen, F., “On Some Discrepancies in the
Literature about the Formation of Icosahedral Quasi-Crystal in Al-Cu-Fe Alloys”, J. Mater.
Res., 16(14), 1037-1046 (2001) (Crys. Structure, Experimental, 24)
[2001Guo] Guo, J.Q., Tsai, A.P., “Single-Crystal Growth of the Al-Cu-Fe Icosahedral Quasicrystal
from the Ternary Melt”, J. Mater. Res., 16(11), 3038-3041 (2001) (Crys. Structure, Equi.
Diagram, Experimental, 18)
[2001Kim] Kim, H-G., Muyng, W-N., Sumiyama, K., Suzuki, K., “Formation of a Nanocrystalline
Phase by Chemical Leaching of Rod-Milled Al0,6(Fe50Cu50) Alloy”, J. Alloys Compd., 322,
214-219 (2001) (Crys. Structure, Experimental, Phys. Prop., 17)
[2001Muk] Mukhopadhyay, N.K., “An Investigation on the Transformation of the Icosahedral Phase in
the Al-Fe-Cu System During Mechanical Milling and Subsequent Annealing”, Philos. Mag.
A, 82(16), 2979-2993 (2002) (Crys. Structure, Experimental, 31)
17
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[2001Ros] Rosas, G., Perez, R., “On the Relationships Between Isothermal Phase Diagrams and
Quasicrystalline Phase Transformations in AlCuFe Alloys”, Mater. Sci. Eng. A, 298, 79-83
(2001) (Equi. Diagram, Experimental, 10)
[2001Qia] Qiang, J.-B., Wang, D.-H., Bao, C.-M., Wang, Y.-M., Xu, W.-P., Song, M.-L., Dong, Ch.,
“Formation Rule for Al-Based Ternary Quasi-Crystals: Example of Al-Ni-Fe Decagonal
Phase”, J. Mater. Res., 16(9), 2653-2660 (2001) (Crys. Structure, Equi. Diagram,
Experimental, 31)
[2001Sin] Singh, A., Tsai, A.P., “Melting Behaviour of Bismuth Nanoparticles Embedded in
Al-Cu-Fe Quasicrystalline Matrix”, Scr. Mater., 44(8-9), 2005-2008 (2001) (Equi.
Diagram, Experimental, Thermodyn., 16)
[2001Sur] Suryanarayana, C., “Mechanical Alloying and Milling”, Prog. Mater. Sci., 46(1-2), 1-184
(2001) (Crys. Structure, Equi. Diagram, Experimental, Kinetics, Review, Thermodyn., 932)
[2001Tur] Turchanin, M.A., Agraval, P.G., “Thermodynamics of Liquid Alloys, and Stable and
Metastable Phase Equilibria in the Copper-Iron System”, Powder Metall. Met. Ceram., 40
(7-8), 337-353 (2001), translated from Poroshk. Metall. (Kiev), (7-8), 34-53 (2001)
(Thermodyn., Experimental, Assessment, Equi. Diagram, 56)
[2002Ban] BanerJee, R., Amancherla, S., Banerjee, S., Fraser, H.L., “Modeling of Site Occupancies in
B2 FeAl And NiAl Alloys with Ternary Additions”, Acta Mater., 50, 633-641 (2002)
(Calculation, Equi. Diagram, Experimental, 21)
[2002Bar] Barua, P., Murty, B.S., Mathur, B.K., Srinivas, V., “Icosahedral Phase Formation Domain
in Al-Cu-Fe System by Mechanical Alloying”, J. Mater. Res., 17(3), 653-659 (2002) (Crys.
Structure, Experimental, 26)
[2002Dub] Dub, S., Novikov, N., Milman, Yu., “The Transition from Elastic to Plastic Behavior in an
Al-Cu-Fe Quasicrystal Studied by Cyclic Nanoindentation”, Philos. Mag. A, 82(10),
2161-2172 (2002) (Crys. Structure, Experimental, 24)
[2002Fik] Fikar, J., Schaller, R., Guilbaud, N., Baluc, N., “Mechanical Spectroscopy of Icosahedral
Al-Cu-Fe Quasicrystals Metal-Based Composites”, Def. Diffus. Forum, 203-205, 289-292
(2002) (Experimental, Phys. Prop., 7)
[2002Gre] Grenet, T., Giroud, F., “Formation of Icosahedral Al-Cu-Fe Quasicrystal in Annealed
Metallic Multilayers”, Philos. Mag. A, 82(16), 2909-2922 (2002) (Crys. Structure,
Experimental, 30)
[2002Gul] Gulay, L.D., Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, in “Crystal Chemistry of Intermetallic Compounds”, Abstr. VIII Int. Conf. Lviv,
P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Hir] Hiraga, K., “The Structure of Quasicrystals Studied by Atomic-Scale Observations of
Transmission Electron Microscopy”, Adv. Imag. Electr. Phys., 122, 1-86 (2002)
(Assessment, Crys. Structure, 99)
[2002Kra] Kraposhin, V.S., Talis, A.L., Dubois, J.M., “Structural Realization of the Polytope
Approach for the Geometrical Description of the Transition of a Quasicrystal into a
Crystalline Phase”, J. Phys.: Condens. Matter, 14, 8987-8996 (2002) (Crys. Structure,
Experimental, 20)
[2002Mel] Mele, A., Liu, H., Russo, R.E., Mao, X., Giardini, A., Satta, M., “Inductively Coupled
Plasma Mass Spectrometric Study of Laser Sputtering from the Surface of an Al-Cu-Fe
Alloy and Quasicrystal”, Appl. Surf. Sci., 186, 322-328 (2002) (Crys. Structure,
Thermodyn., 19)
[2002Sha] Shalaeva, E.V., “On Mutual Transformation of Icosahedral Phase and -Solid Solution with
Participation of Ordered -Like Displasements in Quenched Alloys of Al61Cu26Fe13”, J.
Alloys Compd., 342, 134-138 (2002) (Crys. Structure, Experimental, 9)
[2002Tch] Tcherdyntsev, V.V., Kaloshkin, S.D., Salimon, A.I., Tomilin, I.A., Korsunsky, A.M.,
“Quasicrystalline Phase Formation by Heating a Mechanically Alloyed Al65Cu23Fe12
Powder Mixture”, J. Non-Cryst. Solids, 312-314, 522-526 (2002) (Crys. Structure,
Experimental, 19)
18
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
[2002Yok] Yokoyama, Y., Matsuo, Y., Yamamoto, K., Hiraga, K., “Growth Condition and X-Ray
Analysis of Single Al64Cu23Fe13 Icosahedral Quasicrystal by the Czochralski Method”,
Mater. Trans., JIM, 43(4), 762-765 (2002) (Crys. Structure, Experimental, 13)
[2002Zha] Zhang, L.M., Lück, R, “Phase Equilibria of the Icosahedral Al-Cu-Fe Phase”, J. Alloys
Compd., 342, 53-56 (2002) (Equi. Diagram, Experimental, #, *, 11)
[2003Zha1] Zhang, L.M., Lück, R., “Phase Diagram of the Al-Cu-Fe Quasicrystal-Forming Alloy
System. I. Liquidus Surface and Phase Equilibria with Liquid”, Z. Metallkd., 94(2), 91-97
(2003) (Crys. Structure, Equi. Diagram, Experimental, Magn. Prop., #, *, 25)
[2003Zha2] Zhang, L.M., Lück, R., “Phase Diagram of the Al-Cu-Fe Quasicrystal-Forming Alloy
System. II. Isopleths”, Z. Metallkd., 94(2), 98-107 (2003) (Equi. Diagram, Experimental, #,
*, 11)
[2003Zha3] Zhang, L.M., Lück, R., “Phase Diagram of the Al-Cu-Fe Quasicrystal-Forming Alloy
System. III. Isothermal Sections”, Z. Metallkd., 94(2), 108-115 (2003) (Equi. Diagram,
Experimental, #, *, 14)
[2003Zha4] Zhang, L.M., Lück, R., “Phase Diagram of the Al-Cu-Fe Quasicrystal-Forming Alloy
System. IV. Formation and Stability of the -Al10Cu10Fe1 Phase”, Z. Metallkd., 94(3),
341-344 (2003) (Equi. Diagram, Experimental, Magn. Prop., 12)
[2003Mie] Miettinen, J., “Thermodynamic Description of the Cu-Al-Fe System at the Cu-Fe Side”,
Calphad, 27(1), 91-102 (2003) (Equi. Diagram, Thermodyn., #, *, 19)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Al)
<660.45
cF4
Fm3m
Cu
a = 404.88 pure Al [V-C2]
(Cu)
<1084.87
cF4
Fm3m
Cu
a = 361.48 pure Cu [V-C2]
( Fe)
1394-912
cF4
Fm3m
Cu
a = 366.60
a = 364.67
[V-C2]
[Mas2]
( Fe)
1538-1394
( Fe)
< 912
cI2
Im3m
W
a = 293.78
a = 293.15
a = 286.65
[V-C2]
[Mas2]
[V-C2], extensive joint solubility of Al
and Cu
Cu3Al
1049-559
cI2
Im3m
W
a = 294.6 [V-C2]
70.6 to 82 at.% Cu [Mas2]
, CuAl2<591
tI12
I4/mcm
Al2Cu
a = 606.3
c = 487.2
[V-C2]
31.9 to 33 at.% Cu [Mas2]
1, CuAl(h) 1)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
[V-C2, Mas2, 1985Mur]
49.8 to 52.4 at.% Cu [Mas2]
Pearson symbol: [1931Pre]
19
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
2, CuAl(r) 1)
<560
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
[V-C2]
49.8 to 52.3 at.% Cu [Mas2]
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2
Cu47.8Al35.5
a = 812
b = 1419.85
c = 999.28
55.2 to 59.8 at.% Cu [Mas2]
structure: [2002Gul]
2, Cu11.5Al9(r)
<570
oI24 - 3.5
Imm2
Cu11.5Al9
a = 409.72
b = 703.13
c = 997.93
[V-C2]
55.2 to 56.3 at.% Cu [Mas2, 1994Mur]
structure: [2002Gul]
1, CuxAl100-x
958-848
Cubic?
cP8
Pm3m
CsCl
[V-C2]
59.4 to 62.1 at.% Cu [Mas2]
[1998Wan]
2, Cu2-xAl
850-560
hP6
P63/mmc
InNi2
a = 414.6
c = 506.3
[V-C2]
55.0 to 61.1 at.% Cu [Mas2]
NiAs type in [Mas2, 1994Mur]
, Cu1-xAlx<686
hR*
R3m
a = 1226
c = 1511
0.381 x 0.407 [Mas2, 1985Mur]
59.3 to 61.9 at.% Cu [Mas2]
at x = 38.9 [V-C]
0, Cu100-xAlx1037-800
CI52
I43m
Cu5Zn8
- 59.8 to 69 at.% Cu [1998Liu]
1, Cu9Al4<890
CP52
P43m
Cu9Al4
a = 870.68
62 to 68.5 at.% Cu [Mas2, 1998Liu]
[V-C2] from single crystal
2, CuxAl100-x
<363
TiAl3long period
superlattice
a = 366.8
c = 368.0
76.5 to 78 at.% Cu [Mas2]
at 76.4 at.% Cu
(subcell only)
, FexCuyAlz
Fe4Al13
<1160
mC102
C2/m
Fe4Al13
a = 1548.9
b = 808.31
c = 1247.6
= 107.72°
0.22 < x < 0.31 [2003Zha1]
0 < y < 6
0.78 < z < 0.72
at x = 0.24
y = 0
z = 0.76 [V-C2]
Fe2Al5<1171
oC56
P63/mmc
Al5Co2
a = 767.5
b = 640.3
c = 420.3
[1953Sch]
for 72.0 at.% Al
70 to 73 at.% Al [1993Kat]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
20
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
1)1 and 2 phases are not distinquished in [2003Zha1, 2003Zha2, 2003Zha3], notation is used in the diagrams
Table 2: Invariant Equilibria
, FeAl2<1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
[1973Cor], [V-C]
66 to 66.9 at.% Al [1993Kat]
at 66.9 at.% Al [V-C2]
, Al3Fe2
1232-1102
cI16
a = 598.0
~58 to ~65 at.% Al [1993Kat]
at 61 at.% Al [V-C], [1988Ray]
, (FexCuyAlz)
FeAl
< 1310
cP8
Pm3m
CsCl
a = 290.9
0 < x < 1,
0 < y < 1,
~0.23 < z 0.70
ordered bcc [V-C2]
23.3 to ~55 at.% Al [1993Kat]
1, Fe3Al
<552.5
cF16
Fm3m
BiF3
a = 579.23 [V-C]
23 to 34 at.% Al [1993Kat]
* 1, Al23CuFe4 oC28
Cmcm
Al6Mn
a = 643.43
b = 746.04
c = 877.69
[1961Bla]
exp=3.62 Mgm-3
* 2, FeCu2Al7 tP40
P4/mnc
Al7Cu2Fe
a = 633.6
c = 1487.0
[1956Bow], [1958Bro]
exp= 4.30 Mgm-3
* 3, FeCu10Al10 hP5
P3m1
-Ni2Al3
- [1939Bra2]
* i, ~Fe12.5Cu25.5Al62 - - icosahedral face centered
6D hypercubic unit [1989Dev],
[1989Eba], [1990Cal], [1990Fau2]
* 4, Fe15Cu20Al65 cI62
Mg32(Al,Zn)49
a = 1407 [1988Che], sample was heterogeneous
( 4+ i)
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Fe
L + + ( Fe) Cu3Al 1048 P1 L 17.1 80.0 2.9
L + ( Fe) (Cu) + Cu3Al 1046 U1 L 17.0 81.0 2.0
L + Cu3Al 0 + 1015 U2 L 35.5 59.3 6.0
L + + i 882 P2 L 58.6 35.4 5.2
L + 2 ~750 p1max L 68.7 28.7 2.6
L + i + 2 ~740 U3 L 65.7 31.9 2.4
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
21
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
L + i + 2 ~695 U4 L 61.3 36.7 2.0
3 + i 640 esol.1max - - - -
3 + 2 ~630 esol.2max - - - -
L + 1 626 p2max L 90.2 8.4 1.4
L + 2 + ~622 U5 L 61.5 37.7 0.8
L + 1 + 2 622 U6 L 87.45 11.70 0.85
L + 1 + (Al) 620 U7 L
(Al)
94.4
99.35
4.90
0.63
0.70
0.02
+ 2 3 + ~618 Usol.1
2
48.8
44.7
49.0
55.0
2.2
0.3
+ i 3 + 2 ~616 Usol.2
i
52.5
61.9
44.0
28.3
3.5
9.8
L + 2 + ~595 U8 L 62.2 36.9 0.9
L + 1 2 + (Al) 590 U9 L
(Al)
89.80
99.88
9.65
0.12
0.55
0.001
L 2 + 588 e1max L 68.2 31.0 0.8
2 + + 3 ~580 Esol.1 52.0 44.5 3.5
L 2 + + ~565 E1 L 66.4 32.9 0.9
Cu3Al (Cu) + + 1 564 Esol.2 Cu3Al 24.2 75.3 0.5
L (Al) + 2 + 542 E2 L
(Al)
82.83
99.77
17.03
0.23
0.14
0.0006
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Fe
20 40500
750
1000
Fe 22.80Cu 0.00Al 77.20
Fe 0.00Cu 57.50Al 42.50Cu, at.%
Tem
pera
ture
, °C
P2,882
L
L+β
L+λ1
L+λ2
L+λ1+λ2
λ2 λ2+τi
(Al)+λ1
τi
τi+λ2+β
(Al)+λ1+λ2(Al)+λ2
L+λ2+τiL+τi+β
L+λ2+β
L+τi
β
τ3+ε2
β+ε2ε2
τi+β+τ3
τi+τ2+τ3
τ2+τ3 τ3
β+τ3
τi+τ3
τ3+ητ2+τ3+η
τ2+τ3+ββ+τ3+η
~630
580
616
L
L+ε1
L+ε2
ε2+δ1
ζ2+δ1
Fig. 1: Al-Cu-Fe.
Vertical section along
the composition line
between Fe22.8Al77.2
and Cu57.5Al42.5
22
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
20500
600
700
800
900
1000
1100
1200
Fe 20.00Cu 30.00Al 50.00
Fe 0.00Cu 10.00Al 90.00Cu, at.%
Tem
pera
ture
, °C
P2,882
U6,622
E2,542
L
L+λ
τi+β
λ+τi+β
L+β
L+λ+β
λ+τi
L+λ+τi
τi+τ2
τ2
L+λ+τ2
λ+τ2
L+τ1+τ2
L+(Al)+τ2
(Al)+θ+τ2
L+τ2
(Al)+θL+(Al)+θL+(Al)
L+τ1
L+λ+τ1
p1
τi
β
max
Fig. 2: Al-Cu-Fe.
Vertical section along
the composition line
between
Fe20Cu30Al50 and
Cu10Al90
10500
600
700
800
900
1000
1100
1200
Fe 0.00Cu 37.50Al 62.50
Fe 20.00Cu 21.00Al 59.00Fe, at.%
Tem
pera
ture
, °C
P2,882
Usol2
L
L+β
λ+β
τi+λ+βτi+β
L+λ+βL+λ
L+τi L+τi+
β
L+τi+τ2
L+τ2+β
L+τ2+η1U8,595
E1,565
τ2+η+τ3
τi+τ3+τ2τi+τ3τi+τ3+β
τ2+τi+βU4,695
L+τ2
θ+η2
L+η1+θL+η1
L+λ+τi
τ2+βesol1
τ2+η2+θ
max
L+η2+θL+τ2+η2
Fig. 3: Al-Cu-Fe
Vertical section along
the composition line
between
Fe20Cu21Al59 and
Cu37.5Al62.5
23
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10 20 30 40500
600
700
800
900
1000
1100
Fe 14.50Cu 0.00Al 85.50
Fe 3.50Cu 50.00Al 46.50Cu, at.%
Tem
pera
ture
, °C
P2,882
L+λ+β
L+β
L
L+λ
L+β+τi
L+λ+τi
L+τi
β
τi+βτ2+τi+β
τ2+τ3
τ2+η+τ3
τ2+τ3+β
τi+τ2+τ3
β+ε2
β+τ3
τ3+ε2
β+τ3+ητ3+ητ3
Esol1,580
Usol2,616
U4,695
U3,740
(Al)+τ1+τ2
L+τ1+τ2
L+λ+τ2
λ+τ2
τ2
τi+τ2
L+λ+τ1
(Al)+λ(Al)+λ+τ1
L+λ+(Al)
L+(Al)+τ1
L+τ1
(Al)+τ1
U9,590
U6,622
p1
τi+τ3+βp2
τi+τ2+L
Usol1U7,620
max
max
10500
600
700
800
900
1000
1100
1200
Fe 20.00Cu 25.00Al 55.00
Fe 0.00Cu 25.00Al 75.00Fe, at.%
Tem
pera
ture
, °C
LL+β
β
λ+β
L+λ+β
L+λ
L+τi
λ+τi
λ+τi+β
L+τ2
L+λ+τ2
L+τ2+θ
(Al)+θ+τ2E2,542
L+τi+τ2
L+τ2τ2+τi
E1
τ2+τi+τ3 θ+τ2
τ2+τi
τ2+η+τ3
e1U8,595
τi
L+λ+τi
U 3,740
U4,695
P2,882
β+
η+
τ2+τ3 τ2+θτ2+η
(Al)+θL+(Al)+θL+θ
β+
Esol1
Usol2
maxp1
max
Fig. 4: Al-Cu-Fe.
Vertical section along
the composition line
between Fe14.5Al85.5
and Fe3.5Cu50Al46.5
Fig. 5: Al-Cu-Fe.
Vertical section at
25 at.% Cu
24
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10 20 30 40500
750
1000
Fe 7.50Cu 0.00Al 92.50
Fe 7.50Cu 50.00Al 42.50Cu, at.%
Tem
pera
ture
, °C
L+β
β
L
L+λ
L+τ2
L+λ+τ2
L+τ1+τ2
L+(Al)+λL+λ+τ1
p2
L+τ1L+(Al)+τ1
(Al)+τ1+τ2
(Al)+τ1 (Al)+τ2
E2
(Al)+θ+τ2
τ2+θ
L+τ2+θ
L+(Al)+τ2
(Al)+τ1+λ τ2+θ
τ2+η τ2+τ3
τ2+τ3+η
Esol1
τ2+τ3+β
Usol2
τi+τ2+βτi+τ3+β
τi+τ3τi+τ2+τ3
τi+β
L+τi+βL+τi
U3
L+τi+λ
p1max
P2,882
U4,695L+τi+τ2
U6
U9
L+τ2+η
E1
L+τ2+βτ2+β
U8
η+(Al)+λ
L+λ+β
max
U7
10 20 30 40500
750
1000
Fe 5.00Cu 0.00Al 95.00
Fe 5.00Cu 50.00Al 45.00Cu, at.%
Tem
pera
ture
, °C
L
L+β
L+λ+β
L+τi+β
β
τi+β
τ3
τ2+τ3+τiτ2+η+τ3
τ2+τ3τ2+η
(Al)+τ1+τ2
(Al)+τ1
L+(Al)+τ1
L+τ1
L+τ1+τ2
L+λ+τ1L+(Al)+λ
(Al)+λ+τ1
(Al)+λL+(Al)+τ2
(Al)+τ2
E2 (Al)+τ2+θ
L+τ2+θ
τ2+θ+η
L+τ2+ηE1
U8,595
τ2+β+τ3
L+τ2+β
L+λ+τi
L+λ+τ2
L+λ
L+τ2
U9
U6
e1
τ2+βτ3+τi+β
β+τ3
τi+β+τ2
U2,695U3L+τi+τ2
p1
P2,882
p2
Esol1,580
L+τi
τ2+θ
U 7
τi+τ3
Usol2max
max
max
Fig. 7: Al-Cu-Fe.
Vertical section at
7.5 at.% Fe
Fig. 6: Al-Cu-Fe.
Vertical section at
5 at.% Fe
25
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10 20 30500
600
700
800
900
1000
1100
1200
Fe 10.00Cu 0.00Al 90.00
Fe 10.00Cu 40.00Al 50.00Cu, at.%
Tem
pera
ture
, °C
L
L+βL+λ+β
L+τi+β
L+τi
L+λ+τ i
U3,740
U4,695
L+τi+τ2
τi+τ2+β
τ1+β
τi+τ3+β
τi+τ3
τi+τ1+τ3
τi+τ2
τ2
τ2+λ
L+τ1+τ2
L+λ+τ2
U6,622
U9,590L+τ1(Al)+λ+τ1
L+λ+(Al)L+τ1+λ
p2
p1
L+(Al)+τ1
(Al)+τ1+τ2
(Al)+τ1
β
P2,882
L+λ
U7
(Al)+λ
max
max
Usol2
10 20 30500
600
700
800
900
1000
1100
1200
Fe 12.00Cu 0.00Al 88.00
Fe 12.00Cu 40.00Al 48.00Cu, at.%
Tem
pera
ture
, °C
L+β
L+λ+β
L
L+λ
L+(Al)+λL+λ+τ1
p2
L+λ+τ2
U6,622
λ+τ2λ+τ1+τ2
L+(Al)+τ1
(Al)+τ1+τ2
(Al)+τ1
(Al)+τ1+λ
p1
P2,882
L+τi+β
L+λ+τ
i
L+τi
τi+β
β
τi+τ2
τi
λ+τ2+τi
U3,740
L+τ1
L+τ1+τ2
U9,590
(Al)+λ
τ2+τ1
U7,620
max
max
Fig. 8: Al-Cu-Fe.
Vertical section at
10 at.% Fe
Fig. 9: Al-Cu-Fe.
Vertical section at
12 at.% Fe
26
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
20 40 60 80
750
1000
1250
1500
Fe 90.18Cu 0.00Al 9.82
Fe 0.00Cu 88.97Al 11.03Cu, at.%
Tem
pera
ture
, °C
(Cu)
(αδFe)
L+(αδFe)
(αδFe)+(Cu)
L
20 40 60
750
1000
1250
1500
Fe 81.30Cu 0.00Al 18.70
Fe 0.00Cu 79.26Al 20.74Cu, at.%
Tem
pera
ture
, °C
L
(αδFe)+L(αδFe)
(αδFe)+(Cu)
Cu3Al
(αδFe)+Cu3Al+(Cu)
Fig. 10: Al-Cu-Fe.
Calculated vertical
section at 5 mass% Al
Fig. 11: Al-Cu-Fe.
Calculated vertical
section at
10 mass% Al
27
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
20 40 60
750
1000
1250
1500
Fe 73.24Cu 0.00Al 26.76
Fe 0.00Cu 70.64Al 29.36Cu, at.%
Tem
pera
ture
, °C
L
(αδFe)+L(αδFe)
β(1)
Cu3Al
β(2)
β(1)+(Cu)β(2)+γ1
Tc
β(1)+β(2)
Fig. 13: Al-Cu-Fe. Partial reaction scheme for the Cu corner
Cu-Fe
l + (δFe) (γFe)
1487 p1
Al-Cu-Fe
L+(αδFe)+(γFe) Cu3Al1048 P
1
Al-Cu
l + Cu3Al γ
0
1037 p3
l + (γFe) (Cu)
1095 p2
l (Cu) + Cu3Al
1032 e1
Cu3Al (Cu)+γ
1+(αδFe)564 E
sol2
L+Cu3Al γ
0+(αδFe)1015 U
2
L+(γFe) (Cu)+Cu3Al1046 U
1
L+Cu3Al+(αδFe)
L + (γFe) +Cu3Al (αδFe) + (γFe) +Cu
3Al
(γFe)+(Cu)+Cu3Al
Cu3Al+γ
0+(αδFe)
(Cu) + γ1 + (αδFe)
L + γ0 + (αδFe)
Fig. 12: Al-Cu-Fe.
Calculated vertical
section at
15 mass% Al
28
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
Fig
. 14:
A
l-C
u-F
e.
Par
tial
reac
tion s
chem
e fo
r th
e A
l co
rner
Al-
Fe
Al-
Cu
-Fe
Al-
Cu
L +
λτ 1
62
6p2max
l (
Al)
+ λ
65
5e 2
L +
β +
λτ i
88
2P2
l +
ε2
η6
24
p4
L +
λτ 2
75
0p1
max
Lτ 2
+ η
+ θ
56
5E1
L +
βτ 2
+ η
59
5U8
L +
ε2
β +
η6
22
U5
L +
τi
β +
τ2
69
5U4
L+
λτ i
+ τ2
74
0U3
lθ
+ (
Al)
54
8e 3
l +
ηθ
59
1p5
Lτ 2
+ θ
58
8e 1
max
L +
λτ 1
+ τ2
62
2U6
L +
λτ 1
+ (
Al)
62
0U7
L +
τ1
τ 2+
(A
l)5
90
U9
L(A
l) +
τ2+
θ5
42
E2
l +
(A
l) +
λL
+λ+
τ 1
L+
τ 2+
λ
L+λ
+τ2
L+
λ+τ i
β+λ+
τ i
L+
τ 2+
τ iλ+
τ 2+
τ i
τ 2+λ
+τ1
L +
(A
l) +
τ1
(Al)
+λ+
τ 1
(Al)
+τ 2
+τ1
L+
(Al)
+τ 2
L+
θ+(A
l)
L+
θ+τ 2
(Al)
+τ 2
+θ
L+
ε 2+η
τ i+τ 2
+β
L+
ε 2+β
L+
β+η
β+ε 2
+η
L+
τ 2+
η
L+
θ+η
η+τ 2
+θ
?
βτ 3
+ τi
64
0e sol1max
βτ 3
+ ε2
63
0e sol2max
β +
ε2
τ 3+
η6
18
Usol1
β +
τi
τ 2 +
τ3
61
6Usol2
τ i+β+
τ 3τ i+
β+τ 3 β+
τ 3+
ε 2β+
τ 3+
ε 2
βτ 2
+ η
+τ 3
58
0Esol1
L+
θ+τ 2
β+τ 2
+ηβ+
τ 2+
τ 3τ 2
+τ i+
τ 3
τ 3+
ε 2+
η
L+
τ 2+
τ 1
L+
β+τ i
L+
τ 2+
β
η+τ 3
+τ 2
L+
λ+τ 1
β+η+
τ 3
L+
β+λ
29
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10
20
30
40
60 70 80 90
10
20
30
40
Fe 45.00Cu 55.00Al 0.00
Cu
Fe 0.00Cu 55.00Al 45.00 Data / Grid: at.%
Axes: at.%
p2
e1
p3
U2
U1
(Cu)
Cu3Al
γ0
(αδFe)
(γFe)
P1
10
20
30
40
10 20 30 40
60
70
80
90
Fe 50.00Cu 0.00Al 50.00
Fe 0.00Cu 50.00Al 50.00
Al Data / Grid: at.%
Axes: at.%
λ
β
Fe2Al5
τ i
U4
U8
E1
P2
E2
U6
p 2
U7
e2
1100
10501000
950900
800750
700
U9
e3
τ2
θ
p5
p4
η
ε2
(Al)
τ1
U5
U3
e1
maxp1
max
max
Fig. 15: Al-Cu-Fe.
Partial liquidus
surface projection of
the Cu corner
Fig. 16: Al-Cu-Fe.
Liquidus surface
projection and
contour lines for the
Al-rich portion
30
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10
20
30
40
10 20 30 40
60
70
80
90
Fe 50.00Cu 0.00Al 50.00
Fe 0.00Cu 50.00Al 50.00
Al Data / Grid: at.%
Axes: at.%
λ
τ1
τ2
τ i
p5
e3E2
U6
U9
U7
e2 (Al)
p1max
e1max
Fe2Al5
p4
U5
U4
U8
E1
P2
τ i
β
U3
20
40
60
80
20 40 60 80
20
40
60
80
Fe Cu
Al Data / Grid: at.%
Axes: at.%
δ1
ζ2
η2
θ
β
τ1
τ2
τ i
τ3
λFe2Al5
(Al)
Fig. 17: Al-Cu-Fe.
Liquidus surface
projection and
invariant planes
Fig. 18: Al-Cu-Fe.
Al-rich part of the
isothermal section at
room temperature
31
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
20
40
60
80
20 40 60 80
20
40
60
80
Fe Cu
Al Data / Grid: at.%
Axes: at.%
β+Cu3Al
β(1)+β(2)
β
(αδFe)
(αδFe)+(Cu)
λFe2Al5
ζ
L
(Cu)
β+(Cu)Cu3Al
γ1
ε2
20
40
60
80
20 40 60 80
20
40
60
80
Fe Cu
Al Data / Grid: at.%
Axes: at.%
β
Cu3Al
(αδFe)
β(1)+β(2)
β+Cu3Al
(αδFe)+(Cu)
λFe2Al5
ζ
L
(Cu)
Fig. 19: Al-Cu-Fe.
Calculated
isothermal section at
800°C
Fig. 20: Al-Cu-Fe.
Calculated isothermal
section at 900°C
32
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
20
40
60
80
20 40 60 80
20
40
60
80
Fe Cu
Al Data / Grid: at.%
Axes: at.%
λFe2Al5
ζ
(αδFe)
β β(1)+β(2)
β+Cu3Al
(αδFe)+Cu3Al
(αδFe)+(Cu)
L
(Cu)
(γFe)
Cu3Al
20
40
60
80
20 40 60 80
20
40
60
80
Fe Cu
Al Data / Grid: at.%
Axes: at.%
L
β
λFe2Al5
ζ
β+L
(αδFe)
(αδFe)+L
(γFe)
Fig. 21: Al-Cu-Fe.
Calculated isothermal
section at 1000°C
Fig. 22: Al-Cu-Fe.
Calculated isothermal
section at 1100°C
33
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
20
40
60
80
20 40 60 80
20
40
60
80
Fe Cu
Al Data / Grid: at.%
Axes: at.%
β
(αδFe)
L
β+L
(αδFe)+L
ε
(γFe)
20
40
60
80
20 40 60 80
20
40
60
80
Fe Cu
Al Data / Grid: at.%
Axes: at.%
(αδFe)
L
(γFe)
(αδFe)+L
Fig. 23: Al-Cu-Fe.
Calculated isothermal
section at 1200°C
Fig. 24: Al-Cu-Fe.
Calculated isothermal
section at 1300°C
34
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10
20
30
40
50
10 20 30 40 50
50
60
70
80
90
Fe 60.00Cu 0.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Al Data / Grid: at.%
Axes: at.%
Fe2Al5+β
λ+βλ+Fe
2 Al5 +β
λ+Fe2Al5 λ λ+L
λ+τ i+L
β+L
β
β+τi +λ
β+τ i
β+τi +L
β+ε2+L
ε2
β+ε2
L+ε2
L
τ i L+τ i
10
20
30
40
50
10 20 30 40 50
50
60
70
80
90
Fe 60.00Cu 0.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Al Data / Grid: at.%
Axes: at.%
λ
L
L+λ
β
τ2
τ i
ε2
L+λ+τ2
λ+τ2
L+τ2
λ+τi +β
λ+β
λ+β+Fe2 Al
5 L+τ i
L+τ i+βτ i+β
β+ε2
L+β+ε2
L+ε2
L+β
Fig. 25: Al-Cu-Fe.
Isothermal section in
the Al-rich portion at
800°C
Fig. 26: Al-Cu-Fe.
Isothermal section in
the Al-rich portion at
700°C
35
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10
20
30
30 40 50
50
60
70
Fe 40.00Cu 20.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Fe 0.00Cu 20.00Al 80.00 Data / Grid: at.%
Axes: at.%
β
τ3β+τ3
β+ε2
L+β+ε2
ε2
L+τ2
L
L+β
L+ε2τ i+β
τ i+λ
λ+τ i+β
λ+β
τ iτ2 +β+L
τ2
τ2+λ+τ i
10
20
30
30 40 50
50
60
70
Fe 40.00Cu 20.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Fe 0.00Cu 20.00Al 80.00 Data / Grid: at.%
Axes: at.%
λ+β
λ+τ i+β
τ i+β
τ i+λτ i
τ2+L
L+τ2 +β
β+ε2
β+τ3+ε2
ε2
η+ε2
β+η+ε2β+τ3
L+η+ββ
τ3β
L
η
L+η
τ i+β+τ3
τ2
τ i+λ+β
Fig. 28: Al-Cu-Fe.
Isothermal section in
the Al-rich portion at
620°C
Fig. 27: Al-Cu-Fe.
Isothermal section in
the Al-rich portion at
645°C
36
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10
20
30
30 40 50
50
60
70
Fe 40.00Cu 20.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Fe 0.00Cu 20.00Al 80.00 Data / Grid: at.%
Axes: at.%
λ+β
τ i+λ+β
τ i+β
β+ε2ε2
η+ε2
β
τ3
τ2+L
L
L+β+η
τ3+ε2
τ i+λ
τ iL+τ
2 +β
β
τ2
η
τ i+β+λ
10
20
30
30 40 50
50
60
70
Fe 40.00Cu 20.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Fe 0.00Cu 20.00Al 80.00 Data / Grid: at.%
Axes: at.%
τ i+λ+β
β
τ3
L+τ2 +β
L+β+η
τ i
L
τ2
η
β+τ iβ+λ
L+τ2
β+ε2
ε2
λ+τ i+τ2
λ+τ i
β
τ3+ε2
Fig. 29: Al-Cu-Fe.
Isothermal section in
the Al-rich portion at
617°C
Fig. 30: Al-Cu-Fe.
Isothermal section in
the Al-rich portion at
600°C
37
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Fe
10
20
30
30 40 50
50
60
70
Fe 40.00Cu 20.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Fe 0.00Cu 20.00Al 80.00 Data / Grid: at.%
Axes: at.%
L
η
ε2
τ3
β
τ2
τ i
τ i+λ+β
L+τ2 +η
τ i+β
L+τ2
λ+τ i+τ2
β+ε2
βλ+β
τ3+ε2
10
20
30
30 40 50
50
60
70
Fe 40.00Cu 20.00Al 40.00
Fe 0.00Cu 60.00Al 40.00
Fe 0.00Cu 20.00Al 80.00 Data / Grid: at.%
Axes: at.%
λ+β
λ+τ i+β
τ i+β
τ i
λ+τ i
τ2+θ+η
L+θ+τ2
ε2
β+ε2
τ2 +τ
3 +η
η+τ3+ε2
β
τ3
L
τ2
η
θ
τ3 +ε
2
λ+τ i+τ2
Fig. 31: Al-Cu-Fe.
Isothermal section
diagram in the Al-rich
portion at 592°C
Fig. 32: Al-Cu-Fe.
Isothermal section in
the Al-rich portion at
560°C
38
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
Aluminium – Copper – Gadolinium
Paola Riani, Pierre Perrot
Literature Data
First critical evaluation of the Al-Cu-Gd data was made within the MSIT Ternary Evaluation Program by
[1991Ran] incorporating literature data up to 1988. The present assessment continues the work of
[1991Ran] and considers all information published up to 2002, which leads to amended descriptions of the
reliably known phase equilibria.
As for the phase equilibria, isothermal section at 500 and 600°C have been studied by [1988Pre] and
[2001Gum], respectively. [1988Pre] prepared 76 alloys by arc melting the constituent metals under argon
and annealing at 500°C for not less than 400 hours and quenching. [2001Gum] synthesized 38 ternary
samples by arc melting under purified Ar atmosphere of the components of purities of 99.5 mass% Gd,
99.95 mass% Cu and Al. All alloys prepared were heat treated at 600 and 500°C in evacuated silica
ampoules for 1000 h and then quenched in cold water. Generally X-ray powder diffraction techniques were
used for phase analysis, determination of solubility, etc.
Other contributions to the phase relationships result from the determining the mutual solubility of GdAl2and GdCu2. [1973Hid] annealed samples for two weeks at 800°C; using X-ray diffraction they established
the solubility limit of GdCu2 in GdAl2 to be at 20 at.% over-all Cu concentration. [1974Oes] studied the
homogeneity ranges of GdCu2 and GdAl2 by substituting Cu by Al and Al by Cu, respectively, on samples
prepared by induction melting and quenching. The limits reported are: Cu in GdCu2 can be replaced by Al
up to about 1 at.%, Al in GdAl2 can be replaced by Cu up to about 10 at.%. Between these two binary
compounds, at the composition GdCuAl, the sample has the Fe2P type structure [1968Dwi, 1973Oes,
1975Bus, 1988Pre]. This compound has no significant homogeneity range on the line GdAl2 to GdCu2. The
high pressure modification of GdCuAl and its structure were reported by [1987Tsv1, 1987Tsv2]. Other
ternary compounds were found or confirmed: GdCu4Al8 by [1976Bus] and [1979Fel], GdCu6Al6 by
[1980Fel] and [1981Fel], GdCu4Al by [1978Tak], Gd2Cu7Al10 by [1982Pre], and Gd2Cu6Al11 by
[1978Pop]. [1986Bor] determined the temperature dependence of the lattice parameters of the binary
compound Gd(Cu1-xAlx)2 for temperatures below 150 K with x values up to 0.07.
Binary Systems
The binary systems Al-Gd from [2002Bod], Al-Cu from [2003Gro] and Cu-Gd from [1988Sub, 1994Sub]
are used as boundary systems.
Solid Phases
The solubility of Al in the compound GdCu2 is not more than 3 at.% according to [1988Pre] which is in
good agreement with the value of [1974Oes], whereas different values have been reported for the solubility
of Cu in GdAl2: negligible according to [1988Pre] and [2001Gum], and 10 at.% Cu [1974Oes] or 20 at.%
Cu [1973Hid] and [1994Mag]. Notice however that in the figure reported by [2001Gum] and shown here
an extension of the GdAl2 phase up to about 5 at.% is presented.
The following remarks may be noteworthy for the different ternary phases.
For GdCuAl3 the crystal structure described as BaAl4 by [1988Pre] and assumed to be BaNiSn3 type by
[1994Mul], was not confirmed by [2001Gum]; however the compound Gd3Cu2.1Al8.9 with a close
composition and the related oI28 La3Al11 type structure, was found.
Magnetic properties of GdT4Al8 and GdT6Al6 (T = Cr, Mn, Cu) and crystallographic site occupation were
described by [2001Duo]. The phases GdCu4Al8 and GdCu6Al6 have the same structure (ThMn12 type) and
probably belong to the same solid solution range, although the investigators did not mention this point.
39
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
For the ternary alloys the phase with the ideal BaCd11 type structure has been described for GdCu7.8Al3.2,
with Gd in 4a, Cu in 8d and (Cu+Al) in 4b and 32i by [2001Gum]; an orthorhombic variant of this structure
was observed for GdCu6.6Al4.4 [2001Gum] with similar values of the co-ordination numbers.
For the Gd2(Cu,Al)17 compound the crystal structure was described by [1982Pre, 1988Pre, 2001Gum] as
pertaining to the Th2Zn17 type, corresponding to Gd in 6c, Cu in 9d and a mixed occupation (Cu + Al) in
the other sites. For the Gd2Cu7Al10 compound [1982Pre] a homogeneity range was described by [1988Pre]
and [2001Gum] respectively by the formula Gd2Cu6.7-8.0Al9.0-10.3 and Gd2Cu9.4-6.7Al7.6-10.3.
According to [1978Pop] the structure Th2Ni17 type was observed in the Gd system at ~Gd2Cu6Al11; this
phase however was not confirmed by [1988Pre] and [2001Gum].
The alloy GdCu4Al, which was reported as a ternary compound [1978Tak], is included in the ternary
homogeneity range of the binary compound Gd(Cu1-xAlx)5 with 0 x 0.6 derived from GdCu5, to which
a limit of solubility for Al up to 50 at.%, with the formula of GdCu2Al3 was assigned [1988Pre]. Details on
crystal structures of the solid phases are reported in Table 1.
Isothermal Sections
Based on crystallographic data Kuz’ma and co-authors published equilibria in two subsequent papers,
[1988Pre], [2001Gum]. The isothermal sections at 500 and 600°C published in both papers are
incompatible, however the applied changes are not commented and no indication is given how the equilibria
have been concluded. The problem arising from the two papers may be summarized as follows: the phase
previously indicated by [1988Pre] as GdCuAl3 (BaAl4 type) was not found by [2001Gum] (neither at 500°C
nor at 600°C); a composition 5,Gd3Cu2.1Al8.9 was instead proposed for a phase with the structure La3Al11
type. The new phase 6,GdCu0.9Al2.1 (PuNi3 type) was identified by [2001Gum]. For the phase with
unknown structure previously indicated by [1988Pre] as GdCu5Al4, the composition 2,GdCu7.8Al3.2
(BaCd11 type) was proposed by [2001Gum]. The phase indicated as ~GdCu11Al8 in the English version of
[1988Pre], but cited by [2001Gum] as Gd2Cu11Al8, referring to the same publication of [1988Pre], but to
the Russian version, is described as 3,GdCu6.6Al4.4 (Tb(Cu0.58Al0.42)11 type) by [2001Gum]. In the earlier
published 500°C isothermal section by [1988Pre] the 2, 3 phases were not characterized in their structure
and the annealing times were much shorter than in the later published work of [2001Gum] in which structure
and composition ranges of the phases have been refined. In [2001Gum] the authors claim to have found at
both temperatures, 500 and 600°C, the same phases but do not give an isothermal section at 500°C. The
present evaluation accepted the phases and phase compositions as published in [2001Gum] and amended
with considerable reservation the 500°C section accordingly. This revealed that the refined compositions of
2, 3 and 5 can not exist in an equilibrium configurations as shown earlier by [1988Pre]. Therefore the
equilibria at 500°C had to be modified, too, to show a possible configuration. See the isothermal section at
500°C, Fig. 1.
There is some disagreement between the accepted binary Al-Cu system [2003Gro] and the Al-Cu phases
shown in the diagrams by [1988Pre] and [2001Gum]. In the 600°C section by [2001Gum] no indication is
given of the liquid phase in the Al-rich region. The 2 phase should possibly be 1, instead of the phase
should have been observed. The phase sequence along the Al-Cu edge at 600°C reported in [2001Gum]
would be in better agreement with the accepted binary Al-Cu system with a temperature of ~ 550°C instead
of 600°C, except for the phase. Fig. 2 shows the partial isothermal section at 600°C after [2001Gum]
corrected to eliminate the above inconsistencies.
The present evaluation supersedes the slightly different evaluation made in the MSIT Evaluation Program
by [1991Ran].
Notes on Materials Properties and Applications
[2001Duo] studied the magnetic properties of GdCu4Al8 and GdCu6Al6 by means of standard
magnetization and susceptibility measurements, magnetization measurements in high fields up to 35 T and
measurements of specific heat; moreover they analyzed the data in terms of a simple mean-field
two-sublattice model and found that the coupling between Gd moments is fairly weak and leads to
antiferromagnetic ordering at rather low temperatures.
40
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
Magnetic and electrical properties of the GdCu5-xAlx (x = 0 to 2) alloys have been described by [1998Tun]:
all the alloys were of the CaCu5 type; to avoid the cubic AuBe5 type, splat cooling was applied to
GdCu5-xAlx alloys with x = 0 and 0.1; for 0.5 x 2.0 it was found that the AuBe5 type structure does not
exist and these compounds melt congruently to form the hexagonal CaCu5 type structure.
[1994Mul] investigated the magnetic properties and the 155Gd Mössbauer spectra of GdCuAl3 which was
found to order anti-ferromagnetic at low temperatures.
[1998Jav] studied the magnetic properties of the RCuAl (R = Y, Ce to Sm, Gd to Tm and Lu) intermetallic
compounds by means of susceptibility, magnetization and specific heat measurements and observed a
magnetic ordering at low temperatures in most of these materials: PrCuAl and NdCuAl showed an
antiferromagnetic behavior while in the heavy rare-earth compounds (R=Gd-Er) a ferromagnetic coupling
was found.
The magnetization, electrical resistivity and AC susceptibility measurements, carried out by [2000Jar],
provide evidence for a ferromagnetic type of order-disorder transition at 83 K in GdCuAl; a second
transition at 23 K was also found.
References
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Phials. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1968Dwi] Dwight, A.E., Müller, M.H., Conner, R.A.Jr., Downey, J.W., Knott, H., “Ternary
Compounds with the Fe2P-Type Structure”, Trans. Met. Soc. AIME, 242, 2075-2080 (1968)
(Crys. Structure, Experimental, 14)
[1973Hid] Hidaka, M., Sakai, M., Hosokawa, H., Sakurai, J., “The Paramagnetic Curie Temperature
of the Alloys Gd(Al1-xCux)2 and Gd(Al1-xNix)2”, J. Phys. Soc. Japan, 35, 452-455 (1973)
(Crys. Structure, Experimental, 12)
[1973Oes] Oesterreicher, H., “Structural and Magnetic Studies on Rare Earth Compounds RNiAl and
RCuAl”, J. Less-Common Met., 30, 225-236 (1973) (Crys. Structure, Experimental, 21)
[1974Oes] Oesterreicher, H., “Constitution of Aluminum Base Rare Earth Alloys RT2-RAl2 (R = Pr,
Gd, Er; T = Mn, Fe, Co, Ni, Cu)”, Inorg. Chem., 13, 2807-2811 (1974) (Crys. Structure,
Equi. Diagram, Experimental, 30)
[1975Bus] Buschow, K.H.J., “Note on the Magnetic Properties of Some Fe2P-Type Rare-Earth
Intermetallic Compounds”, J. Less-Common Met., 39, 185-188 (1975) (Crys. Structure,
Experimental, 1)
[1976Bus] Buschow, K.H.J., van Vucht, J.H.N., van den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth - 3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Crys. Structure, Experimental, 2)
[1978Pop] Pop, I., Coldea, M., Wallace, W.E., “NMR and Magnetic Susceptibility of Gd2Cu6Al11 and
Gd2Co6Al11 Intermetallic Compounds”, J. Solid State Chem., 26, 115-121 (1978) (Crys.
Structure, Experimental, 7)
[1978Tak] Takeshita, T., Malik, S.K., Wallace, W.E., “Crystal Structure of RCu4Ag and RCu4Al (R =
Rare Earth) Intermetallic Compounds”, J. Solid State Chem., 23, 225-229 (1978) (Crys.
Structure, Experimental, 8)
[1979Fel] Felner, I., Nowik, I., “Magnetism and Hyperfine Interactions of 57Fe, 151Eu, 155Gd, 161Dy,166Er and 170Yb in RM4Al8 Compounds (R=Rare Earth or Y, M=Cr, Mn, Fe, Cu)”., J. Phys.
Chem. Solids, 40, 1035-1044 (1979) (Crys. Structure, Experimental, 8)
[1980Fel] Felner, I., “Crystal Structure of Ternary Rare Earth - 3d Transition Metal Compounds of the
RT6Al6 Type”, J. Less-Common Met., 72, 241-249 (1980) (Crys. Structure, Experimental,
10)
[1981Fel] Felner, I., Seh, M., Rakavy, M., Nowik, I., “Magnetic Order and Hyperfine Interactions in
RFe6Al6 (R = Rare Earth)”, J. Phys. Chem. Solids, 42, 369-377 (1981) (Crys. Structure,
Experimental, 6)
41
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
[1982Pre] Prevarskiy, A.P., Kuz'ma, Yu.B., “New Compounds with Th2Sn17 Type Structure in
REM-Al-Cu Systems”, Russ. Metall., 6, 155-156 (1982) (Crys. Structure, Experimental, 5)
[1985Mur] Murray, J.L., “The Aluminum-Copper System”, Int. Met. Rev., 30(5), 211-233 (1985) (Equi
Diagram, Crys. Structure, Review, 230)
[1986Bor] Borombaev, M.K., Levitin, R.Z., Markosyan, A.S., Smetana, Z., Sneginev, V.V., Svoboda,
P., “Magnetic and Crystallographic Properties of Gd(Cu1-xNix)2 and Gd(Cu1-xAlx)2
Intermetallic Compounds”, Phys. Status Solidi, 97, 501-509 (1986) (Crys. Structure,
Experimental, Magn. Prop., 13)
[1987Tsv1] Tsvyashchenko, A.V., Fomicheva, L.N., “High-Pressure Synthesis and Structural Studies of
Rare Earth (R) Compounds RCuAl”, J. Less-Common Met., 134(2), L13-L15 (1987) (Crys.
Structure, Experimental, 10)
[1987Tsv2] Tsvyashchenko, A.V., Fomicheva, L.N., “New Polymorphic Modifications of the
Compounds RTAl (R = r.e.m., T = Cu, Ni)”, Inorg. Mater., 23, 1024-1027 (1987), translated
from Izv. Akad. Nauk SSSR, Neorg. Mater., 23(7), 1148-1152 (1987) (Crys. Structure,
Experimental, 15)
[1988Gsc] Gschneidner, Jr K.A., Calderwood, F.W., “The Al-Gd (Aluminum-Gadolinium) System”,
Bull. Alloy Phase Diagrams, 9, 680-683 (1988) (Equi. Diagram, Review, 41)
[1988Pre] Prevarskii A.P., Kuz'ma, Yu.B., “X-Ray Structural Investigation of the System Gd-Cu-Al”,
Russ. Metall., (1), 205-207 (1988), translated from Izv. Akad. Nauk SSSR, Met., (1), 207-209
(1988) (Crys. Structure, Equi. Diagram, Experimental, 6)
[1988Sub] Subramanian, P.R., Laughlin, D.E., “The Cu-Gd (Copper-Gadolinium) System”, Bull. Alloy
Phase Diagrams, 9, 347-354 (1988) (Equi. Diagram, Review, 34)
[1989Mee] Meetsma, A., de Boer, J.L., van Smaalen, S., “Refinement of the Crystal Structure of
Tetragonal Al2Cu”, J. Solid State Chem., 83(2), 370-372 (1989) (Crys. Structure,
Experimental, 17)
[1991Ell] Ellner, M., Kolatschek, K., Predel, B., “On the Partial Atomic Volume and the Partial Molar
Enthalpy of Aluminium some Phases with Cu and Cu3Al Structures”, J Less-Common
Metals, 170, 171-184 (1991) (Crys. Structure, Experimental, 57)
[1991Ran] Ran, Q., “Aluminium - Copper - Gadolinium”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.12786.1.20 (1991) (Crys. Structure, Equi. Diagram,
Assessment, 23)
[1994Mag] Magnitskaya, M., Chelkowska, G., Borstel, G., Neumann, M., Ufer, H.,
“ElectronicStructure of Gd-Based Laves Phase Alloys”, Phys. Rev. B, 49, 1113-1119 (1994)
(Calculation, Magn. Prop., Crys. Structure, 25)
[1994Mul] Mulder, F.M., Thiel R.C., Buschow, K.H.J., “155Gd Mössbauer Effect in Several
BaNiSn3-Type Compounds”, J. Alloys Compd., 216, 95-98 (1994) (Crys. Structure, Magn.
Prop., Moessbauer, 9)
[1994Mur] Murray, J.L., “Al-Cu (Aluminum-Copper)” in “Phase Diagrams of Binary Copper Alloys”,
Subramanian, P.R., Chakrabarti, D.J., Laughlin, D.E. (Eds.), ASM International Materials
Park, OH, Vol. 10, 18-42, (1994) (Equi. Diagram, Review, 226)
[1994Sub] Subramanian P.R., Laughlin, D.E., “The Cu-Gd (Copper-Gadolinium) System” in “Phase
Diagrams of Binary Copper Alloys”, Subramanian, P.R., Chakrabarti, D.J., Laughlin, D.E.
(Eds.), ASM International, Materials Park, OH, Vol. 10, 185-190 (1994) (Equi. Diagram,
Review, 33 )
[1996Goe] Gödecke, T., Sommer, F., “Solidification Behaviour of the Al2Cu Phase”, Z. Metallkd.,
87(7), 581-586 (1996) (Equi. Diagram, Crys. Structure, 8)
[1998Jav] Javorský, P., Havela, L., Sechovský, V., Michor, H., Jurek, K., “Magnetic Behaviour of
RCuAl Compounds”, J. Alloys Compd., 264, 38-42 (1998) (Experimental, Magn. Prop.,
Crys. Structure, 15)
42
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264(1-2), 201-208 (1998) (Equi. Diagram,
Crys. Structure, 25)
[1998Tun] Tung, L.D., Buschow, K.H.J., Franse, J.J.M., Brommer, P.E., Duijn, H.G.M., Brück, E.,
Thuy, N.P., “Magnetic and Electrical Properties of the Pseudo-Binary GdCu5-xAlxCompounds”, J. Alloys Compd., 269, 17-24 (1998) (Crys. Structure, Electr. Prop.,
Experimental, Magn. Prop., 22)
[2000Jar] Jarosz, J., Talik, E., Mydlarz, T., Kusz, J., Boehm, H., Winiarski, A., “Crystallographic,
Electronic Structure and Magnetic Properties of the GdTAl; T = Co, Ni and Cu Ternary
Compounds”, J. Magn. Magn. Mater., 208, 169-180 (2000) (Crys. Structure, Experimental,
Magn. Prop., 23)
[2000Sac] Saccone, A., Cardinale, A.M., Delfino S., Ferro R., “Gd-Al and Dy-Al Systems: Phase
Equilibria in the 0 to 66.7 at.% Al Composition Range”, Z. Metallkd., 91(1), 17-23 (2000)
(Experimental, Equi. Diagram, Crys. Structure, 12)
[2001Duo] Duong, N.P., Klaasse, J.C.P., Brück, E., de Boer, F.R., Buschow, K.H.J., “Magnetic
Properties of GdT4Al8 and GdT6Al6 Compounds (T = Cr, Mn, Cu)”, J. Alloys Compd., 315,
28-35 (2001) (Experimental, Magn. Prop., 18)
[2001Gum] Gumeniuk, R.V., Stel’makhovych, B.M., Kuz’ma, Yu.B., “The Gd-Cu-Al System”, J.
Alloys Compd., 329, 182-188 (2001) (Crys. Structure, Equi. Diagram, Experimental, 27)
[2002Bod] Bodak, O., “Al-Gd (Aluminium-Gadolinium)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 20.12303.1.20 (2002) (Crys. Structure, Equi. Diagram,
Assessment, 15)
[2002Gul] Gulay, L.D., Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. ”Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2003Gro] Gröbner, J., “Al-Cu (Aluminium - Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 68)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
(Cu)
< 1084.62
Cu1-xAlx
cF4
Fm3m
Cu
a = 361.46
a = 361.52
a = 365.36
at 25°C [Mas2], 0 to 19.7 at.% Al [Mas2]
0 to 0.1 at.% Ce at 876°C [1994Sub]
[1991Ell], x = 0, quenched from 600°C
[1991Ell], x = 0.152, quenched from 600°C
( Gd)
1313-1235
~630°C (10.5 at.% Cu)
cI2
Im3m
W
a = 406 [Mas2]
~10 to 15 at.% Cu at 675°C, [1994Sub]
0 to ~3 at.% Al at 1200°C, [2000Sac]
( Gd)
< 1235
hP2
P63/mmc
Mg
a = 363.36
c = 578.10
at 25°C [Mas2]
0 to ~2 at.% Cu at 630°C, [1994Sub]
0 to ~0.9 at.% Al at 1200°C, [2000Sac]
, Cu3Al(h)
1049-559
cI2
Im3m
W
a = 294.6
a = 295.64
~70 to 82 at.% Cu [1985Mur], [1998Liu]
at 580°C
at 672°C in two-phase (Cu)+ alloy
43
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
2, Cu100-xAlx< 363
t**
TiAl3long period
super-lattice
a = 366.8
c = 368.0
22 x 23.5 [1985Mur]
76.5 to 78.0 at.% Cu
at 76.4 at.% Cu (subcell only)
0, Cu100-xAlx Cu~2Al
1037-800
cI52
I43m
Cu5Zn8
31.5 x 37 [Mas2],
63 to 68.5 at.% Cu [1998Liu]
1, Cu9Al4< 890
cP52
P43m
Cu9Al4
a = 870.23
a = 870.68
62 to 68 at.% Cu [Mas2, 1998Liu];
from single crystal [V-C] at 68 at.% Cu
from single crystal [V-C]
, Cu100-xAlx< 686
hR*
R3m
a = 1226
c = 1511
38.1 x 40.7 [1985Mur]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C]
1, Cu100-xAlx958-848
cubic? 37.9 x 40.6
59.4 to 62.1 at.% Cu [Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6-x
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.45 x 0.78
55 to 61 at.% Cu [Mas, 1985Mur, V-C2],
NiAs in [Mas2, 1994Mur]
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2
Cu47.8Al35.5
a = 812
b = 1419.85
c = 999.28
55.2 to 57 at.% Cu [Mas2, 1994Mur]
structure: [2002Gul]
2, Cu11.5Al9(r)
< 570
oI24 - 3.5
Imm2
Cu11.5Al9
a = 409.72
b = 703.13
c = 997.93
55.2 to 56.3 at.% Cu [Mas2, 1985Mur]
structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]
Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu [V-C]
, CuAl2< 592
tI12
I4/mcm
CuAl2 a = 606.7
c = 487.7
32.05 to 32.6 at.% Cu at 549°C
32.4 to 32.8 at.% Cu at 250°C [1996Goe]
single crystal [V-C2, 1989Mee]
Gd2Al
< 940
oP12
Pnma
Co2Si
a = 674.2
b = 525.4
c = 975.6
a = 661.2
b = 515.0
c = 957.8
a = 660.6
b = 514.6
c = 953.1
as cast, [2000Sac]
cooled 10 K min-1, [2000Sac]
[1988Gsc]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
44
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
Gd3Al2< 970
tP20
P42/mnm
Zr3Al2
a = 832.0
c = 762.8
a = 833.9
c = 762.0
cooled 10 K min-1, [2000Sac]
[1988Gsc]
GdAl
< 1070
oP16
Pmma
ErAl
a = 589.3
b = 1159
c = 569.5
a = 588.8
b = 1153
c = 565.6
cooled 10 K min-1, [2000Sac]
[1988Gsc]
Gd(CuxAl1-x)2
GdAl2< 1520
cF24
Fd3m
MgCu2
a = 790.6
a = 790.0
a = 782.37
0 x 0.075 at 600°C [2001Gum]
at x = 0 cooled 10 K min-1, [2000Sac]
at x = 0 [1988Gsc]
at x = 0.25 [1994Mag]
GdAl3< 1125
hP8
P63/mmc
Ni3Sn
a = 633.1
c = 460.0
[1988Gsc]
GdCu
< 830
cP2
Pm3m
CsCl
a = 350.1 to 350.5 [1994Sub]
Gd(Cu1-xAlx)2
GdCu2
< 860
oI12
Imma
CeCu2 a = 432 to 433
b = 686 to 689
c = 733 to 738
0 x 0.06 at 600°C (from diagram
reported in [2001Gum])
x = 0 [1994Sub]
Gd2Cu7
~870-825
[1994Sub]
high temperature phase
Gd2Cu9
< 930
t** a = 500
c = 1390
[1994Sub]
GdCu5
925-~870
Gd(Cu1-x Al x)5
hP6
P6/mmm
CaCu5
a = 502 to 504
c = 412 to 410
a = 531
c = 431
at x = 0 [1994Sub]
a homogeneity range of 0 x 0.6
reported by [1988Pre, 2001Gum] and
presented in their isothermal sections at
500 and 600°C, respectively. However at
these temperatures, the CaCu5 type phase
should be metastable according to
[1994Sub]
at x = 0.6 [1988Pre]
GdCu5
< ~870
cF24
F43m
AuBe5
a = 706 [1994Sub]
GdCu6
< 865
oP28
Pnma
CeCu6
a = 803 to 804
b = 502 to 501
c =1001 to 999.5
[1994Sub]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
45
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
GdCu7
~850 to ~700 (?)
hP8
P6/mmm
TbCu7
a = 495.1
c = 417.1
[1994Sub]
closely related to hP6 - CaCu5
* 1, Gd(CuxAl1-x)12
GdCu6Al6
tI26
I4/mmm
ThMn12 a = 874.8
c = 514.6
a = 875.6
c = 514.5
a = 869.1
c = 506.2
0.33 x 0.5
0.39 x 0.41 at 600°C [2001Gum]
at x = 0.33, as cast samples [1976Bus]
at x = 0.39 [2001Gum]
observed on a sample at x = 0.5 annealed at
~800°C [1980Fel]
* 2, GdCu7.8Al3.2 tI48
I41/amd
BaCd11
a = 1026.9
c = 660.54
[2001Gum]
* 3, GdCu6.6Al4.4 oF*
Fddd
Tb(Cu0.58Al0.42)11
a = 1430.3
b = 1496.2
c = 657.4
[2001Gum]
* 4, Gd2(CuxAl1-x)17
Gd2Cu9.4Al7.6
hR57
R3m
Th2Zn17 a = 883.0
c = 1283
a = 884.5
c = 1290.1
a = 896.8
c = 1298.4
a = 883.0
c = 1285.7
0.394 x 0.47 at 500°C [1988Pre]
0.394 x 0.55 at 600°C [2001Gum]
x = 0.47 [1988Pre]
x = 0.41 [1982Pre]
x = 0.394 [1988Pre]
x = 0.55 [2001Gum]
*, Gd2Cu6Al11 hP38
P63/mmc
Th2Ni17
a = 892.3
c = 901.6
[1978Pop] not shown in the isothermal
section
* 5, Gd3Cu2.1Al8.9
GdCuAl3
oI12
Immm
La3Al11 or
tI10
I4/mmm
BaAl4
a = 423.98
b = 1255.3
c = 993.93
a = 415.91
c = 1063.6
[2001Gum]
[1988Pre]
* 6, GdCu0.9Al2.1 hR36
R3m
PuNi3
a = 551.53
c = 2551.9
[2001Gum]
* 7, GdCuAl hP9
P62m
Fe2P or ZrNiAl
a = 707.77
c = 406.49
a = 705.1
c = 406.0
[1968Dwi]
[2001Gum]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
46
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Gd
20
40
60
80
20 40 60 80
20
40
60
80
Gd Cu
Al Data / Grid: at.%
Axes: at.%
γ1
δ
ζ2
η2
θ
GdAl3
GdAl2
GdAl
Gd3Al2
Gd2Al
GdCu GdCu2 GdCu4GdCu5 GdCu6
Gd3Al
τ1
τ4
τ3
τ7
(Cu)
τ2
(Al)
τ5
τ6
(αGd)
20
40
60
80
20 40 60 80
20
40
60
80
Gd Cu
Al Data / Grid: at.%
Axes: at.%
γ2
δ
ε2
η1
(Al)
GdAl3
GdAl2
GdCu2 GdCu5GdCu6
β
τ1
τ4
τ7
τ5
τ6
τ3
τ2
Gd2Cu9
(Cu)
L
Fig. 1: Al-Cu-Gd.
Isothermal section at
500°C
Fig. 2: Al-Cu-Gd.
Isothermal section at
600°C
47
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Aluminium – Copper – Magnesium
Günter Effenberg, Alan Prince†, updated by Nathalie Lebrun, Hans Leo Lukas, Mireille G. Harmelin
Literature Data
This system was previously evaluated by [1991Eff]. Their evaluation has been used by two groups as the
basis for thermodynamic assessments and phase diagram calculations [1993Zuo, 1996Zuo, 1997Che] and
[1998Buh, 2003Jan]. Some experiments have been performed to support these calculations [1995Hua,
1995Kim, 1995Soa, 1998Fau] and [1999Fau]. The equilibria in the Al-Cu-Mg system are complicated by
the existence of four ternary phases. There is need for experiments to clarify the ternary equilibria involving
the three Laves phases, 1-3, which have clearly been identified as three separate phases. The 1 phase with
a Cu2Mg type structure is a solution phase of the binary Cu2Mg compound with replacement of the Cu
atoms by Al along the 33.3 at.% Mg section. At a composition close to the Cu3Mg2Al formula, the 1 phase
melts congruently at ~910°C. Further replacement of Cu by Al stabilizes the 2 phase with a MgNi2 type
structure and then the 3 phase with a MgZn2 type structure. A variety of polytype structures with different
atom layer stacking sequences have been observed between the MgNi2 and MgZn2 type phases. The 2-3
phases appear to be formed by peritectic reaction and each Laves phase is associated with a region in which
it forms as the primary phase on solidification of melts. Four additional ternary compounds have also been
studied extensively. The S phase is based on the CuMgAl2 composition, V on Cu6Mg2Al5 and Q on
Cu3Mg6Al7. These three phases exist over very limited homogeneity ranges. The T phase has a broad range
of homogeneity. A formula (Cu1-xAlx)49Mg32 is derived from the crystal structure [1952Ber], but also some
mutual replacement between Mg and Cu+Al takes place.
The liquidus projection, presented by [1952Ura], does not include the monovariant curves associated with
the L + 1 2 and L + 2 3 peritectic reactions. The Laves phase 1 is the predominant primary phase,
but also the regions for primary solidification of (Al) and (Mg) are relatively large. Six pseudobinary
reactions have been identified experimentally, and the pseudobinary reaction e3 (Table 2b) has been
suggested. The invariant reactions associated with the primary (Al) phase region are well characterized by
numerous workers. The invariant reactions associated with the primary V, Q and T phase regions have been
elucidated by Russian workers, summarized by [1952Ura]. The liquidus surface across the Mg2Al3, T and
Mg17Al12 phase regions is exceptionally flat and ranges in temperature from 420 to 475°C. [1952Ura] gave
a complete reaction scheme. The thermodynamic calculations referred to above in principle reproduce this
reaction scheme, but differ in some details.
Binary Systems
Assessments of the Al-Cu system by [2003Gro], of the Al-Mg system by [2003Luk] and of the Cu-Mg
system by [2002Iva] are accepted. They are based on [1994Mur, 1998Liu] for Al-Cu, [1982Mur, 1998Lia1]
for Al-Mg and [1994Nay] for Cu-Mg. The thermodynamic data set of the COST 507 action [1998Ans,
1998Buh] was updated recently in some details [2003Jan]. It was used for the calculated figures and the
reaction scheme presented in this assessment. The homogeneity ranges of the phases Mg2Al3, and were
simplified to stoichiometric phases. 1 and 2 were treated as a single phase, . 1 and 2 were also not
distinguished and called .
Solid Phases
There are four well-defined ternary phases, designated in the literature as Q, S, T and V phases. It is quite
interesting to note that all ternary compounds in the Al-Cu-Mg system are formed at maxima of three-phase
equilibria involving the liquid phase, except the V phase, which is formed in a four-phase peritectic reaction
(P1). In addition the section at 33.3 at.% Mg contains a complex series of ternary Laves-Friauf phases that
are designated as 1, 2, 3, 5L, 6L, 9L and 16L in this assessment, Table 1. The Q phase is based on the
chemical formula Cu3Mg6Al7 [1947Str, 1951Mir1] and has a very limited homogeneity range. The S phase
48
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
has been extensively studied [1936Lav1, 1937Nis1, 1938Pet1, 1938Pet2, 1940Kuz, 1941Obi, 1943Per,
1944Lit, 1946Pet, 1946Ura, 1947Str, 1949Mir]. It also has a limited homogeneity range, based on the
chemical formula CuMgAl2. Its structure was determined by [1943Per] and confirmed by [1949Mir]. The
T phase has been equally thoroughly investigated [1919Vog, 1923Gay, 1935Lav, 1937Nis1, 1940Kuz,
1943Gue, 1944Lit, 1946Pet, 1946Ura, 1948Str, 1949Ura1, 1949Ura2, 1950Phr, 1952Ber, 1966Aul,
2000Tak] and a variety of chemical formulae assigned to it. From the crystal structure determined by
[1952Ber], the formula (Cu1-x Alx)49Mg32 is adequate. It is found that very few Al atoms occupy site A,
which is the center of an isochahedral cluster being almost empty [2000Tak]. The V phase has a small
region of homogeneity centered on the Cu6Mg2Al5 formula [1936Lav1, 1936Lav2, 1937Sch, 1943Gue,
1947Str, 1948Str, 1949Sam, 1949Ura1, 1951Mir3, 1952Ura] although other chemical formulae have been
quoted in the literature. Its structure was determined by [1949Sam] with the ideal formula Cu6Mg2Al5. New
recent results using DSC and EDS/WDX techniques [2001Fau] confirmed small solubility ranges of the Q
and S phases. Moreover, the solubility domain of the V phase seems to be parallel to the Al-Cu binary edge
[2001Fau]. Addittional experiments are needed to confirm it.
The Laves-Friauf phases, although well studied, have not been integrated experimentally into the ternary
equilibria in a satisfactory manner. The 1 phase with a Cu2Mg type structure is based on the Cu2Mg binary
compound with a substitution of Al atoms for Cu to form a solid solution series. At a composition close to
Cu3Mg2Al, the 1 phase melts congruently [1936Lav1, 1952Ura]. With further replacement of Cu by Al on
the 33.3 at.% Mg section, an MgNi2 type phase is stable, 2. There is general agreement between [1953Kle,
1965Sli, 1977Kom, 1981Mel1] and [1981Mel2] on the extent of the 2 phase region. Earlier work did not
detect 2 [1934Lav, 1943Gue, 1949Ura1] or regarded it as stable at high temperature only [1936Lav1]. The
MgZn2 type structure, 3, is formed with further substitution of Cu atoms by Al. The results from the
different workers are summarized in Fig. 1. Polytype structure Laves phases with variations in the layer
stacking sequences have been studied by [1962Kom, 1977Kit, 1977Kom] and [1981Mel1]. They are
located between 1 and 2, but their ranges of stability could not exactly be separated from those of 1 and
2. [1998Che] proposed a “new intermetallic compound Mg1.75Cu1.0Al0.4” at a composition, where
[1991Eff, 2000Fau] and the calculations [1997Che, 1998Buh, 2003Jan] assume two phases, 1 and (Mg).
The characteristics of this “new phase”, however, clearly identify it as the 1 phase [2000Fau]. The presence
of (Mg) and 1 phases were confirmed by [2000Fau] who made XRD experiments on alloys having the
same composition as those reported by [1998Che]. Most probably the also present (Mg) phase was not
detected in the X-ray patterns of [1998Che] due to line broadening by cold deformation.
Pseudobinary Systems
A number of pseudobinary systems have been reported. The calculation [2003Jan] found 13 maxima of
three-phase equilibria, but some of them are less than 1 K above an adjacent four-phase equilibrium and
must be taken as tentative only. The (Mg)- 1 section is a pseudobinary eutectic [1932Por, 1933Bas,
1934Por, 1949Ura2], e13, Table 2. The (Al)-S section contains a pseudobinary eutectic e14 [1937Nis1,
1946Ura, 1948Bro, 1952Han]. The calculated temperatures [2003Jan] of both equilibria are far below those
given by [1946Ura] and accepted by [1991Eff]. The sections Mg2Al3-T, e19, and Mg17Al12-T, e16, are also
pseudobinary eutectic sections at Cu contents below the beginning of the primary Q phase region.
[1943Gue, 1949Ura1, 1949Ura2, 1951Mir2] and [2003Jan] are in agreement on the nature of these two
sections, Table 2. The investigation [1951Mir2] of the region of primary solidification of Q led to the
conclusion that the T phase is formed by peritectic reaction with Q at p13, Fig. 2. A pseudobinary reaction
was indicated by [1946Ura] who found a maximum on the curve U8U11 corresponding with the peritectic
formation of S by reaction of liquid with a Laves phase. [1949Ura1, 1949Ura2] and [1952Ura] refer to the
cubic Cu2Mg type phase 1 or to a composition CuMgAl. They take no account of the 2 and 3 Laves
phases. The calculation of [2003Jan] gives 2 as the Laves phase participating in this reaction, p10, which
is also favoured by [1991Eff]. [1938Pet1] regarded the CuAl2-S section as a pseudobinary, but later work
has disproved this assumption.
49
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Invariant Equilibria
Table 2 lists the invariant reactions following from the thermodynamic calculation of [2003Jan] for the
Al-Cu-Mg ternary system and may be read in conjunction with Fig. 2. The reaction scheme, following from
this calculation is given in Fig. 3. In this calculation, 1 and 2 as well as 1 and 2 were considered as single
phases and called and , respectively. The ternary eutectic reaction E5 has been widely studied, Table 3.
The flat nature of the liquidus surface near to E7 has led to a considerable scatter in quoted compositions
and temperatures, Table 4. The reaction has normally been quoted as a ternary eutectic reaction and this is
accepted. The transition reaction U16 has also been widely studied, Table 5. The work of [1946Ura,
1949Ura2] and [1948Bro] rests on an examination of a greater number of alloys than other work and
allowed a more precise determination of the liquid composition at U16. Ternary eutectic reactions in
Mg-rich alloys occur at E6 and E9. The reaction temperature at E6 is 1°C [1932Por, 1933Bas, 1934Por] or
2°C [1949Ura2] below the binary Cu-Mg eutectic temperature. The ternary eutectic E9, Table 6, was
initially regarded as involving a Laves phase, but the work of [1951Mir2] indicates that this eutectic
involves the Q phase, which was not detected by the previous workers. Faudot et al. [1998Fau, 1999Fau]
confirmed the eutectic, Table 6. The ternary eutectic reaction at E9 was found by [1949Ura2] at 423°C, what
agrees well with that calculated by [2003Jan], 424°C. The reaction at U13 was regarded as a transition
reaction by [1937Nis1, 1952Han], as calculated by [2003Jan], whereas [1946Ura] and [1949Ura2]
considered it to be a ternary peritectic reaction, L+ 1+S T. [1951Mir2] gives it as L+ 1+S Q. There is
doubt about this reaction on two counts. The Q phase lies virtually on the L- 1 tie line [1952Ura] and it is
unlikely that the Laves phase is 1. For the reactions U15 and U18 [2003Jan] reproduced those given by
[1951Mir2] with 3°C deviation. For U18 Faudot et al. [1998Fau] gave 427°C as calculated by [1998Buh,
2003Jan]. But later [1999Fau] found it at 451°C with a more Al-rich liquid, Table 6. The transition reaction
at U17 was given by [1951Mir2] as L+ 1 (Mg)+Q, but the work of [1981Mel2] indicates 3 as the reactant
rather than 1, whereas [1998Fau, 1999Fau, 2003Jan] assume 2. The reactions in the Cu-rich corner have
been little studied. In Table 2 are given those calculated by [2003Jan]. [1949Ura2] assumed an eutectic
instead of U2 and a transition reaction instead of E4. The temperatures of the invariant equilibrium in this
area calculated by the two groups [1997Che] and [1998Buh, 2003Jan] deviate up to 20°C. The regions of
primary solidification of the Laves phases 1, 2 and 3 have not been experimentally defined, but the
calculation [2003Jan] gives them as shown in Fig. 2. [1997Che] did not distinguish these Laves phases.
Liquidus Surface
A liquidus projection, Fig. 2b, is taken from the calculation of [2003Jan] with some minor modifications on
the edges according to the binary systems accepted in this assessment. It should be compared with the
projection, Figs. 2 and 2a, deduced also from the calculations of [2003Jan]. The liquidus in the ternary
diagram was also calculated by [2001Che, 2002Che] using the multicomponent phase diagram calculation
software PANDAT. [1999Xie] also studied the liquidus projection in the Al rich corner. Results are in
agreemnt with those calculated by [2003Jan]. According to the liquidus of the binary systems accepted in
this assessment, the liquidus projection was modified at the edge boundaries. The liquidus isotherms
reproduce fairly well those assessed by [1991Eff]. The primary (Al) region has been widely studied with
general agreement on the form of the liquidus. The isotherms for the region of primary solidification of the
series of Cu-rich Al-Cu phases are uncertain.
Isothermal Sections
The calculated 400°C isothermal section calculated by [2003Jan], Fig. 4, agrees with Fig. 4 of [1991Eff]
except the broadening of the homogeneity range of 1 near 25 at.% Al, which in calculation needs to model
an anomaly in the Gibbs energy description at that composition, but there is no other evidence for an
anomaly. The phase Mg2Al3 is simplified as a stoichiometric phase as well as the CuMg2, , and phases.
The solubility of Cu and Mg in Al-rich alloys at 460°C was determined by [1944Lit] and [1947Str], Fig. 5.
[1944Lit] also produced data for 375°C. The results of [1932Dix] agree with the solubilities given in Fig. 5.
[1946Pet] found lower Mg solubilities but used fewer alloys. [1955Zam] published solubility curves with a
50
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
series of cusps that cannot be reconciled with the alloy constitution. The solubilities of Mg and Cu in (Al)
reported in the accepted binary systems have also been taken into account in Fig. 5. The calculated solvus
isotherms of [1986Cha] and [2003Jan], Fig. 6, are in good agreement with [1944Lit] and [1947Str].
[1957Rog] reported the solubility of Al and Mg in (Cu), Fig. 7. No comparable work has appeared. In this
area the calculation is less reliable, as it cannot be based on adjacent experimental data. More extensive
isothermal sections were determined by [1946Pet] at 400°C in the region from Al to S and T. [1949Mir]
reported on the S phase region at 420°C, [1949Ura1] on the T and 1 phase region at 400°C, [1951Mir1]
on the Q phase region at 400°C, [1952Ura] on an almost complete isothermal section at 400°C and
[1981Mel2] on the region from 33.3 to 100 at.% Mg at 400°C. [1944Lit] and [1947Str] studied the 460°C
isothermal section from Al to the , S, Q and T phases.
Temperature – Composition Sections
The liquidus and solidus of the Al rich alloys along the isopleth Al-Cu0.5Mg0.5 were calculated by
[1997Che, 1999Xie, 2000Lia] using thermodynamic descriptions. The measured solidus data found by
[1988Mur] was found to be 0.5 at.% higher than the model-calculated values, while the measured liquidus
is in good agreement with the model-calculation. The inaccuracy for the solidus is explained by
microsegregations occuring in ternary Al-Cu-Mg alloys [1999Xie].
Several isopleths were calculated by [1997Che, 2003Jan] from thermodynamic descriptions. Figs. 8 and 9a,
9b, 9c show isopleth sections at 33.3 at.% Mg and x mass% Al (x =60, 70 and 95.5) respectively. The
calculated isopleth, taken from [2003Jan] and reported on Fig. 8, is in agreement with the experimental data
reported by [1936Lav1] and [1953Kle]. The calculated isopleths reported on Figs. 9a, 9b and 9c are taken
from [1998Buh] and describe quite well the experimental information reported by [1937Nis1, 1937Nis2,
1952Han] and [1946Ura]. The calculated isopleths at 37 at.% Al (Fig. 10a) and 43.75 at.% Al (Fig. 10b)
show the 2 and the Q phases formations respectively [2003Jan].
Thermodynamics
[1972Pre] studied the enthalpy of formation of alloys on the 33.3 at.% Mg section. Substitution of Cu by Al
increases the stability of the 1 phase although there is a decrease of stability at a valency electron
concentration of 1.5 (76.9Cu, 17.3Mg). [1987Hoc] calculated the enthalpy of a ternary alloy containing
33.3% “MgAl2”; agreement with [1972Pre] is fair. [1985Kuz] applied a thermodynamic model to predict
the ternary solidus from the ternary liquidus and the binary solidus-liquidus for Al-rich alloys. [1973Dav]
used quasi-chemical regular solution theory to calculate the monovariant curve e2E5 of Fig. 2a. With the
introduction of a ternary interaction parameter the calculated ternary eutectic point E5, Table 3, shows
reasonable agreement with the assessed composition. [1987Lac] calculated the Al-rich region of the phase
diagram using an extended Redlich-Kister formalism. Excellent agreement was obtained with the assessed
liquidus, Fig. 2b. [1985Far] calculated the composition of the ternary eutectic E5, Fig. 2a and Table 2,
assuming both ideal solution behaviour and regular solution behaviour. The calculated eutectic
compositions, 34.4Cu-8.8Mg (mass%) for ideal solutions and 30.3Cu-7.5Mg (mass%) for regular solutions,
approximate to the assessed values. The calculated eutectic temperatures are surprisingly low at 273°C and
271°C, respectively. Recently two groups [1997Che] and [1998Buh, 2003Jan] calculated the whole ternary
system, describing the Gibbs energies of all phases involved by the compound energy formalism. Both
calculations show very similar results, only in the Cu-rich part there is some disagreement of the invariant
temperatures (up to 20°C). The first group also calculated solidification paths using the model of Scheil
[1993Zuo, 1996Zuo].
[1986Che] measured the enthalpy of fusion of the ternary eutectic E5 as 365 J g-1 corresponding to 11.8
kJ mol-1 of atoms. [1986Not] measured the enthalpy of formation of the S phase as -63.2 ± 4.0 kJ mol-1 of
CuMgAl2. [1995Kim] measured the enthalpy of mixing of ternary liquids by a high temperature calorimeter
at 713°C along three lines with constant Al/Mg ratios up to 40 at.% Cu and along Al/Cu = 13/7 up to 27
at.% Mg. [1995Soa] measured the chemical potential of Mg in ternary melts by an isopiestic method.
51
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Notes on Materials Properties and Applications
The mechanical properties such as tensile strengh were investigated by [2002Dav] on
0.02Zn-0.05Ti-0.42Mn-0.27Fe-4.5Cu-1.5Mg-Al-0.17Si alloys.
[2002Zhu] reported that a small addition of Ag (< 0.1 at.%) to an Al-Cu-Mg alloy with a high content of Al
promote an increasing strength and creep resistance when compared to Al-Cu-Mg alloys that contain only
the CuAl2 precipitate.
Miscellaneous
[1940Kuz] and [1946Kuz] measured lattice spacings of the (Al) phase along sections from Al with various
Cu:Mg ratios. [1951Poo] measured the lattice spacings of the (Al) phase along sections from 99 at.% Al, 1
at.% Mg to 99.5 at.% Al, 0.5 at.% Cu and from 98 at.% Al, 2 at.% Mg to 99 at.% Al, 1 at.% Cu, Table 7.
A small addition of Mg to Al-Cu alloys accelerates the formation of Guinier-Preston (GP) zones through
the Mg/Cu/vacancy complexes mechanism [2000Hir, 2002Hir].
The crystal structure of a metastable variant of S on aging Al alloys was studied by [1950Bag]. Aging
studies of single crystals of an alloy containing 1.2 at.% Cu, 1.2 at.% Mg [1978Ale] showed S particles to
be coherent with the Al matrix. The effect of aging on mechanical properties of Al-rich alloys have been
reported by [1939Han, 1941Mec] and [1948Sha]. More recent studies on metastable precipitates in (Al) are
from [1990Gar] and [1991Jin].
[1959Pal] prepared thin film Al-rich ternary alloys by evaporation on to Al substrates. The constitution is
claimed to correspond with bulk samples. There is a growing literature on the formation of a
non-equilibrium icosahedral quasicrystalline phase by rapid solidification of alloys in the T phase region.
[1986Cas] tentatively outlined the phase region that produces quasicrystals on rapid solidification as
containing 10 to 13.5 at.% Cu, 35 to 37 at.% Mg. This composition range is on the low Mg side of the
equilibrium T phase region. Annealing a rapidly solidified alloy with 1 at.% Cu, 5 at.% Mg for 100 h at
190°C gave both the icosahedral phase and the equilibrium T phase at the grain boundaries of the Al matrix.
For anneals of 24 h at 250°C only the T phase was observed at the grain boundary [1986Cas, 1987Cas] with
precipitation of the S phase in the Al matrix. [1987San1] and [1987San2] rapidly solidified an alloy
corresponding to CuMg4Al6. This composition lies in the T phase region. DSC measurements gave a
melting point of 474.9°C which is in good agreement with the assessed temperature of the pseudobinary
reaction p6, L+Q T, Fig. 3. A polymorphic transformation of the T phase, reported at 356.5°C, has not been
noted by other workers. [1988She] rapidly solidified an alloy containing 12.5Cu-36.5Mg-51Al (at.%) and
found it to be a single phase icosahedral quasicrystal. This composition is within the phase region given by
[1986Cas]. A wider, but less exact, delineation of the icosahedral quasicrystal phase region was given by
[1988Shi]. They quote the composition as typically CuMg4Al5, as proposed by [1937Nis1] for the stable T
phase. [1988San] rapidly solidified the composition CuMg4Al6 and carried out a detailed X-ray study of the
quasicrystalline phase and its transformation to the crystalline T phase by annealing for 1 h at 340°C.
[1989She] used high resolution X-ray diffraction to study atomic distribution in quasicrystalline phases as
well as differential scanning calorimetry (DSC) to get thermodynamic properties. [1991Wit] prepared and
studied an icosahedral alloy with composition Cu12.5Mg36.5Al51 by electrical resistivity measurements and
DSC.
References
[1919Vog] Vogel, R., “Ternary Alloys of Al with Mg and Cu” (in German), Z. Anorg. Chem., 107,
265-307 (1919) (Equi. Diagram, Experimental, 10)
[1923Gay] Gayler, M.L.V., “The Constitution and Age-Hardening of the Ternary Alloys of Al with Mg
and Cu”, J. Inst. Met., 29, 507-528 (1923) (Equi. Diagram, Experimental, 8)
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1932Dix] Dix, E.H., Sager, G.F., Sager, B.P., “Equilibrium Relations in Al-Cu-Mg and Al-Cu-Mg2Si
of High Purity”, Trans. AIME, 99, 119-131 (1932) (Equi. Diagram, Experimental, 8)
52
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
[1932Por] Portevin, A., Bastien, P., “Contribution to the Study of the Mg-Al-Cu Ternary System” (in
French), Compt. Rend., 195, 441-443 (1932) (Equi. Diagram, Experimental, 6)
[1933Bas] Bastien, P., “Study of the Ultra-Light Alloys of Mg-Al-Cu” (in French), Rev. Met., 6,
478-501 (1933) (Equi. Diagram, Experimental, 22)
[1934Lav] Laves, F., Löhberg, K., “The Crystal Structure of Intermetallic Compounds with the
Formula AB2” (in German), Nachr. Ges. Wiss. Goettingen, 1, 59-66 (1934) (Crys.
Structure, Experimental, 11)
[1934Por] Portevin, A., Bastien, P., “Constitution and Properties of Alloys of Mg with Al and Cu” (in
French), Chim. et Ind. Paris, Special No. (April), 490-519 (1934) (Equi. Diagram,
Experimental, 24)
[1935Lav] Laves, F., Löhberg, K., Witte, H., “The Isomorphism of the Ternary Compounds
Mg3Zn2Al2 and Mg4CuAl6” (in German), Metallwirtschaft, 14, 793-794 (1935) (Crys.
Structure, Experimental, 5)
[1936Lav1] Laves, F., Witte, H., “Investigations in the Mg-Cu-Al System, Especially on the
MgCu2-MgAl2 Section” (in German), Metallwirtschaft, 15, 15-22 (1936) (Crys. Structure,
Equi. Diagram, Experimental, 6)
[1936Lav2] Laves, F., Werner, S., “The Crystal Structure of Mg2Zn11 and its Isomorphy with
Mg3Cu7Al10” (in German), Z. Kristallogr., 95, 114-128 (1936) (Crys. Structure, Equi.
Diagram, Experimental, 11)
[1937Nis1] Nishimura, H., “The Al Corner of the Al-Cu-Mg System” (in Japanese), Nippon Kinzoku
Gakkai-Shi, 1, 8-18 (1937) (Equi. Diagram, Experimental, 8)
[1937Nis2] Nishimura, H., “Investigation of the Al-rich Al-Cu-Mg Alloy System”, Mem. Coll. Eng.
Kyoto Imp. Univ., 10, 18-33 (1937 (Experimental, Equi. Diagram, 7)
[1937Sch] Schütz, W., “The Ternary Compound Mg4Cu11Al11” (in German), Metallwirtschaft, 16,
949-950 (1937) (Equi. Diagram, Experimental, 3)
[1938Pet1] Petrov, D.A., “On the Importance of the Ternary Phase in the Aging of Al-Cu-Mg Alloys”
(in Russian), Metallurgia, 3, 88-91 (1938) (Experimental, 4)
[1938Pet2] Petrov, D.A., “On the Problem of the Age-Hardening of Duralumin”, J. Inst. Met., 62,
81-100 (1938) (Experimental, 31)
[1939Han] Hansen, M., Dreyer, K.L., “The Influence of the Cu and Mg Contents on the Age-Hardening
of Al-Cu-Mg Alloys” (in German), Z. Metallkd., 31, 204-209 (1939) (Experimental, 6)
[1940Han] Hanemann, H., “A Note on the System Al-Cu-Mg” (in German), Z. Metallkd., 32, 114
(1940) (Equi. Diagram, Experimental, 1)
[1940Kuz] Kuznetsov, V.G., Guseva, L.N., “X-Ray Investigation of Al-rich Al-Mg-Cu Alloys” (in
Russian), Izv. Akad. Nauk SSSR, Ser. Khim., 6, 905-928 (1940) (Crys. Structure, Equi.
Diagram, Experimental, 17)
[1941Mec] Mechel, R., “Contribution to the Metallography of Precipitated CuAl2 Phase in Commercial
Al-Cu-Mg Alloys” (in German), Luftfahrtforschung, 18, 107-110 (1941) (Experimental, 7)
[1941Obi] Obinata, I., Mutuzaki, K., “On the Composition and Crystal Structure of the “S” Compound,
the Main Hardening Element of Duralumin” (in Japanese), Nippon Kinzoku Gakkai-Shi, 5,
121-123 (1941) (Crys. Structure, Experimental, 6)
[1943Gue] Guertler, W., Rassmann, G., “The Application of the X-Ray Fine Structure Diagram for the
Recognition of the Phase Equilibria of Ternary Systems in the Crystalline State” (in
German), Metallwirtschaft, 22, 34-42 (1943) (Crys. Structure, Equi. Diagram,
Experimental, 30)
[1943Per] Perlitz, H., Westgren, A., “The Crystal Structure of Al2CuMg”, Arkiv Kemi, Mineral. Geol.,
B16, 13, 1-5 (1943) (Crys. Structure, Experimental, 4)
[1944Lit] Little, A.T., Hume-Rothery, W., Raynor, G.V., “The Constitution of Al-Cu-Mg Alloys at
460°C”, J. Inst. Met., 70, 491-506 (1944) (Equi. Diagram, Experimental, 7)
[1946Kuz] Kuznetsov, V.G., “X-Ray Investigation of Al-Base Ternary Alloys” (in Russian), Izv. Sekt.
Fiz.-Khim. Anal., 16, 232-250 (1946) (Equi. Diagram, Crys. Structure, Experimental, 29)
53
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
[1946Pet] Petrov, D.A., Berg, G.S., “Investigation of the Region of Solid Solution of Cu and Mg in
Al” (in Russian), Zh. Fiz. Khim., 20, 1475-1488 (1946) (Crys. Structure, Equi. Diagram,
Experimental, 21)
[1946Ura] Urazov, G.G., Petrov, D.A., “Investigation of the Al-Cu-Mg Phase Diagram” (in Russian),
Zh. Fiz. Khim., 20, 387-398 (1946) (Equi. Diagram, Experimental, 10)
[1947Str] Strawbridge, D.J., Hume-Rothery, W., Little, A.T., “The Constitution of Al-Cu-Mg-Zn
Alloys at 460C”, J. Inst. Met., 74, 191-225 (1947-48) (Crys. Structure, Equi. Diagram,
Experimental, 11)
[1948Bro] Brommelle, N.S., Phillips, H.W.L., “The Constitution of Al-Cu-Mg Alloys”, J. Inst. Met.,
75, 529-558 (1948-49) (Equi. Diagram, Experimental, 39)
[1948Sha] Sharma, A.S., “The Metallography of Commercial Alloys of the Duralumin Type”, Trans.
Indian Inst. Met., 1, 11-44 (1948) (Experimental, 11)
[1948Str] Strawbridge, D.J., “Correspondence on the Paper by N.S. Brommelle and H.W.L. Phillips,
The Constitution of Al-Cu-Mg Alloys”, J. Inst. Met., 75, 1116-1119 (1948-49) (Review, 4)
[1949Mir] Mirgalovskaya, M.S., Makarov, E.S., “The Crystal Structure and Properties of the S Phase
in the Al-Cu-Mg System” (in Russian), Izv. Sekt. Fiz.-Khim. Anal., 18, 117-127 (1949)
(Crys. Structure, Equi. Diagram, Experimental, 16)
[1949Sam] Samson, S., “The Crystal Structure of Mg2Cu6Al5” (in German), Acta Chem. Scand., 3,
809-834 (1949) (Crys. Structure, Experimental, 11)
[1949Ura1] Urazov, G.G., Mirgalovskaya, M.S., “Ternary Intermetallic Phases in the Al-Cu-Mg
System” (in Russian), Izv. Sekt. Fiz.-Khim. Anal., 19, 514-521 (1949) (Crys. Structure, Equi.
Diagram, Experimental, 20)
[1949Ura2] Urazov, G.G., Mirgalovskaya, M.S., Nagorskaya, N.D., “Phase Diagram of the Al-Mg-Cu
System” (in Russian), Izv. Sekt. Fiz.-Khim. Anal., 19, 522-530 (1949) (Equi. Diagram,
Experimental, 19)
[1950Bag] Bagaryatsky, Yu.A., “Structural Changes on Aging Al-Cu-Mg Alloys” (in Russian),
Zh. Tekhn. Fiz., 20, 424-427 (1950) (Crys. Structure, Experimental, 7)
[1950Phr] Phragmen, G., “On the Phases Occurring in Alloys of Al with Cu, Mg, Mn, Fe and Si”,
J. Inst. Met., 77, 489-552 (1950) (Crys. Structure, Equi. Diagram, Experimental, 67)
[1951Mir1] Mirgalovskaya, M.S., “The Q Phase in the Al-Cu-Mg System” (in Russian), Dokl. Akad.
Nauk SSSR, 77, 289-292 (1951) (Crys. Structure, Equi. Diagram, Experimental, 7)
[1951Mir2] Mirgalovskaya, M.S., “The Region of Primary Solidification of the Q Phase in the
Al-Cu-Mg System” (in Russian), Dokl. Akad Nauk SSSR, 77, 1027-1030 (1951) (Equi.
Diagram, Experimental, 5)
[1951Mir3] Mirgalovskaya, M.S., “On Similar Crystallochemical Characteristics in the Mg-Zn and
Mg-Al-Cu Systems” (in Russian), Dokl. Akad. Nauk SSSR, 78, 909-911 (1951) (Crys.
Structure, Experimental, Theory, 7)
[1951Poo] Poote, O.M., Axon, H.J., “Lattice-Spacing Relationships in Al-rich Solid Solutions of the
Al-Mg and Al-Mg-Cu Systems”, J. Inst. Met., 80, 599-604 (1951) (Crys. Structure,
Experimental, 11)
[1952Ber] Bergman, G., Waugh, J.L.T., Pauling, L., “Crystal Structure of the Intermetallic Compound
Mg32(Al,Zn)49 and Related Phases”, Nature, 169, 1057-1058 (1952) (Crys. Structure,
Experimental, 4)
[1952Han] Hanemann, H., Schrader, A., “Ternary Alloys of Al”, in “Atlas Metallographicus”, (in
German), Verlag Stahleisen M.R.H. Dsseldorf, 3(2), 73-81 (1952) (Equi. Diagram,
Experimental, Review, 9)
[1952Ura] Urazov, G.G., Mirgalovskaya, M.S., “The Al-Cu-Mg System” (in Russian), Dokl. Akad.
Nauk SSSR, 83, 247-250 (1952) (Equi. Diagram, Experimental, 8)
[1953Kle] Klee, H., Witte, H., “Magnetic Susceptibilities of Ternary Mg Alloys and their Significance
from the Standpoint of the Electron Theory of Metals” (in German), Z. Phys. Chem.
(Leipzig), 202, 352-378 (1953) (Experimental, 32)
54
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
[1955Zam] Zamotorin, M.I., “Solubility of Cu and Mg in the Solid State in Al at Various Temperatures”
(in Russian), Tr. Leningrad. Polytekhn. Inst., 180, 32-37 (1955) (Equi. Diagram,
Experimental, 12)
[1957Rog] Rogel'berg, I.L., “Solubility of Mg in Cu and Combined Solubility of Mg and Al in Cu” (in
Russian), Tr. Gosud. N.-I. Pr. Inst. Obrab. Tsvetn. Met., 16, 82-89 (1957) (Equi. Diagram,
Experimental, 12)
[1959Pal] Palatnik, L.S., Fedorov, G.V., Gladkikh, N.T., “Study of Al Alloys of the Al-Cu-Mg System
in Samples of Variable Compositions” (in Russian), Fiz. Met. Metalloved., 8, 378-386
(1959) (Experimental, 14)
[1962Kom] Komura, Y., “Stacking Faults and Two New Modifications of the Laves phase in the
Mg-Cu-Al System”, Acta Crystallogr., 15, 770-778 (1962) (Crys. Structure, Experimental,
15)
[1965Sam] Samson, S., “The Crystal Structure of the Phase Mg2Al3”, Acta Crystallogr. 19, 401-413
(1965) (Experimental, Crys. Structure, 16)
[1965Sli] Slick, P.I., Massena, C.W., Craig, R.S., “Electronic Specific Heats of Alloys of the
MgCu2-xAlx System”, J. Chem. Phys., 43, 2788-2794 (1965) (Experimental, 13)
[1966Aul] Auld, J.H., Willians, B.E., “X-Ray Powder Data of T Phases Composed of Al and Mg with
Ag, Cu or Zn”, Acta Crystallogr., 21, 830-831 (1966) (Crys. Structure, Experimental, 4)
[1967Coo] Cooksey, D.J.S., A. Hellawell, A., “The Microstructures of Ternary Eutectic Alloys in the
Systems Cu-Sn-(Pb, In, Tl), Al-Cu-(Mg, Zn, Ag) and Zn-Sn-Pb”, J. Inst. Met., 95, 183-187
(1967) (Experimental, 17)
[1968Sam] Samson, S., Gordon, E.K., “The Crystal Structure of Mg23Al30”, Acta Crystallogr., B B24,
1004-1013 (1968) (Experimental, Crys. Structure, 32)
[1972Gar] Garmong, G., Rhodes, C.G., “Structure and Mechanical Properties of the Directionally
Solidified Al-Cu-Mg Eutectic”, Metall. Trans., 3, 533-544 (1972) (Experimental, 26)
[1972Pre] Predel, B., Ruge, H., “Investigation of Enthalpies of Formation in the Mg-Cu-Zn,
Mg-Cu-Al and Mg-Cu-Sn Systems as a Contribution to the Clarification of the Bonding
Relationships in Laves Phases” (in German), Mater. Sci. Eng., 9, 141-150 (1972)
(Thermodyn., Experimental, 61)
[1973Dav] Davison, J.E., Rice, D.A., “Application of Computer Generated Phase Diagrams to
Composite Synthesis”, in “In-Situ Composites. III-Physical Properties”, 33-60 (1973)
(Equi. Diagram, Thermodyn., Experimental, 10)
[1976Mon] Mondolfo, L.F., Aluminium Alloys: Structure and Properties, Butter Worths,
London-Boston, 497-505 (1976) (Equi. Diagram, Review, 70)
[1977Kit] Kitano, Y., Komura, Y., Kajiwara, H., “Electron-Microscope Observations of Friauf-Laves
Phase Mg(Cu1-xAlx)2 with x = 0.465”, Trans. Japan Inst. Met., 18, 39-45 (1977) (Crys.
Structure, Experimental, 9)
[1977Kom] Komura, Y., Kitano, Y., “Long-Period Stacking Variants and their Electron-Concentration
Dependence in the Mg-Base Friauf-Laves Phases”, Acta Crystallogr., 33B, 2496-2501
(1977) (Crys. Structure, Experimental, 16)
[1978Ale] Alekseev, A.A., Ber, L.B., Klimovich, L.G., Korohov, O.S., “The Structure of the Zones in
an Al-Cu-Mg Alloy” (in Russian), Fiz. Metall. Metalloved., 46, 548-556 (1978) (Crys.
Structure, Experimental, 17)
[1980Bir] Birchenall, B.E., Riechman, A.F., “Heat Storage in Eutectic Alloys”, Metall. Trans.A, 11A,
1415-1420 (1980) (Experimental, 13)
[1981Mel1] Mel'nik E.V., Kinzhibalo, V.V., “Compounds with Laves Phase Structures in the Systems
Mg-Al-Cu, Mg-Ga-Cu and Mg-Ga-Ni” (in Russian), Vestn. L'vov. Univ. Khim., 23, 40-43
(1981) (Crys. Structure, Experimental, 4)
[1981Mel2] Mel'nik, E.V., Kinzhibalo, V.V., “Investigation of the Mg-Al-Cu and Mg-Ga-Cu Systems
from 33.3 to 100 at.% Mg”, Russ. Metall., 3, 154-158 (1981), translated from Izv. Akad.
Nauk SSSR, Met., 3, 154-158 (1981) (Crys. Structure, Equi. Diagram, Experimental, 5)
55
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
[1982Mur] Murray, J.L., “The Al-Mg (Aluminum-Magnesium) System”, Bull. Alloy Phase Diagrams,
3, 60-74 (1982) (Equi. Diagram, Review, 132)
[1985Kuz] Kuznetsov, G.M., Konovalov, Yu.V., “Prediction of the Solidus Surface of the Al-Cu-Mg
System from Data on the Liquidus Surface” (in Russian), Izv. V.U.Z., Tsvetn. Metall., 6,
72-76 (1985) (Theory, 15)
[1985Far] Farkas, D., Birchenall, C.E., “New Eutectic Alloys and Their Heats of Transformation”,
Metall. Trans. A, 16A, 323-328 (1985) (Thermodyn., 18)
[1985Mur] Murray, J.L., “The Al-Cu System”, Int. Met. Rev., 30 (5), 211-233 (1985) (Equi. Diagram,
Review, 230)
[1986Cas] Cassada, W.A., Shen, Y., Poon, S.J., Shiflet, G.J., “Mg32(Zn,Al)49-Type Icosahedral
Quasicrystals Formed by Solid-State Reaction and Rapid Solidification”, Phys. Rev. B,
Condens. Matter, 34, 7413-7416 (1986) (Crys. Structure, Experimental, 17)
[1986Cha] Chakrabarti, D.J., “Interactive Computer Graphics of Phase Diagrams in Al-Based Systems,
Computer Modelling of Phase Diagrams”, Proc. Symp. Met. Soc. A.I.M.E., Bennett, L.H.
(Ed.), 399-416 (1985) (Equi. Diagram, Theory, 6)
[1986Che] Cherneeva, L.I., Rodionova, E.K., Martynova, N.M., “Determination of the Energy
Capacity of Metallic Alloys as Promising Heat-Storage Materials” (in Russian), Izv.
Vyss.Uchebn.Zaved. Energia, (12), 78-82 (1986) (Thermodyn., Experimental, 7)
[1986Not] Notin, M., Dirand, M., Bouaziz, D., Hertz, J., “Determination of the Partial Molar Enthalpy
at Infinite Dilution of Liquid Mg and Solid Cu in Pure Liquid Al and of the Enthalpy of
Formation of the S-Phase (Al2CuMg)” (in French), Compt. Rend. Acad. Sci., Paris, Ser. II,
302, 63-66 (1986) (Thermodyn., Experimental, 3)
[1987Cas] Cassada, W.A., Shiflet, G.J., Poon, S.J., “Quasicrystalline Grain Boundary Precipitates in
Al Alloys Through Solid-Solid Transformations”, J. Microsc., 146, 323-335 (1987) (Crys.
Structure, Experimental, 26)
[1987Hoc] Hoch, M., “Application of the Hoch-Arpshofen Model to the Thermodynamics of the
Cu-Ni-Sn, Cu-Fe-Ni, Cu-Mg-Al and Cu-Mg-Zn Systems”, Calphad, 11, 237-246 (1987)
(Thermodyn., 16)
[1987Lac] Lacaze, J., Lesoult, G., Relave, O., Ansara, I., Riquet, J.-P., “Thermodynamics and
Solidification of Al-Cu-Mg-Si Alloys”, Z. Metallkd., 78, 141-150 (1987) (Equi. Diagram,
Thermodyn., 10)
[1987San1] Sanyal, M.K., Sahni V.C., Dey, G.K., “Evidence for Endothermic Quasicrystalline -
Crystalline Phase Transitions in Al6CuMg4”, Nature, 328, 704-706 (1987) (Crys. Structure,
Experimental, 10)
[1987San2] Sanyal, M.K., Sahni, V.C., Dey, G.K., “Endothermic Quasicrystalline Phase Transition in
Al6CuMg4”, Pramna - J. Phys., 28, L709-712 (1987) (Crys. Structure, Experimental, 7)
[1988Mur] Murray, J.L., Private Communication, Alcoa Laboratory, Aluminium Co. of America,
Alcoa, PA (1988)
[1988San] Sanyal, M.K., Sahni, V.C., Chidambaram, R., “X-Ray Structural Study of Crystalline and
Quasicrystalline Al6CuMg4”, Solid State Commun., 66, 1043-1045 (1988) (Crys. Structure,
Experimental, 19)
[1988She] Shen, Y., Dmowski, W., Egami, T., Poon, S.J., Shiflet, G.J., “Structure of Al-(Li,Mg)-Cu
Icosahedral Alloys Studied by Pulsed Neutron Scattering”, Phys. Rev. B, Condens. Matter,
37, 1146-1154 (1988) (Crys. Structure, Experimental, 14)
[1988Shi] Shibuya, T., Kimura, K., Takeuchi, S., “Compositional Regions of Single Icosahedral Phase
in Ternary Nontransition Metal Systems”, Japan. J. Appl. Phys., 27, 1577-1579 (1988)
(Crys. Structure, Experimental, 14)
[1989Mee] Meetsma, A., De Boer, J.L.,Van Smaalen, S., “Refinement of the Crystal Structure of
Tetragonal Aluminum-Copper (Al2Cu)”, J. Solid State Chem., 83(2), 370-372 (1989) (Crys.
Structure, Experimental, 17)
[1989She] Shen, Y., “The Formation and Structure of Al-Cu-(Li,Mg) Icosahedral Alloys”, Thesis,
University of Virginia, (1989) (Crys. Structure, Experimental)
56
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
[1990Gar] Garg, A., Chang, Y.C., Howe, J.M., ”Precipitation of the Omega Phase in an
Al-4.0Cu-0.5Mg Alloy”, Scr. Metall. Mater., 24, 677-680 (1990) (Crys. Structure,
Experimental, 12)
[1991Eff] Effenberg, G., Prince, A., “Aluminium-Copper-Magnesium”, MSIT Ternary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 10.12587.1.20, (1991) (Crys. Structure, Equi.
Diagram, Assessment, 80)
[1991Ell] Ellner, M., Kolatschek, K., Predel, B., “On the Partial Atomic Volume and the Partial Molar
Enthalpy of Aluminium in some Phases with Cu and Cu3Au Structures”, J. Less-Common
Met., 170, 171-184 (1991) (Experimental, Crys. Structure, 57)
[1991Jin] Jin, Y., Li, C., Yan, M., “A Precipitate Phase in AA2124”, J. Mater. Sci., 26, 3244-3248
(1991) (Crys. Structure, Experimental, 6)
[1991Wit] Wittmann, R., Löbl, P., Lüscher, E., Fritsch, G., Wollgarten, M., Urban, K., “Electrical
Resistivity and Crystallization Behaviour of Icosahedral Al51Cu12.5Mg36.5”, Z. Phys. B -
Condens. Matter., 83, 193-198 (1991) (Crys. Structure, Experimental, 30)
[1993Gin] Gingl, F., Selvam, P., Yvon, K., “Structure Refinement of Mg2Cu and a Composition of the
Mg2Cu, Mg2Ni and Al2Cu Structure Types”, Acta Crystallogr., Sect. B: Struct. Crystallogr.
Crys. Chem., B49, 201-203 (1993) (Crys. Structure, Experimental, *, 15)
[1993Zuo] Zuo, Y., Chang ,Y.A., “Calculation of Phase Diagram and Solidification Paths of Al-rich
Al-Mg-Cu Ternary Alloys”, Light Met.(Warrendale Pa), 935-942 (1993) (Equi. Diagram,
Thermodyn., Assessment, 29)
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)”, in “Phase Diagrams of Binary Copper
Alloys”, Subramanian, P.R., Chakrabarti, D.J., Laughlin, D.E., (Eds.), ASM International,
Materials Park, OH, 18-42 (1994) (Equi. Diagram, Crys. Structure, Thermodyn., Review, #,
*, 226); similar to [1985Mur]
[1994Nay] Nayeb-Nashemi, A.A., Clark J.B., “Cu-Mg (Copper-Magnesium)” in “Phase Diagrams of
Binary Copper Alloys”, Subramanian, P.R., Chakrabarti, D.J., Laughlin, D.E., (Eds.), ASM
International, Materials Park, OH, 245-252 (1994) (Equi. Diagram, Crys. Structure,
Thermodyn., Review, #, 44)
[1995Hua] Huang, C., Chen, S., “Phase Equilibria of Al-rich Al-Cu-Mg Alloys”, Metall. Mater. Trans.
A, 26A, 1007-1011 (1995) (Equi. Diagram, Experimental, 18)
[1995Kim] Kim, Y.B., Sommer, F., Predel, B., “Determination of the Enthalpy of Mixing of Liquid
Aluminum-Copper-Magnesium Alloys”, Z. Metallkd., 86, 597-602 (1995) (Thermodyn.,
Experimental, 15)
[1995Soa] Soares, D., Malheiros, L.F., Hämäläinen, M., Castro, F., “Isopiestic Determination of the
Coefficients of Activity of Magnesium in Al-Cu-Mg Liquid Alloys”, J. Alloys Comp., 220,
179-181 (1995) (Thermodyn. Experimental, 3)
[1996Zuo] Zuo, Y., Chang, Y.A., “Calculation of Phase Diagram and Solidification Paths of Ternary
Alloys: Al-Mg-Cu”, Mater. Sci. Forum, 215-216, 141-148 (1996) (Equi. Diagram,
Thermodyn, Assessment, 32)
[1997Che] Chen, S., Zuo, Y., Liang, H., Chang, Y.A., “A. Thermodynamic Description for the Ternary
Al-Cu-Mg System”, Metall. Mater. Trans. A, 28A, 435-446 (1997) (Equi. Diagram,
Thermodyn., Assessment, 48)
[1998Ans] Ansara, I., Dinsdale, A.T., Rand, M.H., COST 507, Thermochemical Database for Light
Metal Alloys, Vol. 2, European Communities, Luxembourg, 311-315 (1998) (Equi.
Diagram, Thermodyn., Calculation)
[1998Buh] Buhler, T., Fries, S.G., Spencer, P.J., Lukas, H.L., “A Thermodynamic Assessment of the
Al-Cu-Mg Ternary System”, J. Phase Equilib., 19, 317-333 (1998) (Equi. Diagram,
Thermodyn., Assessment, 38)
[1998Che] Chen, Y., “A New Intermetallic Compound Mg1.75Cu1.0Al0.4”, J. Mater. Sci. Lett., 17,
1271-1272 (1998) (Crys. Structure, Experimental, 7)
57
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
[1998Don] Donnadieu, P., Harmelin, M.G., Seifert, H.J., Aldinger, F., “Commensurately Modulated
Stable States Related to the Phase in Mg-Al Alloys”, Philos. Mag. A, 78(4), 893-905
(1998) (Experimental, Crys. Structure, 21)
[1998Fau] Faudot, F., P. Ochin, M.G., Harmelin, S.G., Fries, T., Jantzen, Spencer, P.J., Liang, P.,
Seifert, H.J., “Experimental Investigation of Ternary Invariant Reactions Predicted by
Thermodynamic Calculations for the Al-Cu-Mg System”, Proceedings of the JEEP’98,
173-176, Nancy 1998 (Equi. Diagram, Experimental, 14)
[1998Lia1] Liang, P., Su, H.L., Donnadieu, P., Harmelin, M.G., Quivy, A., Effenberg, G., Seifert, H.J.,
Lukas, H.L., Aldinger, F., “Experimental Investigation and Thermodynamic Calculation of
the Central Part of the Mg-Al Phase Diagram”, Z. Metallkd., 98, 536-540 (1998) (Equi.
Diagram, Experimental, 33)
[1998Lia2] Liang, P., Tarfa, T., Robinson, J.A., Wagner, S., Ochin, P., Harmelin, M.G., Seifert, H.J.,
Lukas, H.L., Aldinger, F., “Experimental Investigation and Thermodynamic Calculation of
the Al-Mg-Zn System”, Thermochim. Acta, 314, 87-110 (1998) (Experimental, Calculation,
Thermodyn., Equi. Diagram, 69)
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264, 201-208 (1998) (Equi. Diagram,
Experimental, #, *, 25)
[1999Fau] Faudot, F., Harmelin, M.G., Fries, S.G., Jantzen, T., Liang, P., Seifert, H.J., Aldinger, F.,
“DSC Investigation of Invariant Equilibria in the Mg-Rich Side of the Al-Cu-Mg System”,
Proceedings of the JEEP’99, in press, Annecy, 1999 (Equi. Diagram, Experimental, 14)
[1999Xie] Xie, F.Y., Kraft, T., Zuo, Y., Moon, C.H., Chang, Y.A., “Microstructure and
Microsegregation in Al-rich Al-Cu-Mg Alloys”, Acta Mater., 47, 489-500 (1999)
(Experimental, Calculation, Equi. Diagram, 42)
[2000Fau] Faudot, F., Dallas, J.P., Harmelin, M.G., “Comment on the Paper a New Intermetallic
Compound Mg1.75Cu1.0Al0.4”, J. Mater. Sci. Letter., 19, 539-540 (2000) (Experiment,
Crys. Structure, 9)
[2000Hir] Hirosawa, S., Sato, T., Kamio, A., Flower, H.M., “Classification of the Role of
Microalloying Elements in Phase Decomposition of Al Based Alloys”, Acta Mater., 48,
1797-1806 (2000) (Experimental, Calculation, 35)
[2000Lia] H. Liang, T. Kraft, Y.A. Chang, “Importance of Reliable Phase Equilibria in Studying
Microsegregation in Alloys Al-Cu-Mg”, Mater. Sci. Eng. A, A292, 96-103 (2000)
(Experimental, Equi. Diagram, 31)
[2000Tak] Takeuchi, T., Mizuno, T., Banno, E., Mizutani, U., “Magic Number of Electron
Concentration in the Isocahedral Cluster of AlxMg40X60-x (X=Zn, Cu, Ag and Pd) 1/
1-Cubic Approximants”, Mater. Sci.Eng. A, 294-296, 522-526 (2000) (Experiment, Crys.
Struct., 14)
[2001Che] Chen, S.L., Daniel, S., Zhang, F., Chang, Y.A., Oates, W.A., Schmid-Fetzer, R., “On the
Calculation of Multicomponent Stable Phase Diagrams”, J. Phase Equilib., 22, 373-378
(2001) (Calculation, Equi. Diagram, 26)
[2001Fau] Faudot, F., Harmelin, M., Liang, P., Seifert, H., Private communication (2001)
[2002Che] Chen, S.L., Daniel, S., Zhang, F., Chang, Y.A., Yan, X.Y., Xie, F.Y., Schmid-Fetzer, R.,
Oates, W.A., “The PANDAT Software Package and its Applications”, Calphad, 26,
175-188 (2002) (Calculation, Equi. Diagram, 24)
[2002Cze] Czeppe, T., Zakulski, W., Bielanska, E., “Determination of the Thermal Stability of Phase
in the Mg-Al System by the Application of DSC Calorimetry”, J. Phase Equilib., 23, in
press (2002) (Experimental, Equi. Diagram, 10)
[2002Dav] Davydov, V.G., Ber, L.B., “TTT and TTP Ageing Diagrams of Commercial Aluminum
Alloys and Their use for Ageing Acceleration and Properties Improvement”, Mater. Sci.
Forum, 396-402, 1169-1174 (2002) (Equi. Diagram, Phys. Prop., Experimental, 10)
58
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
[2002Gul] Gulay, L.D, Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, in “Crystal Chemistry of Intermetallic Compounds”, Abstr. VIII Int. Conf, Lviv,
P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Iva] Ivanchenko, V., Ansara, I., “Cu-Mg (Copper-Magnesium)”, MSIT Binary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 20.10551.1.20, (2002) (Crys. Structure, Equi.
Diagram, Assessment, 13)
[2002Hir] Hirosawa, S., Sato, T., “Atomistic Behavior of Microalloying Elements in Phase
Decomposition of Al Based Alloys”, Mater. Sci. Forum, 396-402, 649-654 (2002)
(Calculation, 7)
[2002Zhu] Zhu, A.W., Gable, B.M., Shiflet, G.J., Starke Jr., E.A., “The Intelligent Design of the High
Strength, Creep-Resistant Aluminium Alloys”, Mater. Sci. Forum, 396-402, 21-30 (2002)
(Experimental, Calculation, Phys. Prop., 23)
[2003Gro] Groebner, J., “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 68)
[2003Jan] Jantzen, T., Fries, S.G., Harmelin, M.G., Faudot, F., Lukas, H.L., Liang, P., Seifert, H.J.,
Aldinger, F., Private Communication (1999)
[2003Luk] Lukas, H.L., “Al-Mg (Aluminium-Magnesium)”, MSIT Binary Evaluation Program, in
MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 49)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.88 at 24°C [V-C]
100 to 81.4 at.% Al at 450°C
[1982Mur]
(Cu)
< 1084.62
Cu1-xAlx
cF4
Fm3m
Cu
a = 361.46
a = 361.52
a = 365.36
at 25°C [Mas2]
0 to 19.7 at.% Al [Mas2]
melting point [1994Mur]
[1991Ell], x=0,quenched from 600°C
[1991Ell], x=0.152,quenched from
600°C, linear da/dx
(Mg)
< 650
hP2
P63/mmc
Mg
a = 320.94
c = 521.01
at 25°C [V-C2]
0 to 11.5 at.% Al at 437°C
[1982Mur]
, CuAl2< 591
tI12
I4/mcm
CuAl2 a = 606.7
c = 487.7
31.9 to 33.0 at.% Cu
[1994Mur]
single crystal [V-C2, 1989Mee]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu,
[V-C, Mas2, 1985Mur]
Pearson symbol: [1931Pre]
59
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
2, CuAl(r)
< 569
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
[1985Mur]
49.8 to 52.3 at.% Cu, [V-C2]
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2Cu47.8Al35.5
a = 812.67
b = 1419.85c = 999.28
55.2 to 59.8 at.% Cu [Mas2, 1994Mur]structure: [2002Gul]
2, Cu11.5Al9(r)
< 570
oI24 - 3.5
Imm2Cu11.5Al9
a = 409.72
b = 703.13c = 997.93
55.2 to 56.3 at.% Cu [Mas2, 1985Mur]structure: [2002Gul]
1, Cu100-xAlx958-848
cubic (?) 37.9 x 40.6
59.4 to 62.1 at.% Cu, [Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.47 x 0.78
55.0 to 61.1 at.% Cu, [Mas, 1985Mur,
V-C2],
NiAs in [Mas2, 1994Mur]
, Cu100-xAlx< 686
hR*
R3m a = 1226
c = 1511
38.1 x 40.7 [Mas2, 1985Mur]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C]
0, Cu100-xAlx Cu 2Al
1022-780
cI52
I43m
Cu5Zn8
- 31 x 40.2 [Mas2],
62 to 68 at.% Cu
[1998Liu]
1, Cu9Al4890
cP52
P43m
Cu9Al4
a = 870.23
a = 870.68
62 to 68 at.% Cu, [Mas2, 1998Liu];
powder and single crystal [V-C2]
from single crystal [V-C2]
, Cu3Al(h)
1049-559
cI2
Im3m
W
a = 295.64
70.6 to 82 at.% Cu [1985Mur][1998Liu]
at 672°C in +(Cu) alloy
CuMg2
< 568
oF48
Fddd
CuMg2
a = 907
b = 528.4
c = 1825
a = 905
b = 528.3
c = 1824.7
a = 904.4 ± 0.1
b = 527.5 ± 0.1
c = 1832.8 ± 0.2
[Mas2, V-C2]
[1994Nay]
[1993Gin]
Cu2Mg
< 797
cF24
Fd3m
Cu2Mg
a = 702.1 64.7 to 69 at.% Cu [Mas2, V-C2]
Mg2Al3 452
cF1168
Fd3m
Mg2Al3
a = 2823.9 [1982Mur]
60-62 at.% Al [1982Mur, 2002Cze]
1168 atoms on 1704 sites per unit cell
[1965Sam, 1982Mur]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
60
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Mg17Al12
458
cI58
I43m
Mn
a = 1054.38 [1982Mur]
At 41.4 at.% Al, [V-C2]
39.5 to 51.5 at.% Al, [1998Lia11]
40 to 52 at.% Al, [2002Cze]
Space group from [1998Don]
Mg23Al30
410-250
hR159
R3
Mn44Si9
a = 1282.54
c = 2174.78
54.5-56.5 at.% Al [1998Lia1, 1998Lia2,
2002Cze]
Structure : 159 atoms refer to
hexagonal unit cell [1968Sam]
1, (Cu1-xAlx)2Mg
Cu2Mg
< 900
cF24
Fd3m
Cu2Mg a = 701.3
a = 715.42
0 x 0.433 [1936Lav1]
space group from [1936Lav1]
at x = 0
For Mg1.75Cu1.0Al0.4 at 480°C
[2000Fau]
* Q, Cu3Mg6Al7 cI96
Im3m
CuFeS2
a = 1208.7 [1951Mir1]
space group from [1991Eff]
* S, CuMgAl2 oC16
Cmcm
BRe3
a = 401
b = 925
c = 715
[1943Per]
space group from [1991Eff]
* T, (Cu1-xAlx)49Mg32 cI162
Im3
Mg32(Al,Zn)49
a = 1428 to 1435
[1952Ber]
composition dependent
space group from [1981Mel2]
* V, Cu6Mg2Al5 cP39
Pm3
Mg2Zn11
a = 827 [1949Sam]
space group from [1991Eff]
* 2, (Cu1-x Alx)2Mg
< 601.6
hP24
P63/mmc
MgNi2
a = 509.8 to 510.2
c = 1664 to 1676
0.492 x 0.576 [1936Lav1]
space group from [1936Lav1]
* 3, (Cu1-xAlx)2Mg
< 537.8
hP12
P63/mmc
MgZn2
a = 507 to 512
c = 829 to 839
0.598 x 0.613 [1936Lav1]
space group from [1936Lav1]
* 5L, (Cu,Al)2Mg hP30 a = 514
c = 2105
stacking variation of Laves phases
observed by electron diffraction
[1962Kom]
* 6L, (Cu,Al)2Mg hP36
P6m2
a = 510
c = 2500
a = 514
c = 2530
stacking variation of Laves phases
observed by electron diffraction
[1977Kit]
[1977Kom]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
61
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Table 2a: Invariant Four-Phase Equilibria
* 9L, (Cu,Al)2Mg hR18 a = 1297
= 22.50°
[1962Kom], stacking variation of Laves
phases observed by electron diffraction
[1977Kom]
* 16L, (Cu,Al)2Mg hP96
P63/mmc
a = 510
c = 6670
a = 514
c = 6740
stacking variation of Laves phases
observed by electron diffraction
[1977Kit]
[1977Kom]
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Mg
0 + 1 L + 1 876.4 U1 0
1
L
1
34.2
36.8
39.2
35.0
65.8
62.8
56.4
65.0
0.0
0.4
4.4
0.0
1 L + 1 + 2 827.6 E1 1
L
1
2
39.7
43.4
36.1
42.0
59.9
52.4
63.9
58.0
0.4
4.2
0.0
0.0
L 0 + 1 + 1 804.0 E2 L
0
1
1
25.1
31.8
32.7
16.3
59.6
68.2
67.3
50.6
15.3
0.0
0.0
33.1
L + 0 + 1 800.3 E3 L
0
1
21.8
27.5
31.3
14.2
62.8
71.4
68.7
52.8
15.4
1.1
0.0
33.0
L + (Cu) + 1 782.8 U2 L
(Cu)
1
12.9
20.7
17.8
8.6
70.2
78.3
81.1
58.7
16.9
1.0
1.1
32.7
0 + 1 + 1 782.1 U3 0
1
1
31.2
14.0
27.2
31.4
68.8
53.0
71.7
68.6
0.0
33.0
1.1
0.0
L + 1 2 + 1 739.9 U4 L
1
2
1
38.7
36.3
42.5
23.4
48.4
63.7
57.5
43.4
12.9
0.0
0.0
33.2
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
62
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
2 + 1 , 1 690.2 D1 2
1
1
42.8
36.3
40.0
23.4
57.2
63.7
60.0
43.3
0.0
0.0
0.0
33.2
L + 2 + 1 V 683.9 P1 L
2
1
V
46.5
44.2
27.1
38.5
41.0
56.8
39.8
46.1
12.5
0.0
33.1
15.4
2 + 1 +V 641.8 U5 2
1
V
43.6
25.0
40.0
38.5
56.4
41.8
60.0
46.1
0.0
33.2
0.0
15.4
L + 2 + V 601.5 U6 L
2
V
58.3
45.8
49.0
38.5
33.5
54.2
51.0
46.1
8.1
0.0
0.0
15.4
2 + , V 582.7 D2 2
V
44.4
40.0
45.0
38.5
55.6
60.0
55.0
46.1
0.0
0.0
0.0
15.4
2 + , V 579.3 D3 2
V
47.5
48.9
45.0
38.5
54.3
51.1
55.0
46.1
0.0
0.0
0.0
15.4
(Cu) + 1+ 1 564.6 E4
(Cu)
1
1
22.8
20.4
29.6
10.2
76.9
79.3
10.4
56.7
0.3
0.3
0.0
33.1
L + 1 2 + V 562.0 U7 L
1
2
V
60.0
32.9
36.6
38.5
26.6
34.1
30.9
46.1
13.4
32.9
32.5
15.4
L + 2 S +V 561.2 U8 L
2
S
V
60.1
36.6
50.0
38.5
26.5
30.9
25.0
46.1
13.4
32.5
25.0
15.4
L + + V 559.4 U9 L
V
62.5
49.6
67.0
38.5
29.4
50.4
33.0
46.1
8.1
0.0
0.0
15.4
L + V + S 543.8 U10 L
S
V
63.0
67.0
50.0
38.5
28.9
33.0
25.0
46.1
8.1
0.0
25.0
15.4
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Mg
63
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
L + 2 3 + S 534.7 U11 L
2
3
S
58.4
39.0
40.4
50.0
10.7
28.0
26.3
25.0
30.9
33.0
33.3
25.0
L + 3 2 + Q 524.9 U12 L
3
2
Q
46.7
40.1
38.5
43.8
7.7
26.5
28.3
18.7
45.6
33.4
33.2
37.5
L + 3 Q + S 513.2 U13 L
3
Q
S
58.6
41.0
43.8
50.0
8.2
25.6
18.7
25.0
33.2
33.3
37.5
25.0
L + (Al) + S 502.1 E5 L
(Al)
S
73.9
67.8
95.7
50.0
15.5
32.2
1.7
25.0
10.6
0.0
2.6
25.0
L + 1 2 + (Mg) 497.3 U14 L
1
2
(Mg)
18.6
31.0
34.6
3.8
7.1
35.5
32.0
0.0
74.3
33.5
33.4
96.2
L 1 + CuMg2 + (Mg) 481.2 E6 L
1
CuMg2
(Mg)
1.1
19.2
0.0
0.1
16.6
47.1
33.3
0.1
82.3
33.7
66.7
99.8
L + Q T + S 479.0 U15 L
Q
T
S
64.1
43.8
52.0
50.0
5.5
18.7
8.3
25.0
30.4
37.5
39.7
25.0
L + S T + (Al) 469.2 U16 L
S
T
(Al)
67.0
50.0
52.4
89.2
4.9
25.0
8.1
0.3
28.1
25.0
39.5
10.5
L + 2 Q + (Mg) 454.6 U17 L
2
Q
(Mg)
26.3
37.2
43.8
7.5
4.1
29.4
18.7
0.0
69.6
33.4
37.5
92.5
L T + Mg2Al3 + (Al) 447.6 E 7 L
T
Mg2Al3(Al)
63.5
55.4
61.1
83.6
0.5
4.1
0.0
0.0
36.0
40.5
38.9
16.4
L T + Mg2Al3 + Mg17Al12 447.6 E8 L
T
Mg2Al3Mg17Al12
57.4
55.1
61.1
51.9
0.3
3.4
0.0
0.0
42.3
41.5
38.9
48.1
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Mg
64
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Table 2b: Invariant Maxima of Two- and Three-Phase Equilibria
L + Q T + (Mg) 426.8 U18 L
T
Q
(Mg)
31.1
47.8
43.8
11.0
1.7
9.3
18.7
0.0
67.2
42.9
37.5
89.0
L (Mg) + T + Mg17Al12 424.7 E9 L
(Mg)
T
Mg17Al12
31.6
11.1
47.9
40.0
1.8
0.0
9.2
0.0
66.6
88.9
42.9
60.0
Mg2Al3 + Mg17Al12 Mg23Al30, T 409.8 D4 Mg3Al2Mg17Al12
Mg23Al30
T
61.1
50.6
56.6
55.2
0.0
0.0
0.0
3.4
38.9
49.4
43.4
41.4
Mg23Al30 Mg2Al3 + Mg17Al12, T 250.1 D5 Mg23Al30
Mg3Al2Mg17Al12
T
56.6
61.1
46.4
55.8
0.0
0.0
0.0
3.5
43.4
38.9
53.6
40.7
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Mg
L 1 909.3 congruent L
1
16.1
16.1
50.5
50.5
33.4
33.4
L 0 + 1 804.4 e3 L
0
1
24.2
31.6
15.8
60.4
68.4
51.1
15.4
0.0
33.1
L 1 + 1 804.0 e4 L
1
1
25.1
32.7
16.3
59.6
67.3
50.6
15.3
0.0
33.1
L + 1 800.4 e5 L
1
20.9
26.9
13.7
63.5
72.0
53.3
15.6
1.1
33.0
L+ 1 2 601.6 p8 L
1
2
51.5
33.9
37.0
16.4
32.9
29.9
32.1
33.2
33.1
L 1 + CuMg2 566.5 e10 L
1
CuMg2
0.2
9.3
0.0
33.9
56.6
33.3
65.9
34.1
66.7
L + 2 S 570.9 p10 L
2
S
60.2
37.5
50.0
20.8
29.8
25.0
19.0
32.7
25.0
L + 2 3 537.8 p11 L
2
3
54.4
38.8
40.3
9.7
28.1
26.4
35.9
33.1
33.3
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Mg
65
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Table 3: Reported Data for the Invariant Reaction E5, L (Al) + S +
L 1 + (Mg) 528.2 e13 L
1
(Mg)
7.8
26.3
1.1
10.7
40.1
0.0
81.5
33.6
98.9
L + 3 Q 527.5 p12 L
3
Q
49.1
40.3
43.8
7.9
26.3
18.7
43.0
33.4
37.5
L (Al) + S 505.5 e14 L
(Al)
S
73.5
95.2
50.0
12.6
1.1
25.0
13.9
3.7
25.0
L + Q T 495.4 p13 L
Q
T
53.5
43.8
51.1
4.8
18.7
8.3
41.7
37.5
40.6
L Mg17Al12 + T 457.2 e16 L
Mg17Al12
T
48.0
47.1
52.4
0.9
0.0
5.4
51.1
52.9
42.2
L Mg2Al3 + T 449.3 e19 L
Mg2Al3T
60.5
61.1
55.3
0.4
0.0
3.8
39.1
38.9
40.9
Temperature [°C] Liquid composition (mass%) References Comment
Cu Mg
500 26.8 6.2 [1937Nis1] -
500 29.7 7.2 [1946Ura, 1949Ura2] -
507 33 6.1 [1948Bro] -
- 29 6.5 [1950Phr] scaled from figure
506.5 33.1 6.8 [1952Han] -
506 33 7 [1967Coo] unidirect solidification
506 33.1 6.25 [1972Gar] unidirect solidification
507 33 7.1 [1973Dav] -
507 34 7.6 [1973Dav] calculated
507 30 6 [1976Mon] -
506±1 - - [1980Bir] d.s.c
506.6 33.4 7.2 [1987Lac] calculated
503 32 7.2 [1995Hua] DTA
503±2 33.4 6.95 [1997Che] calculated
503 30.4 8 [1998Buh] calculated
502.1 30.4 8 [2003Jan] calculated
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Mg
66
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Table 4: Reported Data for the Invariant Reaction E7, L T + (Al) + Mg2Al3
Table 5: Reported Data for the Invariant Reaction U16, L + S T + (Al)
Temperature [°C] Liquid Composition (mass%) References
Cu Mg
451 ~0.0 35 [1919Vog]
447 3 32 [1937Nis1]
445 1.5 33 [1946Ura, 1949Ura2]
451 ~2.7 ~ 32 [1948Bro]
450 ~ 3.5 ~ 32 [1952Han]
- 4 31.5 [1950Phr]
~ 450 2.8 32 [1951Mir2]
443 3.4 34 [1987Lac]
448±5 1.34 34.2 [1997Che]
448 1.5 33.3 [1998Buh]
447.6 1.3 33.4 [2003Jan]
Temperature [°C] Liquid Composition (mass%) References Comment
Cu Mg
471 10 27 [1919Vog] -
465 11 25 [1937Nis1] -
465 10 25.6 [1946Ura] -
462 10 25.6 [1949Ura2] -
467 10 26 [1948Bro] -
465 9.3 26.5 [1951Mir2] -
472.3 11.3 25.7 [1952Han] scaled from figure
467 10 26 [1976Mon] -
468 11.4 25.5 [1987Lac] assessment
467±4 10.7 26.1 [1997Che] calculated
469 11.1 24.6 [1998Buh] calculated
469.2 11.2 24.4 [2003Jan] calculated
67
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Table 6: Reported Data for the Mg-Rich Invariant Reactions E9, U17 and U18
Table 7: Lattice Parameter, a, of the (Al) Phase [1951Poo] at 25°C
Temperature [°C] Liquid Composition (mass%) References Invariant Reaction
Cu Mg
412
419-420
423
425
423.6
426
424.9
17
6
4.6
6
5.4
4.4
4.3
56.5
62.2
67
63
62.6
63.2
63.3
[1933Bas, 1934Por]
[1940Han]
[1949Ura2]
[1951Mir2]
[1997Che]
[1998Buh]
[2003Jan]
L (Mg) + Al11Mg17 +
L (Mg) + Al11Mg17 +
L (Mg) + Al11Mg17 +
L (Mg) + Al12Mg17 + Q
L (Mg) + Al12Mg17 + Q
L (Mg) + Al12Mg17 + Q
L (Mg) + Al12Mg17 + Q
452.0
456.6
11.3
9.9
62.7
63.7
[1997Che]
[2003Jan]
L + 2 (Mg) + Q
L + 2 (Mg) + Q
444.0
428
426.8
6.0
4.4
4.4
52.9
62.3
62.6
[1997Che]
[1998Buh]
[2003Jan]
L + T Al12Mg17 + Q
L + T Al12Mg17 + Q
L + T Al12Mg17 + Q
Analysed Composition (at.%) Observed a [pm] Intended Composition (at.%) Corrected a [pm]
Mg Cu Mg Cu
0.189 0.367 404.8 0.25 0.375 404.81
0.456 0.247 404.97 0.5 0.25 404.99
0.655 0.119 405.1 0.75 0.125 405.14
0.202 0.88 404.58 0.25 0.875 404.6
0.414 0.75 404.72 0.5 0.75 404.76
0.637 0.628 404.9 0.75 0.625 404.95
0.927 0.5 405.07 1 0.5 405.1
1.247 0.362 405.24 1.25 0.375 405.24
1.311 0.246 405.32 1.5 0.25 405.4
1.608 0.127 405.5 1.75 0.125 405.56
0.356 0.302 404.91 0.375 0.313 404.91
0.578 0.179 405.05 0.625 0.188 405.07
1.058 0.422 405.12 1.125 0.438 405.14
0.57 0.659 404.77 0.625 0.688 404.78
0.804 0.521 404.9 0.875 0.563 404.91
68
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
20
40
60
80
20 40 60 80
20
40
60
80
Mg Cu
Al Data / Grid: at.%
Axes: at.%
λ1
S
(Al)
(Mg)(Cu)
θ
β
U6
E5
U7
p8
p10 U8
E1
U1U4
γ1
ε2P1
U16
U2
e5
e3
e4
E3
E2
γ0
U9
η1
e10
E6
U14
U17
E9
λ2
λ3
e16
U 12
U11
U13
U15
p 13p 12
p11
T
Q
E7
E8
e13
e14
e1
p1
p2
e6
p4
e12
U10
U18
e15
p7
Mg17Al12
Mg2Al3p9
e11
ε1
V
CuMg2
e19
e20
Fig. 2: Al-Cu-Mg.
Liquidus univariant
lines and primary
phases
MgZn2Cu2Mg [1934Lav]
Cu2Mgprimary
Cu2Mg+MgNi2prim.
MgNi2
primaryMgZn2
primary[1936Lav1] as-cast
Cu2Mg MgNi2 MgZn2 [1953Kle]
Cu2Mg [1943Gue] annealed close to solidus
Cu2Mg Cu2Mg+MgZn2
[1949Ura1]
Cu2Mg MgZn2
MgNi2
[1936Lav1]
Cu2Mg MgNi2 [1965Sli]
Cu2Mg MgNi2 MgZn2 [1981Mel2]
20 40 60Al, at.%
0.0 Al33.3 Mg66.7 Cu
AlCuMg
MgNi2 MgZn2
stacking variants
[1977Kom]
MgNi2+MgZn2 [1962Kom] slowly cooled from melt
Cu2Mg = �1 MgNi2 = �2 MgZn2 = �3
33.3 Mg 66.7 Al
0.0 Cu
Fig. 1: Al-Cu-Mg.
Phases detected along
the 33.3 at.% Mg
section
69
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
20
40
60
80
20 40 60 80
20
40
60
80
Mg Cu
Al Data / Grid: at.%
Axes: at.%
600
550
900
500
550
650
700
750
800
850
600550
500
550
600
1050
1000
950
900
800850
Fig. 2b: Al-Cu-Mg.
Liquidus projection
with liquidus
isotherms
30
40
50
60
70
10 20 30 40 50
30
40
50
60
70
Mg 80.00Cu 0.00Al 20.00
Mg 20.00Cu 60.00Al 20.00
Mg 20.00Cu 0.00Al 80.00 Data / Grid: at.%
Axes: at.%
S
p8
U16
U17
E9 λ2
λ3
e16
U12
U11
U13
U15
p13
p12 p11
T
Q
E7
E8
U 18
Mg17Al12
Mg2Al3
e19
e20
(Mg)
Fig. 2a: Al-Cu-Mg.
Enlarged part of the
liquidus projetion
shown in Fig. 2
70
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Fig
. 3a:
Al-
Cu
-Mg.
Rea
ctio
n s
chem
e, p
art
1.
Al-
Cu
Al-
Mg
Cu
-Mg
Al-
Cu
-Mg
l (
Cu)
+ β
1036.1
e 1
l +
βγ 0
10
20
p1
l +
γ0
ε 1
95
9p2
l +
ε1
ε 2
850.9
p4
γ 0 +
ε1
γ 1 +
L876.4
U1
ε 1γ 1
+ ε2 +
L827.6
E1
Lγ 0
+ λ1
804.4
e 3
Lγ 0
+ γ1 +
λ1
80
4E2
Lγ 1
+ λ1
804.0
e 4
Lβ
+ γ 0
+ λ1
800.3
E3
L +
β (
Cu)
+ λ1
782.8
U2
γ 0 + ε1
γ1
880.7
p3
β +
γ0
γ 1
781.3
p5
ε 1γ 1
+ ε2
83
7e 2
l (
Cu)
+ λ1
72
5e 6
γ 0 + λ1
β +
γ 1782.1
U3
Lβ
+ λ 1
800.4
e 5
ε 2 +
λ1 +
L
γ 1 +
γ0 +
L
ε 2+
λ 1 +
γ1
β +
γ 1 +
λ1
P1
γ 1 +
ε2
δ690.2
p6
ε 2 +
γ1
δ, λ1
690.2
D1
ε 2 +
δ +
λ 1
β +
γ 0 + λ
1
γ 1 +
δ +
λ 1
ε 1 +
γ1 +
L
β +
λ 1 +
(Cu)
γ 0 +
γ1 +
λ 1
L +
γ1
ε 2 +
λ1
739.9
U4
γ 1 +
ε2
+ L
E4
E4
U5
71
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Fig
. 3b
:
Al-
Cu
-Mg.
Rea
ctio
n s
chem
e, p
art
2
Al-
Cu
Al-
Mg
Cu
-Mg
Al-
Cu
-Mg
β (
Cu) +
γ1
566.9
e 9
l (
Al)
+ θ
547.6
e 12
L +
ε2 +
λ1
V683.9
P1
L +
ε2
η +
V601.5
U6
ε 2 δ
+ ζ
, V582.7
D2
ε 2η
+ ζ,
V579.3
D3
β (
Cu)
+ γ 1
+ λ 1
564.6
E4
L +
λ1
λ 2 +
V5
62
U7
L +
ηθ
+ V
559.4
U9
L +
λ2
S +
V561.2
U8
L +
V
θ +
S543.8
U10
L +
λ2
λ 3 +
S534.7
U11
L +
λ1
λ 2
601.6
p8
Lλ 1
+ C
uM
g2
566.5
e 10
L +
λ2
S
570.9
p10
L +
λ2
λ 3
537.8
p11
lλ 1
+ C
uM
g2
55
2e 11
ε 2η
+ ζ
579.3
e 8
ε 2δ
+ ζ
582.7
e 7
l +
ηθ
595.8
p9
l +
ε2
η624.9
p7
L +
ε2
+ V
ε 2 +
λ1 +
V
V+
η +
ε 2
(Cu)
+ γ 1
+ λ1
V+
η +
θ
V+
λ 1 + λ
2
V+
S +
λ2
U12
ζ +
η +
V
D1
L+
λ 2+V
ε 2 +
λ1
δ +
V641.8
U5
L +
λ1 +
V
ε 2ζ,
V5
88
d(m
ax)
ζ +
δ +
V
λ 1 +
δ +
V
E5
S+
λ 2 +
λ3
L +
V +
θL
+ V
+ S
ε 2+
δ +
V
V+
S +
θ
U14
U2U3
L +
θ+
S
E5
L +
S +
λ3
U13
E6
U4
72
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Fig
. 3c:
A
l-C
u-M
g.
Rea
ctio
n s
chem
e, p
art
3
Al-
Cu
Al-
Mg
Cu
-Mg
Al-
Cu
-Mg
LT
+M
g2A
l 3+
Mg17A
l 12
447.6
E8
L T
+ M
g2A
l 3 +
(A
l)447.6
E7
L +
λ2
Q +
(M
g)
454.6
U17
L +
S
T +
(A
l)469.2
U16
L M
g17A
l 12 +
T
457.2
e 16
L M
g2A
l 3 +
T
449.3
e 19
L +
Q
T +
S4
79
U15
Lλ 1
+C
uM
g2 +
(M
g)
481.2
E6
L +
Q
T
495.4
p13
L +
λ1
λ 2 +
(M
g)
497.3
U14
lM
g2A
l 3+
Mg17A
l 12
449.5
e 18
450.5
e 17
l (
Al)
+ M
g2A
l 3
l C
uM
g2 +
(M
g)
48
5e 15
L (
Al)
+ S
505.5
e 14
Lθ
+ (
Al)
+S
502.1
E5
L +
λ3
Q +
S513.2
U13
L+
λ 2+
(Mg)
L +
Q +
(M
g)
L +
λ3
λ 2 +
Q524.9
U12
L +
λ3
Q
527.5
p12
Lλ 1
+ (
Mg)
528.2
e 13
p11
λ 3 +
Q +
S
(Mg)+
λ 1+λ
2
(Mg)+
Cu
Mg2+λ
1
Q+
S +
Τ
(Al)
+ S
+ Τ
(Mg)
+ Q
+ λ1
U18
E9
(Al)
+Τ+M
g2A
l 3M
g17A
l 12+Τ
+Mg2A
l 3
D4
U18
λ 2 +
λ3 +
Q
L+
T+
(Al)
(Al)
+ S
+ θ
e 12
U11
U10
p8
e 10
L +
Q +
S
L +
T +
S
L +
λ2 +
Q
73
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Fig
. 3d
: A
l-C
u-M
g.
Rea
ctio
n s
chem
e, p
art
4
Al-
Cu
Al-
Mg
Cu
-Mg
Al-
Cu
-Mg
Mg23A
l 30
Mg2A
l 3+
Mg17A
l 12
25
0e 21
Mg
2A
l 3+
Mg17A
l 12
Mg23A
l 30
41
0p14
Mg23A
l 30
Mg2A
l 3+
Mg17A
l 12,
T250.1
D5
Mg2A
l 3+
Mg17A
l 12
Mg23A
l 30,
T409.8
D4
L (
Mg)+
T+
Mg17A
l 12
424.7
E9
L +
Q
T +
(M
g)
426.8
U18
l (
Mg)+
Mg17A
l 12
43
6e 20
e 16
p13
U17
T +
Q +
(M
g)
E8
Mg23A
l 30 +
Mg2A
l 3+
T
T +
Mg17A
l 12
+ M
g2A
l 3
(Mg
)+T
+M
g17A
l 12
T+
Mg17A
l 12+
Mg23A
l 30
L +
T +
(Mg)
74
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
10
10
90
Mg 20.00Cu 0.00Al 80.00
Mg 0.00Cu 20.00Al 80.00
Al Data / Grid: at.%
Axes: at.%
(Al)+θ
(Al)
(Al)+S
(Al)+T
460°C
375°C
20
40
60
80
20 40 60 80
20
40
60
80
Mg Cu
Al Data / Grid: at.%
Axes: at.%
(Cu)+λ1
T
γ1
η2
δ
S
Q
θ(Al)+S+θ
S+V+θ
CuMg2+λ1
CuMg2
Mg23Al30
λ2
λ3
V
λ2+S+V
(Al)+T+S
γ1+λ1
CuMg2+(Mg)+λ1
(Mg)+λ1
(Mg)+Q+λ 2
Mg2Al3
λ1+V
ζ
λ1
(Cu)
(Al)
(Mg)
Mg17Al12
(Mg)
+T+Q
Fig. 5: Al-Cu-Mg.
Isothermal sections in
the Al-rich corner at
460 and 375°C
Fig. 4: Al-Cu-Mg.
Calculated isothermal
section at 400°C
75
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
Mg 5.00Cu 0.00Al 95.00
Mg 0.00Cu 5.00Al 95.00
Al Data / Grid: at.%
Axes: at.%
Q
S52
5500
475
450
425
375350
325
400
300
T
10
90
10
Mg 20.00Cu 80.00Al 0.00
Cu
Mg 0.00Cu 80.00Al 20.00 Data / Grid: at.%
Axes: at.%
(Cu)
25400
700
Fig. 6: Al-Cu-Mg.
Isotherms of the
(Al)-solvus and
phases in equilibrium
with (Al)
Fig. 7: Al-Cu-Mg.
Solubility of Al and
Mg in (Cu)
[1957Rog]
76
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
60 50 40 30 20 10400
500
600
700
800
900
Cu 66.67Mg 33.33Al 0.00
Cu 0.00Mg 33.33Al 66.67Cu, at.%
Tem
pera
ture
, °C
L
L+λ1
L+T
λ1
λ1+λ2
L+λ3
L+λ2
λ 2+Q
λ2+λ3
λ3+S
λ 2+λ3+Q
λ2+λ3+S
L+λ2+λ3 L+Q
S+TQ
+S+
T
λ3+
Q+
S
L+Q+S
L+S+T L+T+Mg2Al3
(Al)+S+T(Al)+T+Mg2Al3
L+Mg2Al3
(Al)+Mg2Al3
10 20 30 40400
500
600
Mg 0.00Cu 22.06Al 77.94
Mg 42.53Cu 0.00Al 57.47Mg, at.%
Tem
pera
ture
, °C
L+Q
L+(Al)+Q
L+S+(Al)
S+(Al)+T
S+(A
l)L+S+Q
L+S
L+T
(Al)+T+L
(Al)
+T
+β
β+ε+T
(Al)+T
L
β+ζ+T
Fig. 8: Al-Cu-Mg.
Isopleth at 33.33 at.%
Mg showing the 1
congruent melting
Fig. 9a: Al-Cu-Mg.
Isopleth at 60 mass%
Al
77
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
10 20 30400
500
Mg 0.00Cu 15.39Al 84.61
Mg 32.23Cu 0.00Al 67.77Mg, at.%
Tem
pera
ture
, °C
L+(Al)L+(Al)+Q
L+(Al)+S
(Al)+S+T
(Al)+S+Q
L+(Al)+T
(Al)+T+β(Al)+T
L
(Al)+S
100
200
300
400
500
600
700
Mg 0.00Cu 1.96Al 98.04
Mg 4.97Cu 0.00Al 95.03Mg, at.%
Tem
pera
ture
, °C
L+(Al)
(Al)
(Al)+Q
(Al)+ S
(Al)+S+T (Al)+T
(Al)+
T+β
(Al)+S+Q
L
4.02.0
Fig. 9b: Al-Cu-Mg.
Isopleth at 70 mass%
Al
Fig. 9c: Al-Cu-Mg.
Isopleth at 95.5
mass% Al
78
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mg
30
600
Cu 25.00Mg 38.00Al 37.00
Cu 35.00Mg 28.00Al 37.00Cu, at.%
Tem
pera
ture
, °C
601.6
λ2
L+λ1
L+λ2
λ2+S+V
L+λ1+λ2
L+λ2
L+λ1+λ2
L+λ1+V
λ2+V
λ2+S
558554
550
20Cu 14.00Mg 42.25Al 43.75
Cu 24.00Mg 32.25Al 43.75Cu, at.%
Tem
pera
ture
, °C
L+λ 2+λ 3
L+λ2
L+λ3
527.5
527
513
Q+λ3+S
L+Q
L+λ3+Q
L+λ
3+S
L+λ3+Q
525
515
Fig. 10a:Al-Cu-Mg.
Isopleth at 37 at.% Al
showing the 2 phase
formation
Fig. 10b:Al-Cu-Mg.
Isopleth at 43.75 at.%
Al showing the Q
phase formation
79
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
Aluminium – Copper – Manganese
Hans Leo Lukas
Literature Data
The most well-investigated details of the constitution are the equilibria of the (Al) solid solution. The first
papers [1927Kri, 1933Saw] assumed equilibrium between (Al), CuAl2 and the most Al-rich binary Al-Mn
phase, at that time assumed to be MnAl4. [1938Pet] and [1939Han] detected a ternary phase which was
verified by [1943Gue, 1944Ray] and [1947Day] and later papers. The liquidus surfaces after [1938Pet] and
[1947Day] disagree, as [1947Day] found lower temperatures for the U type invariant equilibria than
[1938Pet]. Although the most extensive constitutional investigation [1966Koe] accepted Petri's [1938Pet]
results, a newer paper, [1979Bar], determined the distribution coefficients of Cu and Mn between liquid and
(Al) by unidirectional solidification and stated the results to confirm the liquidus of [1947Day]. The
solubility of Cu and Mn in the (Al) solid solution was most precisely determined by [1950Hof] using
electric resistivity measurements. The data were confirmed and supplemented by [1954Bag]. A detailed
review of the liquidus, solidus and solvus of the Al corner is given by Phillips [1959Phi] and [1961Phi], the
liquidus based on [1947Day]. The kinetics of age hardening of the (Al) phase were studied by [1953Kus],
and those of rapidly quenched supersaturated (Al) by Polesya et al. [1968Pol] and [1970Pol]. Another part
of the constitution, studied several times, is the - equilibrium in the Cu corner. [1947Dea] reported 10
isothermal sections between 850 and 400°C in steps of 50°C. The results were confirmed and supplemented
by [1956Wes], giving 9 isothermal sections at 800, 700, 600, 550, 525, 500, 450, 425 and 400°C. Six
isotherms given by [1955Tur] and 8 isotherms given by [1964Rom] are slightly different, but within the
accuracy of the drawings, may be accepted to agree with [1947Dea] and [1956Wes]. A survey of the
constitution of the whole ternary system was first given by [1927Kri], who gave isotherms of the liquidus
surface, but without lines of double saturation. [1943Gue] determined the phases stable at room temperature
by X-ray diffraction. He found a ternary phase 2 additional to 1 detected by [1938Pet].
The most detailed investigation of the whole system is from [1966Koe]. These authors determined
experimentally the liquidus surface, 4 complete and 8 partial isothermal sections. For simplification they
did not distinguish between 0, 1and (denoted ), 0, , 1 and 2 (denoted ), 1 and 2 (denoted ).
The phases 2, 1 and 2 were ignored. The distinction between the phases MnAl(h) and Mn5Al8(h), as well
as between Mn4Al11(h) and Mn4Al11(r) is due to a later paper by the same group of authors [1971Goe].
Also, the distinction between and in the Al-Mn binary system was established later [1987McA]. The
MnAl(h) phase was later determined to be of the W-type [1990Ell] and thus should be treated as identical
to [1966Koe] accepted the results of [1938Pet, 1947Dea] and [1956Wes] and partially those of
[1943Gue].
[1979Wac] studied the field, containing two areas of ferromagnetic alloys. [1982Sca] and [1988Cou]
reported differences in the Cu-rich area. However, their suggestion that 3 is stable up to 900°C is not
convincing when compared with [1956Wes, 1966Koe] or [1979Wac].
The metals used for the experiments were generally of high purity. [1938Pet] and [1950Hof] prepared
Al-Mn master alloys from 99.99% pure Al and high purity crystalline MnCl2. The alloys of [1947Dea]
contained less than 0.005% Si and with a few exceptions less than 0.02% Fe; those of [1950Hof] contained
less than 0.005% Si and 0.0025% Fe. [1956Wes] used “super pure” Al and electrolytic Cu and Mn.
[1966Koe] used 99.9% pure elements. An important feature of the Al-Cu-Mn system are ferromagnetic
alloys, detected by F. Heusler in 1899 and called Heusler alloys. Many papers are dedicated to the study of
these alloys and to another group of ferromagnetic alloys detected later [1961Tsu1]. While [1927Har] could
not determine which phase was responsible for the ferromagnetism, [1928Heu] located the W type phase
to be the ferromagnetic one. Persson [1928Per] and [1929Per] assumed a superstructure with a
face-centered cubic cell with twice the lattice parameter of . This superstructure was confirmed by
[1933Heu, 1934Bra] and [1934Heu]. The phase is metastable below 400°C, but the decomposition into the
stable phases is very slow and needs prolonged annealing above 300°C. The degree of order of the
80
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
superstructure is time dependent and leads to magnetic aging [1934Heu]. [1940Hir] studied the ternary
ordering by the Bragg Williams theory. In later papers the critical temperature of the superstructure
formation was studied. [1962Kim] found, by high temperature X-ray diffraction at 750°C, the absence of
the MnCu2Al type order, but still a CsCl type order. Using X-ray and neutron diffraction, [1968Joh1]
detected the presence of two different cubic lattices in aged nonstoichiometric Heusler alloys, due to the
miscibility gap between MnCu2Al and the metastable quenched Cu3Al. [1968Oho] assumed the
CsCl-MnCu2Al type transition at 650°C from resistivity measurements during rapid cooling. [1969Nes]
found this transition at 400°C and the CsCl to W type transition at 750 to 770°C. [1973Che] measured 620
± 20 and 780 ± 10°C for the two transitions. All these temperatures belong to the composition MnCu2Al.
[1998Kai] measured the two transition temperatures along the line of constant Al content of 25 at.% from
MnCu2Al to quenched Mn5Cu70Al25 by DTA and found nearly linear change from 794 to 679 and from
644 to 541°C, respectively. The Al content has a more pronounced influence on the transition temperature
than the Mn-content at constant 25 at.% Al. [1999Liu] found evidence for the W type/CsCl type transition
also in the binary Al-Mn system in the MnAl(h) phase at 965 to 967°C.
[1973Gra] heated the room temperature equilibrium phase mixture ( 3, Mn and Cu9Al4) at 290 K and thus
synthesized the Heusler alloy between 470 and 500°C. In several papers, the kinetics of decomposition of
the Heusler phase were studied [1968Joh1, 1969Nes, 1971Lis, 1973Che, 1973Gra, 1974Oka, 1975Bou,
1977Urs, 1979Dub, 1980Yam1, 1980Yam2, 1981Sol1, 1981Sol2, 1981Sol3, 1981Sol4, 1982Koz,
1983Koz1, 1983Koz2, 1983Koz3, 1983Tan, 1985Kok, 1987Koz]. Another area of ferromagnetic alloys
was detected in the CsCl type ordered phase by Tsuboya [1961Tsu1, 1961Tsu2] and [1962Tsu]. The
ferromagnetism is explained by antiferromagnetic coupling of the Mn atoms, which are in different site
fractions on the two sublattices of the CsCl type structure. This was confirmed by [1963Kat] by neutron
diffraction. A metastable tetragonal phase in the Al-Mn system is also ferromagnetic [1963Sug]. The
connection of this metastable phase with the CsCl type phase was studied by [1963Sug] and [1978Urs].
[1997Mue] studied this phase in ternary systems of Al-Mn with Cu, Fe, Ni and C. It is formed from the
(hcp) phase during moderately rapid cooling. These authors found the stability range of to extend below
700°C in the ternary Al-Cu-Mn system. [1979Wac] studied both ferromagnetic states of the phase and
determined their areas in the concentration triangle. [1982Kog] studied the ferromagnetism in the area
between the Heusler and CsCl type alloys. The present evaluation is the succesor of the detailed critical
assessment presented in [1991Luk].
Among the huge amount of literature, there is a number of references with minor relevance to the
constitution of the ternary system but providing related additional information. These are given under
“Additional References”, attached to the list of references.
Binary Systems
The binary Al-Cu and Al-Mn systems were accepted from the Landolt Börnstein series [2002LB]. They are
based on the assessments of [1998Sau] and [1999Liu], respectively. The Al-Cu is virtually the same as that
in the MSIT Workplace, from where the description of the Cu-Mn systems was accepted [2003Tur]. For
Al-Mn a very thorough assessment was done by [1987McA].
Solid Phases
The cI2, W type, phase ( ) at elevated temperatures has an extended range of ternary solid solutions and
forms two different superstructures, cP2, CsCl type, and cF16, MnCu2Al type. The latter structure exists
also metastably in quenched Cu3Al as BiF3 type.
Besides these superstructures, three ternary intermetallic phases exist in the Al-Cu-Mn system. 1 was
detected by Petri [1938Pet] and confirmed in all later papers investigating its area of stability. [1952Rob]
explained its existence by the good fit of its Brillouin zones with the Fermi surface, where the Brillouin
zones were derived from the strong X-ray reflections. [1954Rob] determined the crystal structure of the
isotypic phase Mn11Ni4Al60 with Pearson symbol oC156, but about 5 to 6 vacant sites per 156 sites. The
composition was first given by [1938Pet] as 19 mass% Cu and 24 mass% Al. [1943Gue] confirmed an alloy
of this composition to be single phase 1. This composition corresponds to a formula Mn6Cu4Al29, which
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Al–Cu–Mn
is more rich in Mn and Cu than the formula Mn3Cu2Al20 given by [1952Rob]. [1966Koe] gave different
compositions for 1 participating in different invariant equilibria. These compositions range from
Mn6Cu4Al29 as the most Al-rich one to Mn8Cu5Al26 and include Mn8Cu4Al27, Mn7Cu4Al28 and
Mn7Cu5Al27. There is, however, no information on which sites of the oC156 structure (5 4-fold, 9 8-fold,
4 16-fold positions) this exchange takes place. The phase 2 was first detected by [1943Gue] and confirmed
by [1966Koe]. The unit cell is orthorhombic with about 380 atoms per cell, but the structure is not yet
resolved. 3 was found by [1956Wes] to be peritectoidally formed at 550°C, confirmed by [1966Koe] and
found by many authors as decomposition product of the Heusler alloy. Its structure was found by
[1968Joh2] to be of the cubic Laves phase MgCu2 type.
At and near the binary Al-Mn boundary besides these stable phases the metastable phases Mn3Al10 and
MnAl(m) (AuCu type) are formed at moderate cooling rates. At extremely fast cooling rates by melt
spinning icosahedral or decagonal quasicrystalline phases are formed [1988Tsa, 1991Maa, 1992Maa]. A
characteristic composition of the decagonal phase is Mn15Cu20Al65, Maâmar et al. investigated also
Mn15Cu10Al75 and Mn10.5Cu32.5Al57 [1990Eck] prepared quasicrystals of composition Mn15Cu20Al65 by
mechanical alloying in a ball mill. [1992Li] pointed out a relationship between the decagonal
quasicrystalline phases and the crystalline 1 phase. All crystalline phases are listed in Table 1.
Invariant Equilibria
A reaction scheme, mainly based on the work of Köster [1966Koe] is shown in Fig. 1a and Fig. 1b. The
temperatures in the Al corner are changed to those given by [1947Day] (U6 and U8). The simplification used
by [1966Koe] to treat groups of several phases as single phases was partially accepted. However, MnAl(h)
was taken to belong to the phase ( ) as its crystal structure was reported to be the same [1990Ell]. 2 with
a hexagonal, probably NiAs type, structure was treated as separate phase. Finally the following phases are
treated as single ones: 0, 1 and (called ), 0, 1, MnAl(h) and 1 (called ), 1 and 2 (called ),
Mn5Al8(h) and Mn5Al8(r) (called Mn5Al8), Mn4Al11(h) and Mn4Al11(r) (called Mn4Al11), and (called
MnAl4). The phases 2, 1 and 2 are ignored, as they do not seem to enter significantly in the ternary
equilibria. A four-phase equilibrium, L+ +MnAl(h), given by [1966Koe] is not accepted here as and
MnAl(h) are treated to belong to the same phase. The thermal arrests, which [1966Koe] assigned to this
reaction may be caused by the minimum of the L+ + three-phase equilibrium. Another four-phase
equilibrium, 2+ + , had to be added. The temperatures and phase-compositions of the invariant
equilibria are given in Table 2. Since [1966Koe] stated their concentrations to be uncertain by ± 1.5%, the
Al+Cu contents of ( Mn) and the Cu contents of Mn4Al11, MnAl4 and MnAl6 reported by [1966Koe] have
to be taken as tentative only.
Liquidus Surface
The liquidus surface of the whole system is shown in Fig. 2, that of the Al corner in Fig. 3. Figure 2 is based
on [1966Koe], but modified according to the modifications of the reaction scheme discussed in the previous
section. Figure 3 is taken from [1961Phi]. The solidus and solvus surfaces of the (Al) solid solution in
Figs. 4 and 5 are also taken from [1961Phi].
Isothermal Sections
In Figs. 6, 7, 8 and 9, isothermal sections are given, based mainly on the work of [1966Koe], in the Al-corner
on [1961Phi]. Phase notations are partly abbreviated as given under “Invariant Equilibria”.
Notes on Materials Properties and Applications
The (Al) solid solution containing up to 4% Cu and some Mn is the essential phase of the most important
age hardenable aluminium alloys.
Alloys containing the Heusler phase ” MnCu2Al are widely used due to their unique electric and magnetic
properties.
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The metastable AuCu type phase formed during rapid cooling of the epsilon Al-Mn phase is interesting as
hard magnetic material.
Alloys near Cu3Al with small additions of Mn or other elements are used due to the shape memory effect
connected with their martensitic transformation.
Miscellaneous
Quenching of the phase between Cu3Al and MnCu2Al results in a martensite, which shows a shape
memory effect [1981Dob] and [1988Lop]. [1937Koe] measured the enthalpy of mixing of the liquid along
the section Cu67Mn33-Al.
References
[1927Har] Harang, L., “On the Crystal Structure of the Heusler Alloys”, (in German), Z. Kristallogr.,
65, 261-285 (1927) (Experimental, 7)
[1927Kri] Krings, W., Ostmann, W., “Contribution to the Knowledge of the Cu-Al-Mn Ternary
System and its Magnetic Properties”, (in German), Z. Anorg. Allg. Chem., 163, 145-164
(1927) (Equi. Diagram, Experimental, Magn. Prop., 22)
[1928Heu] Heusler, O., “On the Knowledge of the Heusler Alloys, on Mn-Al-Cu” (in German),
Z. Anorg. Allg. Chem., 171, 126-142 (1928) (Experimental, 15)
[1928Per] Persson, E., “X-Ray Analysis of the Heusler Alloys” (in German), Naturwissenschaften, 16,
45 (1928) (Crys. Structure, Experimental, 4)
[1929Per] Persson, E., “On the Structure of the Heusler Alloys” (in German), Z. Phys., 57, 115-133
(1929) (Crys. Structure, Experimental, 13)
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1933Heu] Heusler, O., “Crystal Structure and Ferromagnetism of the Mn-Al-Cu Alloys” (in German),
Z. Metallkd., 25, 261-285 (1933) (Crys. Structure, Experimental, 11)
[1933Saw] Sawamoto, H., “Equilibrium Diagram of the Al-Cu-Mn System” (in Japanese),
Suiyokwai-Shi, 8, 239-246 (1933) (Equi. Diagram, Experimental, 3)
[1934Bra] Bradley, A.J., Rogers, J.W., “The Crystal Structure of the Heusler Alloys”, Proc. Roy. Soc.,
A144, 340-359 (1934) (Crys. Structure, Experimental, 25)
[1934Heu] Heusler, O., “Crystal Structure and Ferromagnetism of the Mn-Al-Cu Alloys” (in German),
Ann. Physik, 19, 155-201 (1934) (Crys. Structure, Experimental, 54)
[1937Koe] Körber, F., Ölsen, W., Lichtenberg, H., “On the Thermochemistry of Alloys II, Direct
Determination of the Heat of Formation of the Ternary Alloys Fe-Ni-Al, Fe-Co-Al,
Cu-Ni-Al, Fe-Al-Si as well as of an Alloy Series of the Cu-Mn-Al System” (in German),
Mitt. K.-W.-Inst. Eisenforschung, 19, 131-159 (1937) (Thermodyn., Experimental, 50)
[1938Pet] Petri, H.-G., “The Aluminium Corner of the Al-Cu-Mn Ternary System” (in German),
Alum. Arch., (14), 5-14 (1938) (Equi. Diagram, Experimental, 7)
[1939Han] Hanemann, H., Schrader, A., “On some Ternary Systems with Al, II. Al-Fe-Mn, Al-Cu-Mn”
(in German), Z. Metallkd., 31, 183-185 (1939) (Equi. Diagram, Experimental, Review, #, 5)
[1940Hir] Hirone, T., Matuda, S., “Theory of the Order-Disorder Transformation in Ternary Alloys”
(in Japanese), Rikagaku-Kenkyusho-Iho, 19, 931-942 (1940) (Theory, 6)
[1943Gue] Guertler, W., Rassmann, G., “The Application of the X-Ray Diffraction for the
Determination of Phase Equilibria in Solid State of Ternary Alloys (Cu-Ni-Co; Al-Cu-Fe;
Al-Sb-Sn; Ag-Cu-Mg; Al-Cu-Mg and Al-Cu-Mn)” (in German), Metallwirtschaft, 22,
65-71 (1943) (Equi. Diagram, Experimental, 16)
[1944Ray] Raynor, G.V., “The Effect on the Compound MnAl6 of Iron, Cobalt and Copper”, J. Inst.
Met., 70, 531-542 (1944) (Equi. Diagram, Experimental, 15)
[1947Day] Day M.K.B., Phillips, H.W.L., “The Constitution of Alloys of Aluminium with Copper and
Manganese”, J. Inst. Met., 74, 33-54 (1947/1948) (Equi. Diagram, Experimental, 33)
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Al–Cu–Mn
[1947Dea] Dean, R.S., Long, J.R., Graham, T.R., Roberson, A.H., Armantrout, C.E., “The Solid
Solution Area of the Copper-Manganese-Aluminium System”, Trans. AIME., 171, 70-88
(1947) (Equi. Diagram, Experimental, 11)
[1950Hof] Hofmann, W., “The Solubility of Copper and Manganese in Solid Aluminium” (in German),
Z. Metallkd., 41, 477-479 (1950) (Equi. Diagram, Experimental, 11)
[1952Rob] Robinson, K., “The Unit Cell and Brillouin Zones of Ni4Mn11Al60 and Related
Compounds”, Philos. Mag., 43, 775-782 (1952) (Crys. Structure, Experimental, 10)
[1953Kus] Kusumoto, K., Ohta, M., “Effect of Manganese on Aging of Al-Cu Alloys” (in Japanese),
Nippon Kinzoku Gakkaishi, 17, 561-564 (1953) (Experimental, 7)
[1954Bag] Bagchi, A.P., Axon, H.J., “The Constitution of Aluminium Rich Alloys Containing Copper,
Manganese and Silicon”, J. Inst. Met., 83, 176-180 (1954/1955) (Equi. Diagram,
Experimental, 15)
[1954Rob] Robinson, K., “The Determination of the Crystal Structure of Ni4Mn11Al60”, Acta
Crystallogr., 7, 494-497 (1954) (Crys. Structure, Experimental, 5)
[1955Tur] Turkin, V.D., Chernova, T.S., “Investigation of Alloys of the Cu-Al-Mn System” (in
Russian), Issled. Splavov Tsvet. Metallov., 1, 106-110 (1955) (Equi. Diagram,
Experimental, 1)
[1956Wes] West, D.R.F., Lloyd Thomas, D., “The Constitution of Copper Rich Alloys of the
Copper-Manganese-Aluminium System”, J. Inst. Met., 85, 97-104 (1956/1957) (Equi.
Diagram, Experimental, 20)
[1958Bla] Bland, J.A., “Studies of Aluminium-Rich Alloys with the Transition Metals Manganese and
Tungsten. II. The Crystal Structure of (Mn-Al)-Mn4Al11”, Acta Crystallogr., 11, 236-244
(1958) (Crys. Structure, Experimental, 19)
[1959Phi] Phillips, H.W.L., “Aluminium-Copper-Manganese”, in “Annotated Equilibrium Diagrams
of Some Aluminium Alloy Systems”, Inst. Metal., London, 35-40 (1959) (Equi. Diagram,
Review, 11)
[1959Tay] Taylor, M.A., “The Crystal Structure of Mn3Al10”, Acta Crystallogr., 12, 393-396 (1959)
(Crys. Structure, Experimental, 10)
[1961Phi] Phillips, H.W.L., “Al-Cu-Mn”, in “Equilibrium Diagrams of Aluminium Alloy Systems”,
Aluminium Development Association, London, 63-66 (1961) (Equi. Diagram, Review, 0)
[1961Tay] Taylor, M.A., “The Space Group of MnAl3”, Acta Crystallogr., 14, 84 (1961) (Crys.
Structure, Experimental, 3)
[1961Tsu1] Tsuboya, I., Sugihara, M., “On the New Magnetic Phase in Manganese-Aluminium-Copper
System”, J. Phys. Soc. Jpn., 16, 571 (1961) (Crys. Structure, Experimental, 3)
[1961Tsu2] Tsuboya, I., “On the New Magnetic Phase in Manganese - Aluminium - Copper System”,
J. Phys. Soc. Jpn., 16, 1875-1880 (1961) (Crys. Structure, Experimental, 11)
[1962Kim] Kimura, R., Endo, K., Ohoyama, T., “A Partially Ordered Structure of the Heusler Alloy
Cu2MnAl at High Temperatures”, J. Phys. Soc. Jpn., 17, 723-724 (1962) (Crys. Structure,
Experimental, 1)
[1962Tsu] Tsuboya, I., Sugihara, M., “The Magnetic Phase in Mn-Al-Co, -Cu, -Fe and -Ni Ternary
Alloys”, J. Phys. Soc. Jpn., 17, 172-175 (1962) (Experimental, 5)
[1963Kat] Katsurai, H., Takada, H., Suzuki, K., “Neutron Diffraction Study of the CsCl Type Phase
Cu-Mn-Al Alloys”, J. Phys. Soc. Jpn., 18, 93-96 (1963) (Crys. Structure, Experimental, 3)
[1963Sug] Sugihara, M., Tsuboya, I., “Structural and Magnetic Properties of Copper Substituted
Manganese - Aluminium Alloy”, Japan. J. Appl. Phys., 2, 373-380 (1963) (Experimental,
Crys. Structure, Magn. Prop., 7)
[1964Rom] Romu, V.G., “Investigation of the Copper Corner of the Phase Diagram of the Cu-Al-Mn
System” (in Russian), Tr. Leningrad. Politekhn. Inst., 234, 57-61 (1964) (Equi. Diagram,
Experimental, 4)
[1966Koe] Köster, W., Gödecke, T., “The Ternary Copper - Manganese - Aluminium System” (in
German), Z. Metallkd., 57, 889-901 (1966) (Equi. Diagram, Experimental, #, *, 11)
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[1968Joh1] Johnston, G.B., Hall, E.O., “Studies on the Heusler Alloys - I. Cu2MnAl and Associated
Structures”, J. Phys. Chem. Solids, 29, 193-200 (1968) (Equi. Diagram, Experimental, 18)
[1968Joh2] Johnston, G.B., Hall, E.O., “Studies on the Heusler Alloys - II. The Structure of
Cu3Mn2Al”, J. Phys. Chem. Solids, 29, 201-207 (1968) (Crys. Structure, Experimental, 6)
[1968Oho] Ohoyama, T., Webster, P.J., Tebble, R.S., “The Ordering Temperature of Cu2MnAl”, Brit.
J. Appl. Phys., 1, 951-952 (1968) (Equi. Diagram, Experimental, 5)
[1968Pol] Polesya, A.F., Kovalenko, V.V., “Composition and Disintegration Kinetics of
Supersaturated Solid Solutions of Rapidly Solidified Alloys of Al-Cu-Mn”, Phys. Met.
Metallogr., 103-109 (1968), translated from Fiz. Metall. Metalloved., 25, 479-485 (1968)
(Experimental, 10)
[1969Nes] Nesterenko, E.G., Osipenko, I.A., Firstov, S.A., “Structure of Cu-Mn-Al Ordered Alloys”,
Phys. Met. Metallogr., 135-139 (1969), translated from Fiz. Metall. Metalloved., 27,
135-140 (1969) (Equi. Diagram, Experimental, 9)
[1970Pol] Polesya, A.F., Kovalenko, V.V., “Phase Diagram of Rapidly Solidified Al-Cu-Mn Alloys”,
Russ. Metall., (1), 114-117 (1970), translated from Izv. Akad. Nauk SSSR, Met., (1),
173-174 (1970) (Experimental, 11)
[1971Goe] Gödecke, T., Köster, W., “An Addition to the Phase Diagram of the Al-Mn System” (in
German), Z. Metallkd., 62, 727-732 (1971) (Equi. Diagram, Experimental, 9)
[1971Lis] Lisse, J.P., Dubois, B., “Preparation and Study of Certain Properties of the Heusler Alloy
Cu2MnAl” (in French), Mem. Sci. Rev. Metall., 68, 521-534 (1971) (Experimental, 26)
[1973Che] Chevereau, D., Gras, J.M., Dubois, B., “Ordering Phenomena in the Heusler Alloy
Cu2MnAl. Determination of Critical Temperatures by X-Ray Diffraction at High
Temperatures” (in French), Compt. Rend. Acad. Sci., Paris, Ser. C, 276, 643-645 (1973)
(Equi. Diagram, Experimental, 4)
[1973Gra] Gras, J.M., Chevereau, D., Dubois, B., “X-Ray Diffraction Study at High Temperature of
the Formation of Its Constituents of the Beta Phase of the Heusler Alloy, Cu2MnAl” (in
French), Compt. Rend. Acad. Sci., Paris, Ser. C, 276, 483-486 (1973) (Equi. Diagram,
Experimental, 5)
[1974Oka] Okada, M., “Phase Transformations in Ordered, Spinodal Cu-Mn-Al Alloys”, Thesis,
California Univ. Berkeley, Report LBL-3176, 1-62 (1974) (Experimental, 33)
[1975Bou] Bouchard, M., Thomas, G., “Phase Transitions and Modulated Structures in Ordered
(Cu,Mn)3Al Alloys”, Acta Metall., 23, 1485-1500 (1975) (Experimental, 43)
[1977Urs] Ursache, M., “Study of the Effect of Thermal Treatments on the Magnetic Properties of
Alloys of the Al-Mn-Cu System” (in Romanian), Constr. Mas., 29, 246-252 (1977)
(Experimental, 9)
[1978Urs] Ursache, M., “Studies of the Possibilities of Using Some Alloys of the Al-Mn-M Systems
for the Fabrication of Permanent Magnets” (in Romanian), Bul. Inst. Politeh. Bucaresti,
Chim. Met., 40(3), 105-112 (1978) (Experimental, 9)
[1979Bar] Bartholomew, D.M.L., Jezuit, M., Watts, B., Hellawell, A., “Segregation and the
Determination of Phase Equilibria in Multicomponent Systems: Al-Cu-Mn”, Solidification
Cast. Met., Proc. Int. Conf. Solidification, Meeting Date 1977, Met. Soc. London, 29-33
(1979) (Equi. Diagram, Experimental, 14)
[1979Dub] Dubois, B., Chevereau, D., “Decomposition of the Heusler Alloy Cu2MnAl at 360°C”,
J. Mater. Sci., 14, 2296-2303 (1979) (Experimental, 36)
[1979Wac] E. Wachtel And R. Winkler, “Constitution and Magnetic Properties of Cu-Mn-Al Alloys”
(in German), Metall, 33, 1160-1168 (1979) (Equi. Diagram, Experimental, 42)
[1980Yam1] Yamane, T., “Aging and Phase Diagram of Cu-Mn-Al Heusler Alloys” (in Japanese), J. Jpn.
Copper Brass Res. Assoc., 19, 131-147 (1980) (Experimental, 19)
[1980Yam2] Yamane, T., Okamoto, H., Takahashi, J., “Aging of Cu-Mn-Al Heusler Alloys”,
Z. Metallkd., 71, 813-817 (1980) (Experimental, 14)
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[1981Dob] Dobrovol'skaya, T.L., Titov, P.V., Khandros, L.G., “Reversible Change of Shape in Alloy
Copper - Aluminium - Manganese”, Phys. Met. Metallogr., 51, 174-177 (1981), translated
from Fiz. Metall. Metalloved., 51, 431-434 (1981) (Experimental, 6)
[1981Sol1] Soltys, J., “The Ordering Process of Atoms in Ternary Alloys Cu-Mn-Al”, Acta Phys. Pol.,
A60, 381-387 (1981) (Experimental, 16)
[1981Sol2] Soltys, J., Kozubski, R., “A Simple Model of the Order-Disorder Transitions in Ternary
Alloys and its Application to Several Selected Heusler Alloys”, Phys. Status Solidi A, 63,
35-44 (1981) (Experimental, 23)
[1981Sol3] Soltys, J., “Order-Disorder Phase Transitions in Ternary Alloys Cu3-xMnxAl”, Phys. Status
Solidi A, 63, 401-406 (1981) (Experimental, 18)
[1981Sol4] Soltys, J., “X-Ray Diffraction Research of the Order-Disorder Transitions in the Ternary
Heusler Alloys B2MnAl (B = Cu, Ni, Co, Pd, Pt)”, Phys. Status Solidi A, 66, 485-491 (1981)
(Experimental, 18)
[1982Kog] Koga, S., Narita, K., “Exchange Anisotropy in Cu-Mn-Al Alloy”, J. Appl. Phys., 53,
1655-1659 (1982) (Experimental, 11)
[1982Koz] Kozubski, R., Soltys, J., “Decomposition of ( )Phase in the Heusler Alloy
Cu2.00Mn1.00Al1.00”, J. Mater. Sci., 17, 1441-1446 (1982) (Experimental, 18)
[1982Sca] Scarabello, J.M., Vicario, E., Mack, J., Counioux, J.J., “Contribution to the Study of the
Ternary Cu-Mn-Al System. Determination of the Section Cu-MnAl6 Limited to the Copper
Rich Part” (in French), Meem. et Etudes Scient., Rev. Meet., 59, 695-707 (1982) (Equi.
Diagram, Experimental, 32)
[1983Koz1] Kozubski, R., Soltys, J., “Precipitation from Metastable -Phase in the Heusler Alloy
Cu2.00Mn1.00Al1.00”, J. Mater. Sci., 18, 1689-1697 (1983) (Experimental, 17)
[1983Koz2] Kozubski, R., Soltys, J., Kuziak, R., “Electron Microprobe Analysis of Phase Segregation
in the Heusler Alloy Cu2.00Mn1.00Al1.00”, J. Mater. Sci., 18, 3079-3086 (1983)
(Experimental, 18)
[1983Koz3] Kozubski, R., Soltys, J., “X-Ray Diffraction Quantitative Analysis of the Heusler Alloy
Cu2.00Mn1.00Al1.00 Annealed at Temperatures Between 423 and 973 K”, J. Mater. Sci.
Lett., 2, 141-143 (1983) (Experimental, 17)
[1983Tan] Tanaka, K., Saito, T., Yasuda, M., “Soft X-Ray Emmission Spectra of Aluminium in
-Phase Cu-Ni-Al and Cu-Mn-Al Alloys”, J. Phys. Soc. Jpn., 52, 1718-1724 (1983)
(Experimental, 14)
[1985Kok] Kokorin, V.V., Osipenko, I.A., Cherekov, S.V., Shirina, T.V., “The Influence of Heating
under Pressure on the Structure State of Heusler Alloy Cu2MnAl”, Phys. Met. Metallogr.,
60, 155-160 (1985), translated from Fiz. Metall. Metalloved., 60, 584-589 (1985)
(Experimental, 10)
[1985Mur] Murray, J.L., “The Aluminium-Copper System”, Int. Met. Rev., 30, 211-233 (1985) (Equi.
Diagram, Review, #, 230)
[1987McA] McAlister, A.J., Murray, J.L., “The Al-Mn (Aluminum-Manganese) System”, Bull. Alloy
Phase Diagrams, 8, 438-447 (1987) (Equi. Diagram, Review, #, 59)
[1987Koz] Kozubski, R., Soltys, J., Dutkiewicz, J., Morgiel, J., “TEM Study of the Decomposition of
the Heusler Alloy Cu2MnAl”, J. Mater. Sci., 22, 3843-3846 (1987) (Experimental, 10)
[1988Cou] Counioux, J.J., Macqueron, J.L., Robin, M., Scarabello, J.M., “Phase Transformations and
Shape Memory Effect in Copper - Aluminium - Manganese Alloys”, Scr. Metall., 22,
821-825 (1988) (Experimental, 10)
[1988Lop] Lopez Del Castilio, G., Blazquez, M.L., Gomez, C., Mellor, B.G., De Diego J. Del Rio, N.,
“The Stabilization of Martensite in Cu-Al-Mn Alloys”, J. Mater. Sci., 23, 3379-3382 (1988)
(Experimental, 25)
[1988Tsa] Tsai, A.-P., Inoue, A., Masumoto, T., “New Quasicrystals in Al65Cu20M15 (M = Cr, Mn or
Fe) Systems Prepared by Rapid Solidification”, J. Mater. Sci. Letters, 7, 322-326 (1988)
(Experimental, Crys. Structure, 17)
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MSIT®
Al–Cu–Mn
[1990Eck] Eckert, J., Schultz, L., Urban, K., “Progress of Quasicrystal Formation During Mechanical
Alloying in Al-Cu-Mn and the Influence of the Milling Intensity”, Z. Metallkd., 81, 862-868
(1990) (Experimental, Quasicrystals, 37)
[1990Ell] Ellner, M., “The Structure of the High-Temperature Phase MnAl(h) and the Displacive
Transformation from MnAl(h) to Mn5Al8”, Met. Trans. A, 21, 1669-1672 (1990)
(Experimental, Crys. Structure, 18)
[1991Maâ] Maâmar, S., Harmelin, M., “On the Transition of the Icosahedral and Decagonal Phases
Towards Equilibrium Phases in Al-Cu-Mn Alloys”, Phil. Mag. Lett., 64, 343-348 (1991)
(Experimental, Egui. Diagram,11)
[1991Luk] Lukas, H.L., “Aluminium - Copper - Manganese”, MSIT Ternary Evaluation Program, in
MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; Document ID: 10.14272.1.20, (1991) (Crys. Structure, Equi. Diagram,
Assessment, 105)
[1992Li] Li, X.Z., Kuo, K.H., “Orthorhombic Crystalline Approximants of the Al-Cu-Mn Decagonal
Quasicrystal”, Phil. Mag. B, 66, 117-124 (1992) 348 (1991) (Experimental, 15)
[1992Maa] Maamar, S., Faudot, F., Harmelin, M., “Relationships Between the Liquidus Temperature
and the Formation of Quasicrystalline Phases in Rapidly Solidified Al-Cu-Mn Alloys”,
Thermochim. Acta, 204, 45-54 (1992) (Experimental, 11)
[1994Mur] Murray, J.L., “Al-Cu (Aluminum-Copper)” in “Phase Diagrams of Binary Copper Alloys”,
Subramanian, P.R., Chakrabati, D.T., Laughlin, D.E. (Eds.), ASM International, Materials
Park, OH, 18-42 1994 (Equi. Diagram, Review, 226)
[1997Mue] Müller, C., Stadelmaier, H.H., Reinsch, B., Petzow, G., “Constitution of Mn-Al-(Cu, Fe, Ni
or C) Alloys near the Magnetic Phase”, Z. Metallkd., 88, 620-624 (1997) (Experimental,
Equi. Diagram, 19)
[1998Kai] Kainuma, R., Satoh, N., Liu, X.J., Ohnuma, I., Ishida, K., “Phase Equilibria and Heusler
Phase Stability in the Cu-rich Portion of the Cu-Al-Mn System”, J. Alloy. Compd., 266,
191-200 (1998) (Experimental, Equi. Diagram, Crys Structure, 28)
[1998Sau] N. Sauter, “System Al-Ti” in “COST 507, Thermochemical Database for Light Metal
Alloys”, Vol. 2, I. Ansara, A.T. Dinsdale, M.H. Rand (Eds.), Office for Official Publications
of the European Communities, Luxembourg, 89-94 (1998) (Assessment, Equi. Diagram,
Thermodyn., Calculation, 27)
[1999Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Thermodynamic Assessment of the
Aluminuim-Manganese (Al-Mn) Binary Phase Diagram”, J. Phase Equilib., 20(1) 45-56
(1999) (Equi. Diagram, Thermodyn., Assessment, Calculation, Experimental, 37)
[2002Gul] Gulay, L.D., Harbrecht,B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, in “Crystal Chemistry of Intermetallic Compounds”, Abstr. VIII Int. Conf., Lviv,
P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002LB] Landolt-Börnstein, Numerical Data and Functional Relationship in Science and
Technology, New Series, Ed. in Chief: W. Martienssen, Group IV: Physical Chemistry, Vol.
19, Thermodynamic Properties of Inorganic Materials compiled by SGTE, Subvolume B,
Binary Systems: Phase Diagrams, Phase Transition Data, Integral and Partial Quantities of
Alloys. Part 1 Elements and Binary System from Ag-Al to Au-Tl. Ed. Lehrstuhl f.
Werkstoffchemie, RWTH Aachen, Authors: Scientific Group Thermodata Europe (SGTE),
Springer Verlag, Berlin, Heidelberg, pp. 139-142 Al-Cu, pp. 164-169 Al-Mn (2002)
[2003Tur] Turchanin, M., Agraval, P., Gröbner, J., Matusch, D., Turkevich, V., “Cu - Mn (Copper -
Manganese)”, MSIT Binary Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.),
MSI, Materials Science International Services GmbH, Stuttgart; to be published, (2003)
(Equi. Diagram, Assessment, Crys. Structure, 25)
87
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
Additional References
[1910Ros] Rosenhain W., Lantsberry, F.C.A.H., “On the Properties of Some Alloys of Cu, Al and Mn”,
9th Report Alloys Research Committee, Proc. Inst. Mech. Eng., London, 119-139 (1910)
(Experimental, Mechan. Prop.)
[1929Mor] Morlet, E., “On Cu-Al with Mn (Co)” (in French), Compt. Rend. Acad. Sci. Paris, 189,
102-104 (1929) (Experimental, Equi. Diagram, 2)
[1933Heu2] Heusler, O., “Lattice Structure and Ferromagnetism of Mn-Al-Cu Alloys. Part 2: Magnetic
and Electrical Investigations” (in German), Z. Elektrochem, 39, 645-646 (1933)
(Experimental, Crys. Structure, 2) see also [1934Heu]
[1933Val] Valentiner, S., Becker, G., “Investigations on Heusler Alloys” (in German), Z. Phys., 83,
371-403 (1933) (Experimental, Crys. Structure, 34)
[1934Fue] Fuess, V., “Al-Cu-Mn” (in German), in “Metallographie des Aluminiums und seiner
Legierungen”, Berlin, 144-148 (1934) (Review, 4)
[1935Val] Valentiner, S., Becker, G., “On Heusler Alloys” (in German), Z. Phys., 93, 629-633 (1935)
(Experimental, 2)
[1943Mon] Mondolfo, L.F., “Metallography of Aluminium Alloys”, Wiley & Sons. Inc., London, 79-81
(1943) (Review, 3)
[1947Ano] Anonymous, “Cu-Mn-Al Alloys”, The Engineer, 183(4766), 470-471 (1947) (Review, 5)
[1948Hum] Hume-Rothery, W., “The Effect of Mn, Fe and Ni on the / Brass Equilibrium”, Philos.
Mag., 39, 89-97 (1948) (Theory, Equi. Diagram, 13)
[1948Sha] Sharma, A.S., “The Metallography of Commercial Alloys of the Duralumin Type”, Trans.
Indian Inst. Met., (1), 39-53 and (2), 11-44 (1948) (Experimental, 43)
[1952Han] Hanemann, H., Schrader, A., “Ternary Alloys of Aluminium” (in German), in “Atlas
Metallographicus III”, part 2, Düsseldorf, 81-85 (1952) (Review, 6)
[1952Haw] Haworth, J.B., Hume-Rothery, W., “The Effect of Four Transitional Metals ob the / Brass
Type of Equilibrum”, Philos. Mag., 43 (7), 613-631 (1952) (Experimental, Equi. Diagram,
23)
[1954Iva] Ivanov-Skoblikov, N.N., “The System Cu-Mn-Al” (in Russian), Zap. Leningrad. Gornogo
Inst., 29(3), 152-180 (1954) (Review, 147)
[1960Spe] Spegler, H., “The Inportance of Research on Eutectics and its Application to Ternary
Eutectic Aluminiun Alloys” (in German), Metall, 14, 201-206 (1960) (Review, Theory, 11)
[1963Oxl] Oxley, D.P., Tebble, R.S., Williams, K.C., “Heusler Alloys”, J. Appl. Phys., 34, 1362-1364
(1963) (Experimental, Crys. Structure, 13)
[1964Tes] Teslyuk, M.Yu., Kripyakevich, P.I., Frankevich, D.P., “New Laves Phases Containing Mn”
(in Russian), Kristallografiya, 9, 558-559 (1964) (Experimental, Crys. Structure, 13)
[1966Sch] Schubert, K., “Structure Research on Metallic Phases” (in German), Metall, 20, 424-430
(1960) (Review, Theory, Crys. Structure, 12)
[1966Vul] Vul'f, B.K., Chernov, M.N., “Influence of Ternary Intermetallic Compounds on the Heat
Resistance of Deformed Aluminium Alloys” (in Russian), Tsvet. Metallurgiya, 147-152
(1960) (Experimental, Mechan. Prop., 15)
[1968Joh3] Johnston, G., “Neutron Diffraction Investigation of Ternary Manganese Alloys”, At.
Energiya, 11(4), 18-24 (1968) (Experimental, Crys. Structure, 15) see also [1968Joh1] and
[1968Joh2]
[1969Gai] Gaillard M., “The Influence of Addition Elements on the Structure of Cu-Al Alloys” (in
French), Mem. Artillerie Franc., 43, 11-42 (1969) (Experimental, Equi. Diagram, 21)
[1969Mai] Maitre, F.Le., “Phase Transformation of Cu-Al Alloys” (in French),
Cuivre-Laitons-Alliages, 107, 8-21 (1969) (Experimental, Equi. Diagram, 10)
[1974Lis] Lisse, J.P., Navrot, F., Pernot, N., Dubois, B., “Precipitation Phenomena during Heat
Treatment of the Phase in Solid Heusler Alloy Specimens” (in French), Mem. Sci. Rev.
Metall., 71, 63-66 (1974) (Experimental, Equi. Diagram, 7)
88
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
[1975Gre] Green, M.L. Chin, G.Y. “Deformation and Fracture of Polycrystalline Cu2MnAl”, Metall.
Trans. A, 6A, 1118-1122 (1975) (Experimental, Mechan. Prop., 9)
[1980Bra] Brandes, E.A., Flint, R.F., “Mn-Phase Diagrams”, Manganese Phase Diagrams,
Manganese Center, Paris, France, 78-79 (1980) (Review, Experimental, 4)
[1981Bre] Brezina, P., “Heat Treatment of Complex Al Bronzes”, Int. Met. Rev., 27(2), 77-120 (1981)
(Review, Mechan. Prop., Equi. Diagram, 210)
[1981Wat] Watanabe H., Sato, E., “Phase Diagram in Al Alloys” (in Japanese), J. Jpn. Inst. Light Met.,
31(1), 64-79 (1981) (Review, Theory, Equi. Diagram, #, 22)
[1982Kan] Kang, S.-J., Stasi, M., Azou, P., “Influence of Mn on Phase Transformations in Cu-Al
Alloys” (in French), Mem. Sci. Rev. Met., 79(5), 229-234 (1982) (Experimental, 12)
[1983Koz4] Kozubski, R., Soltys, J., “Decomposition of the Heusler Alloys Cu2.00Mn1.00Al1.00 During
Isochronal Annealing”, Conference DIMETA-82, Tihany, Hungary, Trans. Tech.
Publications, Rockport, 549-551 (1983) (Experimental, 7) see also [1983Koz1-3]
[1987Sch] Shubert, K., “On the Bindings in the Elements between V and Ga (I). Phases from V to Fe”,
Crys. Res. Technol., 24(4), 517-525 (1987) (Theory, Crys. Structure, 33)
[1988Dan] Danilov, A.N., Likhachev, V.A., “Nature of Matrix Phases in CuAl(Ni,Mn) Alloys” (in
Russian), Fiz. Metall. Metalloved., 65(6), 1176-1181 (1988) (Experimental, Crys.
Structure, 7)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Mn)(h1)
1079-707
cP20
P4132
Mn
a = 631.5 [V-C2]
dissolves 40 at.% Al [1999Liu]
( Mn)(r)
< 710
cI58
I43m
Mn
a = 891.39 [V-C2]
(Al)
< 660
cF4
Fm3m
Cu
a = 404.88 pure Al, 24°C
[V-C2]
2, Cu1-xAlx< 363
-
TiAl3
- 0.22 x 0.235 [Mas, 1985Mur]
long period superlattice
0, Cu1-xAlx1037-964
- - 0.298 x 0.324
[Mas, 1985Mur]
0, Cu1-xAlxCu2Al
1022-780
- - 0.31 x 0.402
[Mas, 1985Mur]
1, Cu9Al4< 873
cP52
P43m
Cu9Al4
a = 871.32
a = 870.68
at 33.8 at.% Al, [V-C2]
from single crystal [V-C2]
, Cu1-xAlx< 686
hR*
a = 869
= 89.78°
0.381 x 0.407 [Mas, 1985Mur]
at x = 38.9 [V-C2]
1, Cu1-xAlx958-848
cI2 ?
W (?)
- 0.379 x 0.406
[Mas, 1985Mur]
89
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
2, Cu1+xAl
850-560
hP4
P63/mmc
NiAs
a = 414.6
c = 506.3
0.47 x 0.78
[Mas, 1985Mur, V-C]
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2
Cu47.8Al35.5
a = 812
b = 1419.85
c = 999.28
55.2 to 59.8 at.% Cu, [Mas2, 1994Mur]
structure: [2002Gul]
2, Cu11.5Al9(r)
< 570
oI24 - 3.5
Imm2
Cu11.5Al9
a = 409.72
b = 703.13
c = 997.93
55.2 to 56.3 at.% Cu, [Mas2, 1985Mur]
structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]
Pearson symbol: [1931Pre]
2, CuAl(r)
< 569
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
[V-C]
, CuAl2< 591
tI12
I4/mcm
CuAl2
a = 606.3
c = 487.2
[V-C]
, Mn4Al3(h)
1260-870
hP2
P63/mmc
Mg
a = 269.0 to 270.5
c = 438.0 to 426.1
40.0 to 46.8 at. % Al
[Mas, 1987McA, 1999Liu]
MnAl(m)
metastable
tP2
P4/mmm
AuCu
a = 277 to 279
c = 354 to 358
ferromagnetic, about 55 at.% Mn,
formed from at rapid or medium
cooling rates
Mn5Al8(h)
1048-957
- - 61.8 to 70.0 at.% Al
[Mas, 1987McA]
Mn5Al8(r)
< 987
hR26
R3m
Cr5Al8
a = 1274
c = 1586
53.0 to 68.6 at.% Al
[Mas, 1987McA]
Mn4Al11(h)
1002-895
oP160
Pnma
a = 1479
b = 1242
c = 1259
71.3 to 75.0 at. % Al
[Mas, 1987McA]
latt. par. from [1961Tay]
Mn4Al11(r)
< 915
aP15
P1
Mn4Al11(r)
a = 509.2
b = 886.2
c = 504.7
= 85.31°
= 100.41°
= 105.34°
[V-C, 1987McA]
Structure: [1958Bla]
Mn3Al10 hP26
P63/mmc
Mn3Al10
a = 754.3
c = 789.8
metastable, formed at cooling rates faster
than 0.2 K s-1 [1971Goe]
Structure: [1959Tay]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
90
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
Table 2: Invariant Equilibria
, MnAl4 (h)
< 923
hP*
or oP*
a = 1995
c = 2452
a = 679.5
b = 934.3
c = 1389.7
[1987McA]
[1987McA]
, MnAl4 (r)
< 690
hP* a = 2840
c = 1240
[1987McA]
MnAl6 oC28
Cmcm
MnAl6
a = 755.18
b = 649.78
c = 887.03
[V-C, 1987McA]
, Mn1-x-yCuxAly Mn(h2)
1246-1143
Cu
< 1083
cF4
Fm3m
Cu
a = 386.2
a = 361.48
0 x 1
at x = 0, y = 0 [V-C]
at x = 1, y = 0, 25°C [V-C]
, Mn1-x-yCuxAly Cu3Al
1049-761
( Mn)(h3)
1143-1079
MnAl(h)
1191-840
'
''
cI2
Im3m
W
cP2
Pm3m
CsCl
cF16
MnCu2Al
a = 294.6
a = 308.1
range see Figs. 6 to 9
at x = 0.757, y = 0.243,
680°C [1985Mur]
at x = 0, y = 0 [V-C]
48.7 to 65.5 at.% Al [1987McA],
structure [1990Ell]
superstructure of
superstructure of ´
* 1,
Mn6+xCu4+yAl29-x-y
< 1020
oB156
Bbmm
Mn6Cu4Al29
a = 2420
b = 1250
c = 772
[1938Pet],
structure: [1954Rob]
0 x 2, 0 y 1, y x [1966Koe]
* 2,
Mn3Cu5Al11
< 700
oP380 a = 1210
b = 2408
c = 1921
[1943Gue, 1966Koe]
* 3,
Mn(Cu0.75Al0.25)2
< 550
cF24
Fd3m
MgCu2
a = 690.46 [1968Joh2]
antiferromagnetic ordering
of the Mn atoms
Reaction T [°C] Type Phase Composition (at.%)
Mn Cu Al
L + Mn5Al8 1 1020 p7 L
Mn5Al8
1
21.3
26.6
21.3
11.4
9.5
11.4
67.3
63.9
67.3
L + Mn5Al8 1 + Mn4Al11 970 U1 L
Mn5Al8
1
18.7
26.7
21.2
8.6
7.3
11.0
72.7
66.0
67.8
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
91
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
L + Mn5Al8 + 1 830 U2 L
Mn5Al8
1
8,4
27.6
23.0
21.1
34.2
12.7
23.9
12.4
54.7
59.7
53.3
66.5
L + Mn4Al11 1 + MnAl4 825 U3 L
1
(6.4)
20.6
(8.5)
10.3
(85.1)
69.1
+ 1 2 700 p12
1
6.0
18.8
41.9
12.4
52.1
68.8
+ 2 638 e11 7.0
3.2
45.0
61.4
48.0
35.4
+ ( Mn) 638 e12
( Mn)
24.4
3.3
69.0
43.4
62.8
1.5
32.2
33.9
29.5
L + MnAl4 1 + MnAl6 625 U4 L
1
(3.8)
18.9
(3.9)
9.9
(92.3)
71.2
L + 2 + 623 U5
L + 1 + 622 U6 L
1
2.1
1.2
17.1
31.8
49.2
11.9
66.1
49.6
71.0
L + MnAl6 1 + (Al) 616 U7 L
1
(Al)
(1.1)
17.9
(0.8)
(7.4)
10.1
(0.5)
(91.5)
72.0
(98.7)
+ 1 + 2 603 U8
1
1.2
16.5
50.5
12.5
48.3
71.0
L + 1 + 582 U9 L
1
1.4
16.6
29.4
11.6
69.2
71.8
+ 2 + 565 U10 0.4
1.8
57.0
61.2
42.6
37.0
+ ( Mn) 3 550 p15
( Mn)
15.9
79.5
63.8
1.2
20.3
19.3
L (Al) + 1 + 547 E2 L
(Al)
1
(0.4)
(0.1)
16.0
(17.0)
(2.4)
9.9
(82.6)
(97.5)
74.1
+ ( Mn) 3 + 520 U11
( Mn)
18.3
80.3
24.7
65.1
1.2
68.8
16.6
18.5
6.5
+ ( Mn) 3 + 420 U12
( Mn)
14.6
78.7
4.6
61.6
1.2
62.3
23.8
20.1
33.1
3+ + 400 E3 7.9
3.6
2.8
68.1
77.6
66.3
24.0
18.8
30.9
Reaction T [°C] Type Phase Composition (at.%)
Mn Cu Al
92
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
Fig
. 1a:
A
l-C
u-M
n.
Rea
ctio
n s
chem
e, p
art
1
Cu
-Mn
Al-
Cu
Al-
Mn
Al-
Cu
-Mn
l +
βΓ
10
37
p6
β l
+ γ
10
97
e 1
L +
Mn5A
l 8 M
n4A
l 11+
τ 19
70
U1
l+
β ε
12
62
p1
L +
εβ
11
35
?p3
Mn5A
l 8+
Mn4A
l 11+
τ 1
(βM
n)
(αM
n),
γ7
06
d1
l +
ε2
η6
24
p13
β Γ
+ ε2
83
6e 8
l +
βε 2
85
1p10
l +
Γβ
95
8e 4
l γ
+ β
10
32
e 2
Lβ
+ Γ
94
0e 5
L
γ +
β8
90
e 6
L +
Mn5A
l 8τ 1
10
20
p7
L +
Mn5A
l 8β
+τ 1
83
0U2
β +
τ 1 τ2
70
0p12
L +
ε2
β +
η6
23
U5
L+β
+η
L +
Mn4A
l 11
MnA
l 4 +
τ1
82
5U3
β (β
Mn
) + Γ
63
8e 12
β τ2 +
Γ6
38
e 11
L +
MnA
l 4τ 1
+ M
nA
l 66
25
U4
l (
Al)
+ M
nA
l 6
65
8e 10
l +
MnA
l 4 M
nA
l 6
70
5p11
β(β
Mn
)+M
n5A
l 8
83
3e 9
ε β
+ (
βMn)
87
2e 7
l+
Mn4A
l 11
MnA
l 4
92
3p9
l+
Mn5A
l 8M
n4A
l 11
10
00
p8
β ε
+ (β
Mn)
10
27
e 3
l +
β
Mn5A
l 8
10
60
p5
γ +
β (β
Mn)
10
67
p4
l+
ε β
11
81
p2
Mn
4A
l 11+
MnA
l 4+
τ 1
L+
Mn4A
l 11+
τ 1
MnA
l 4+
MnA
l 6+
τ 1
Mn5A
l 8+
β+τ 1
L+
MnA
l 4+
τ 1
U12
L+
MnA
l 6+
τ 1U7
ε 2+β
+ηU8U10
U11
L+
β+τ 1
93
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
Al-
Mn
Fig
. 1b
:
Al-
Cu
-Mn
. R
eact
ion s
chem
e, p
art
2
Cu
-Mn
Al-
Cu
Al-
Cu
-Mn
L +
η
θ5
91
p14
β +
τ1
τ 2+
η6
03
U8
β +
(βM
n)
τ 3
55
0p15
l (
Al)
+ θ
548.2
e 16
55
9e 15
βγ
+ Γ
ε 2Γ
+ η
56
0e 14
L +
η
τ 1+
θ5
82
U9
β +
τ 2
Γ+
η5
69
U10
β ε 2
+ Γ
+ η
56
2E1
L (
Al)
+ θ
+ τ1
547.5
E2
β τ3 +
Γ +
γ4
00
E3
β +
(βM
n)
τ3 +
Γ4
20
U12
β +
(βM
n)
τ 3+
γ5
20
U11
ε 2+β
+η
τ 1+τ2+η
β+Γ+
ητ 2
+Γ+η
γ+(β
Mn
)+τ 3
β+τ 3
+Γ(β
Mn
)+τ 3
+Γ
τ 3+Γ
+γ
L +
β
η +
τ1
62
2U6
L +
MnA
l 6τ 1
+ (
Al)
61
6U7
β+η+
τ 1(A
l)+
Mn
Al 6
+τ 1
L+
(Al)
+τ 1
L+
η+τ 1
β+Γ+
ε 2
L+
β+η
L+
β+τ 1
β+τ 1
+τ2
β+τ 2
+Γ
L+
MnA
l 6+
τ 1L
+(A
l)+
Mn4A
l 6β+
(βM
n)+
Γ
β+τ 2
+η
τ 1+θ
+η
L+
τ 1+θ
β+τ 3
+γ
(Al)
+ θ
+τ 1
94
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
20
40
60
80
20 40 60 80
20
40
60
80
Mn Cu
Al Data / Grid: at.%
Axes: at.%
p7
U4
U5
MnAl6 (Al)MnAl4
Mn4Al11
p2
p1
ε
800
U6
ηU9
θ
E2
U7
Γ
U3
U2
β
γ
850900
100095
0
900
950
1000
1050
1100
115012
001250
1300
e5
e6
p3
τ
1050
U1
Mn5Al8
ε2
10
10
90
Mn 12.00Cu 0.00Al 88.00
Mn 0.00Cu 12.00Al 88.00
Al Data / Grid: at.%
Axes: at.%
650
640
630
620
610
660680
700
U7, 616
U4, 625
MnAl4
τ1
(Al)
MnAl6
Al
Fig. 2: Al-Cu-Mn.
Liquidus surface
Fig. 3: Al-Cu-Mn.
Liquidus surface of
the Al corner after
[1991Phi]
95
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
Mn 3.00Cu 0.00Al 97.00
Mn 0.00Cu 3.00Al 97.00
Al Data / Grid: at.%
Axes: at.%400
450
550
600
650 MnAl6 τ1
θ
U7
E2
(Al)+τ1+L
(Al)+MnAl6+L
500
Al
Mn 3.00Cu 0.00Al 97.00
Mn 0.00Cu 3.00Al 97.00
Al Data / Grid: at.%
Axes: at.%
650
640
620
610
600
590
580
570
550
560
630
(Al)+MnAl6+L
(Al)+τ1+L
Al
Fig. 5: Al-Cu-Mn.
Solvus of the (Al)
solid solution after
[1961Phi]
Fig. 4: Al-Cu-Mn.
Solidus of the (Al)
solid solution after
[1961Phi]
96
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
20
40
60
80
20 40 60 80
20
40
60
80
Mn Cu
Al Data / Grid: at.%
Axes: at.%
γ
β
ΓβL
τ1
Mn4Al11
Mn5Al8
ε(βMn)
γ L+γ
L+β
ε+β
β+MnAl
βMn+ε
L+τ1
L+Γ
β+Γ
β+γ
L+γ
(βMn)+γ
β(βMn)+βL+β
β+γ
L+Mn5Al8
20
40
60
80
20 40 60 80
20
40
60
80
Mn Cu
Al Data / Grid: at.%
Axes: at.%
γ
(βMn)
Mn5Al8
Mn4Al11
L
β Γ
τ1
β+γ(βMn)+γ
(βMn)+β
β+Mn 5Al8
L+τ1
L+β
β+Γ
MnAl4
Fig. 6: Al-Cu-Mn.
Isothermal section at
950°C
Fig. 7: Al-Cu-Mn.
Isothermal section at
850°C
Fig. 6: Al-Cu-Mn.
Isothermal section at
950°C
97
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Mn
20
40
60
80
20 40 60 80
20
40
60
80
Mn Cu
Al Data / Grid: at.%
Axes: at.%
γ
(αMn)
Mn 5
Al 8
Mn4Al11
MnAl4
L
Γβ
τ1
τ2
(βMn)+β
(βMn)+γ
β+Γ
β+Mn 5Al 8
β+τ1
L+τ1
β+γ
L+β
L+MnAl6
Mn5Al8+(βMn)
(βMn)
(αMn)+γ
ε2
MnAl6
L+β+τ1
20
40
60
80
20 40 60 80
20
40
60
80
Mn Cu
Al Data / Grid: at.%
Axes: at.%
γ
Γ
η
θ
MnAl6MnAl4
Mn4Al11
(βMn)
(αMn)
τ3
τ1
τ2
β
(αMn)+γ
(βMn)+Γ
β+(βMn) β+Γ
γ+Γ
η+Γ
η+θ
(αMn)+(βMn)+ γ
τ1 +τ
2
(βMn)+Γ+τ3 τ
3+γ+Γ
(βMn)+β+Γ
(Al)+τ1+θ
(Al)
Mn5Al8
Fig. 9: Al-Cu-Mn.
Isothermal section at
20°C
Fig. 8: Al-Cu-Mn.
Isothermal section at
700°C
98
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Nb
Aluminium – Copper – Niobium
Rainer Schmid-Fetzer
Literature Data
The ternary compound Nb(Cu,Al)2 ( ) has been prepared by solid state sintering of the constituent elements
between 1000 and 1100°C [1964Now] and [1965Oes] or by arc melting the components and annealing the
solidified samples [1965Ram] and [1968Hun]. The NbCuAl composition of this -phase occurring in
diffusion couples of Nb with Al-Cu-In alloys has also been observed by electron microprobe analysis
[1978Dew]. The structure of the Laves phase has been investigated by X-ray powder diffraction and the
lattice parameters agree reasonably well [1964Mar, 1964Sch, 1965Oes, 1965Ram] and [1968Hun].
Observation of a cubic Laves phase (MgCu2 type) in samples quenched from above 1000°suggests that
may exhibit polymorphism [1965Oes]. A second ternary compound, Nb6(Cu,Al)7 ( ) has been prepared by
similar methods and studied by powder X-ray [1965Oes] and [1968Hun]. A composition of Nb(Cu,Al)
might be possible for the phase [1965Oes]. However, the occurrence of was not observed by [1978Sav]
and [1980Sav] in their microstructural and X-ray study of Nb-Al-rich samples which had been melted,
quenched and annealed at 800°C. Phase relations in ternary alloys have been studied using X-ray diffraction
with about 40 samples annealed at 1000°C in evacuated silica capsules and air-cooled [1968Hun]. Other
results from fewer samples both for the same temperature [1964Now] and [1965Oes] and for 900°C
[1965Ram] are in agreement with [1968Hun]. The solubility of Cu in Nb-Al phases are in mutual agreement
[1968Hun, 1978Sav] and [1980Sav]. Both the occurrence of a four-phase reaction (Nb)+ Nb2Al+ and
the possible existence of an additional ternary phase at 1300°C are mentioned [1965Oes]. Phase equilibria
at 1000°C and 1400°C have also been studied with 7 and 5 samples, respectively, using similar techniques
by [1990Ric]. An assessment of the then available literature data was published by [1991Bae].
Binary Systems
The three binary systems are accepted from the MSIT Binary Evaluation Program [2002Rom, 2003Gro,
2003Vel] which go substantially beyond the recent reviews given for Al-Cu [1994Mur] and Al-Nb
[1981Ell], and to some extent also for Cu-Nb [1994Cha].
Solid Phases
Data on all solid phases are given in Table 1. Crystal structure data of ternary phases related to the phase
are compiled by [1969Tes].
Isothermal Sections
The isothermal section at 1000°C, given in Fig. 1, is based mainly on the observations of [1968Hun], but
has been revised in order to be consistent with the edge binaries, especially with the liquid phase. In his
original work, [1968Hun] presented some solid state equilibria which do not pertain to the 1000°C isotherm,
but which may develop during his slow air cooling process. These are the equilibria +CuAl+NbAl3 and
NbAl3+CuAl+CuAl2. The tie lines shown erroneously for these equilibria at 1000°C have been repeated in
several reviews [1990Kum, 1979Dri, 1979Cha, 1970Ali].
The single phase regions of and given by [1968Hun] have also been modified in Fig. 1 in order to take
into account other work [1965Oes]. The questionable binary Nb3Al2 phase was not found in ternary
samples.
The isothermal section at 1400°C, Fig. 2, is less well established and based on the 15 sintered samples of
[1990Ric] which were all above 25 at.% Nb. The tie line directions towards the liquid Al-Cu rich phase
could only be estimated.
99
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Nb
Notes on Materials Properties and Applications
Recent interest is in shape memory alloys for high temperature applications. Addition of 0.27 mass% Nb to
Cu86.5-Al13.5 (mass%) alloy increases the Ms temperature from 250 to 313°C, which decreases with
further Nb addition up to 7.86 mass%. In these alloys precipitation of and to a smaller extent also of
phase was found [2000Mor]. Similar data are found in [1999Lel].
The influence of Cu on the critical temperature for superconductivity in the Nb3Al phase has been measured
by [1978Sav] and [1980Sav] and is found to increase from 7.2 K to 9.7 K upon addition of 2.4 at.% Cu.
References
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1964Mar] Markiv, V.Ya., Voroshilov, Yu.V., Kripyakevich, P.I., Cherkashin, E.E., “New Compounds
of the MnCu2Al and MgZn2 Types Containing Aluminium and Gallium”, Sov. Phys.
-Crystallogr. (Engl. Transl.), 9(5), 619-620 (1964), translated from Kristallografiya, 9,
737-738 (1964) (Crys. Structure, Experimental, 4)
[1964Now] Nowotny, H., Oesterreicher, H., “The Crystal Structures of -TaNi3, Ta(Cu,Al)2,
Nb(Cu,Al)2 and Ta6(Cu,Al)7” (in German), Monatsh. Chem., 95, 982-989 (1964) (Crys.
Structure, Experimental, 7)
[1964Sch] Schubert, K., Raman, A., Rossteutscher, W., “Some Structure Data of Metallic Phases (10)”
(in German), Naturwissenschaften, 51, 506-507 (1964) (Crys. Structure, Experimental, 0)
[1965Oes] Oesterreicher, H., Nowotny, H., Kieffer, R., “Study on the Ternaries (V,Nb,Ta)-Cu-Al and
Ta-Ni-Cu” (in German), Monatsh. Chem., 96, 351-359 (1965) (Equi. Diagram, Crys.
Structure, Experimental, 11)
[1965Ram] Raman, A., Schubert, K., “On the Constitution of Alloys Related to TiAl3. III: Study on
some T-Ni-Al and T-Cu-Al Systems” (in German), Z. Metallkd., 56, 99-104 (1965) (Crys.
Structure, Experimental, 14)
[1968Hun] Hunt, Jr.C.R., Raman, A., “Alloy Chemistry of F(U)-Related Phases I. Extension of - and
Occurrence of ’-Phases in the Ternary Systems Nb(Ta)-X-Al (X = Fe, Co, Ni, Cu, Cr,
Mo)”, Z. Metallkd., 59, 701-707 (1968) (Equi. Diagram, Crys. Structure, Experimental, #,
*, 14)
[1969Tes] Teslyuk, M.Yu., “Intermetallic Compounds with Structure of Laves Phases”, in
“Intermetallic Compounds with Structure of Laves Phases”, (in Russian), Moscow, Nauka,
1969, 1-138 (1969) (Crys. Structure, Review, Theory)
[1970Ali] Alisova, S.P., Budberg, P.B., “Al-Cu-Nb” (in Russian), Diag. Sost. Metal. Sistem, Mater.
Vses. Sovesh., 125 (1970) (Equi. Diagram, 1)
[1978Dew] Dew-Hughes, D., Luhmann, T.S., “The Thermodynamics of A15 Compound Formation by
Diffusion from Ternary Bronzes”, J. Mater. Sci., 13, 1868-1876 (1978) (Crys. Structure,
Experimental, 41)
[1978Sav] Savitsky, E.M., Jefinov, Yu.V., Muchin, G.G., Frolova, T.M., “Structure and Properties of
Equilibrium and Rapidly Quenched Cu-Containing Alloys”, Rapidly Quenched Metals III,
1, 167-170 (1978) (Equi. Diagram, Experimental, #, 20)
[1979Cha] Chang, Y.A., Neumann, J.P., Mikula, A., Goldberg, D., “Cu-Al-Nb”, in “Phase Diagrams
and Thermodynamic Properties of Ternary Cu-Metal Systems”, INCRA Monograph VI,
NSRDS, USA (1979) (Equi. Diagram, Crys. Structure, Review, #, 4)
[1979Dri] Drits, M.E., Bochvar, N.R., Guzei, L.S., Lysova, E.V., Padezhnova V., Rokhlin, L.L.,
Turkina, N.I., “Cu-Al-Nb” in “Binary and Multicomponent Copper-Base Systems” (in
Russian), Nauka Moskow, 78-79 (1979) (Equi. Diagram, 1)
[1980Sav] Savitsky, E.M., Jefimov, Yu.V., Frolova, T.M., Shomova, N.A., “Microstructure and
Properties of Alloys V(Nb)-Al(Ga,Si,Ge,Sn)-Cu” (in German), J. Less-Common Met., 76,
81-98 (1980) (Equi. Diagram, Experimental, #, 41)
100
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Nb
[1981Ell] Elliott R.P., Shunk, F.A., “The Al-Nb System”, Bull. Alloy Phase Diagrams, 2, 75-81
(1981) (Equi. Diagram, Crys. Structure, Review, #, 31)
[1985Mur] Murray, J.L., “The Al-Cu System”, Int. Met. Rev., 30, 211-233 (1985) (Equi. Diagram,
Crys. Structure, Review, #, 230)
[1989Mee] Meetsma, A., de Boer, J.L., van Smaalen, S., “Refinement of the Crystal Structure of
Tetragonal Aluminum-Copper (Al2Cu)”, J. Solid State Chem., 83(2), 370-372 (1989) (Crys.
Structure, Experimental, 17)
[1990Kum] Kumar, K.S., “Ternary Intermetallics in Aluminium-Refractory Metal-X Systems (X = V,
Cr, Mn, Fe, Co, Ni, Cu, Zn)”, Int. Mater. Rev., 35(6), 293-327 (1990) (Crys. Structure, Equi.
Diagram, Review, 158)
[1990Ric] Rickes, B., “Reactiones in the Al-Cu-Nb-(O) System, Constitutional sTudies of Syntered
Engineering Materials”, Dissertation, Univ. Stuttgart, (1990) (Experimental, Equi.
Diagram, 161)
[1991Ell] Ellner, M., Kolatschek, K., Predel, B., “On the Partial Atomic Volume and the Partial Molar
Enthalpy of Aluminium in Some Phases with Cu and Cu3Au Structures”, J. Less-Common
Met., 170, 171-184 (1991) (Experimental, Crys. Structure, 57)
[1991Bae] Bätzner, Ch., Hayes, F., Ran, Q., Schmid, E.E., Schmid-Fetzer, R. , ”Aluminium - Copper
- Niobium”, MSIT Ternary Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.),
MSI, Materials Science International Services GmbH, Stuttgart; Document ID:
10.16131.1.20, (1991) (Crys. Structure, Equi. Diagram, Assessment, 14)
[1993Bar] Barth, E.P., Sanchez, J.M., “Observation of a New Phase in the Niobium-Aluminium
System” Scr. Metall. Mater., 28, 1347-1352 (1993) (Crys. Structure, Equi. Diagram,
Experimental, 9)
[1994Cha] Chakrabarti, D.J., Laughlin, D.E., “Cu-Nb (Copper-Niobium)” in “Phase Diagrams of
Binary Copper Alloys”, ASM International, Materials Park, OH, 266-270 (1994) (Equi.
Diagram, Crys. Structure, Thermodyn., Review, 22)
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)”, in “Phase Diagrams of Binary Copper
Alloys”, Subramanian, P.R., Chakrabarti, D.J., Laughlin, D.E. (Eds.), ASM International,
Materials Park, OH, 18-42 (1994) (Equi. Diagram, Crys. Structure, Thermodyn., Review, #,
*, 226); similar to [1985Mur]
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264, 201-208 (1998) (Equi. Diagram,
Experimental, #, *, 25)
[1999Lel] Lelatko, J., Morawiec, N., Koval’, Yu.N., Kolomyttsev, V.I., “Structure and Properties of
High-Temperature Alloys with the Effect of Shape Memory in the System Cu-Al-Nb”, Met.
Sci. Heat Treat., 41(7-8), 351-353 (1999) (Experimental, Magn. Prop., Mech. Prop., 5)
[2000Mor] Morawiec, H., Leltko, J., Koval, Yu., Kolomytzev, V., “High-Temperature Cu-Al-Nb
Shape memory Alloys”, Mater. Sci. Forum, 327-328, 291-294 (2000) (Experimental,
Mechan. Prop., 8)
[2001Liu] Liu, X.J., Wang, C.P., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Stability Among the
(A1), (A2), and (D83) Phases in the Cu-Al-X System”, J. Phase Equilib., 22, 431-438
(2001) (Equi. Diagram, Experimental, 14)
[2002Gul] Gulay, L.D, Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. ”Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Rom] van Rompaey, T., “Cu-Nb (Copper-Niobium)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 20.12479.1.20, (2002) (Crys. Structure, Equi. Diagram,
Assessment, 16)
[2003Gro] Gröbner, J., “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 68)
101
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Nb
[2003Vel] Velikanova, T., Ilyenko, S., “Al-Nb (Aluminium-Niobium)”, MSIT Binary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram,
Assessment, 81)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 pure Al at 25°C [Mas2]
0 to 2.48 at.% Cu [Mas2]
(Cu)
< 1084.62
cF4
Fm3m
Cu
a = 361.46
a = 361.52 +
25.26xAl
at 25°C [Mas2],
0 to 19.7 at.% Al [Mas2]
melting point [1994Mur]
[1991Ell], quenched from 600°C,
xAl=0 to 0.152
practically no solubility for Nb
[1994Cha]
(Nb)
< 2469
cI2
Im3m
W
a = 330.04 pure Nb, [1994Cha]
dissolves up to 1.2 at.% Cu at 1080°C
[1994Cha]
dissolves up to 21.5 at.% Al [Mas2]
, Cu3Al(h)
1049-559
cI2
Im3m
W
a = 295.64
70.6 to 82 at.% Cu [1985Mur]
at 672°C in +(Cu) alloy (Ti free)
[1998Liu]
dissolves at least 0.81 at.% Ti [2001Liu]
1 cF16
Fm3m
BiF3
a = 585 metastable [1994Mur]
supercell of
2, Cu100-xAlx< 363
-
TiAl3long period
super-lattice
-
a = 366.8
c = 368.0
22 x 23.5 [Mas, 1985Mur]
76.5 to 78.0 at.% Cu
at 76.4 at.% Cu
(subcell only)
0, Cu100-xAlx Cu 2Al
1037-800
cI52
I43m
Cu5Zn8
- 31 x 40.2 [Mas2],
62 to 68 at.% Cu
[1998Liu]
1, Cu9Al4< 890
cP52
P3m
Cu9Al4
a = 870.23
a = 870.68
62 to 68 at.% Cu [Mas2, 1998Liu];
powder and single crystal [V-C2]
from single crystal [V-C]
, Cu100-xAlx< 686
hR*
R3m
a = 1226
c = 1511
38.1 x 40.7 [Mas2, 1985Mur]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C]
1, Cu100-xAlx958-848
cubic? - 37.9 x 40.6
59.4 to 62.1 at.% Cu [Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.47 x 0.78
55.0 to 61.1 at.% Cu [Mas, 1985Mur,
V-C2], NiAs in [Mas2, 1994Mur]
102
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Nb
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2Cu47.8Al35.5
a = 812
b = 1419.85c = 999.28
55.2 to 59.8 at.% Cu [Mas2, 1994Mur]structure: [2002Gul]
2, Cu11.5Al9(r)
< 570oI24 - 3.5
Imm2Cu11.5Al9
a = 409.72
b = 703.13c = 997.93
55.2 to 56.3 at.% Cu [Mas2, 1985Mur]structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200c = 863.52
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu
[V-C2]
Cu2Al3 hP5
Pm1
Ni2Al3
a = 410.6
c = 509.4
metastable [1994Mur]
~40 to 50 at.% Cu
, CuAl2< 591
tI12
I4/mcm
CuAl2
a = 606.7
c = 487.7
31.9 to 33.0 at.% Cu [1994Mur]
single crystal
[V-C2, 1989Mee]
’ tP6
distorted CaF2
a = 404.82
c = 581.17
Metastable [1994Mur]
Nb3Al cP8
Pm3n
Cr3Si
a = 518.6 [V-C2]
18.6 to 25 at.% Al [Mas2]
Nb2Al tP30
P42/mnm
CrFe
a = 994.3
c = 518.6
[V-C2]
30 to 42 at.% Al [Mas2]
NbAl3 tI8
I4/mmm
Al3Ti
a = 384.1 ± 1
c = 860.9 ± 2
[V-C2]
Nb3Al21350 < T < 1590
tP20
P42/mnm
Al2Zr3
a = 707 ± 8
c/a ~ 0.05
[1993Bar]
42.4 at.% Nb, equilibrium needs to be
checked
* ,
Nb(CuxAl1-x)2
hP12
P63 /mmc
MgZn2
a = 502
c = 830
a = 502.3
c = 809.0
a = 502
c = 808
x = 0.25 [1965Oes]
x = 0.50 [1968Hun]
x = 0.60 [1965Oes]
homogeneity range, see Fig. 1
[1965Oes];
probability of a cubic high temperature
polymorph (a = 711 pm) [1965Oes]
* ,
Nb6(Cu0.5Al0.5)7
hR13
R3m
(W6Fe7)
a = 502.9
c = 2736
prototype is tentative
[1965Oes, 1968Hun]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
103
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Nb
20
40
60
80
20 40 60 80
20
40
60
80
Nb Cu
Al Data / Grid: at.%
Axes: at.%
L
NbAl3
τ
(Cu)
µ
Nb2Al
(Nb)
γ0
βθ´
L+τ
(Nb)+µ+(Cu)
τ+γ0
τ+β
τ+(Cu)
Nb2Al+τ
Fig. 1: Al-Cu-Nb.
Isothermal section at
1000°C
20
40
60
80
20 40 60 80
20
40
60
80
Nb Cu
Al Data / Grid: at.%
Axes: at.%
L
(Nb)+L
(Nb)+θ´+L
Ni2Al+L
ττ+L
Ni2Al+τ
NbAl3
Ni2Alθ´
(Nb)
Fig. 2: Al-Cu-Nb
Partial isothermal
section at 1400°C
[1990Ric]
104
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
Aluminium – Copper – Nickel
Alan Prince†, updated by K.C. Hari Kumar
Literature Data
Over the last many years several researchers have investigated the Al-Cu-Ni system due to the interest in
thermoelastic martensitic transformation exhibited by certain alloys of this system. This property is
responsible for the unique mechanical behavior of these alloys such as shape memory effect, superplasticity
and stress-induced martensitic transformations. These alloys have the potential to be used at higher
application temperatures ( 200°C) than the conventional shape memory alloys found in Al-Cu-Zn and
Ni-Ti systems ( 100°C) [1990Ye, 1998Pel, 2001Mot], even though it suffers from deterioration of
mechanical properties due to grain boundary embrittlement [1984Hus, 2001Mot].
Although much work has been reported on the constitution of the Al-Cu-Ni system, there is still no
definitive interpretation of the complete equilibria. Nevertheless, there is broad agreement on the major
features of the ternary phase diagram. Early constitutional studies were done by [1923Aus, 1923Bin,
1928Nis, 1936Gri1, 1936Gri2, 1938Ale, 1938Bra, 1940Bra, 1940Rap, 1941Tur, 1945Tur, 1948Koe,
1952Han, 1952Haw, 1956Bow, 1957Lu1, 1957Lu2, 1957Ray, 1972Bed, 1978Tho, 1983Haf, 1983Rud,
1985Li, 1988Ahm]. Later works include publications by [1990Sun, 1994Jia, 1998Pel, 2001Liu, 2003Wan].
[1923Aus] investigated the complete ternary system using 250 alloy compositions, with emphasis on
Cu-rich alloys containing 0 to 20 mass% Al, Ni. Thermal analysis was used to construct a ternary liquidus
surface and, from it, a series of vertical sections on which only the liquidus was given. The Al used by
[1923Aus] contained 0.7 mass% impurities. The salient information provided by this work is the presence
of a maximum in the liquidus surface running from NiAl to Cu3Al, the presence of a eutectic trough joining
the binary Ni-rich eutectic reaction L ( ,NiAl)+Ni3Al to the binary Al-Cu eutectic reaction
L (Cu)+( ,Cu3Al) and the claim that there is a further eutectic trough. This latter trough was said to join
the Al-Cu eutectic L (Al)+ , to the Al-Ni eutectic L (Al)+NiAl3. They concluded that there was neither
a ternary eutectic reaction nor the existence of a liquidus surface associated with any ternary compound.
[1923Bin] studied the liquidus surface Al-rich corner up to 12 mass% Cu, 10 mass% Ni, using low purity
Al (99.65 mass%). Using thermal analysis (5 K·min–1 cooling and heating rates), metallography and
high-temperature electrical resistance techniques they detected the presence of a ternary eutectic reaction,
L (Al)+ + , at about 540°C and another invariant reaction L+Ni2Al3 (Al)+ at 585 ± 5°C. [1923Bin] was
the first to mention the occurrence of a ternary phase and attributed the stoichiometry as NiCu2Al5. This
composition lies close to the Al-rich boundary of the phase as shown later by [1938Bra, 1948Koe,
1957Lu1] and [1957Lu2]. [1928Nis] confirmed the ternary eutectic reaction that [1923Bin] found and gave
the liquid composition as 67.5Al-0.5Ni (mass%) at 540°C. This is close to compositions quoted by later
investigators. Two ternary transition reactions were also detected with reaction temperatures of 600 and
585°C. [1928Nis] considered these reactions to be L+NiAl3 (Al)+ (585°C) with L at 74.5Al-2.5Ni
(mass%) and L+Ni2Al3 NiAl3+ (600°C) with L at 73Al-4Ni (mass%). Later works, [1948Koe] and
[1952Han], have established that these two transition reactions are L+Ni2Al3 (Al)+ and
L+NiAl3 (Al)+Ni2Al3, although there is discrepancy with respect to the temperature. [1936Gri1] reported
that the addition of 2 mass% Ni to 11.5 to 13.0 mass% Al bronzes raised the binary eutectoid horizontal,
( ,Cu3Al) (Cu)+ 1, from 570 to 605°C. [1936Gri2] refers to the effect of 6 mass% Ni and states that an
alloy with 10 mass% Al has a eutectoid at 780°C. This is not agreed by other researchers. [1938Ale] studied
over 100 alloy compositions in characterizing the equilibria in the region Cu-Ni-NiAl-Cu3Al. Total
impurities in the alloys, as determined spectrographically, were less than 0.1 mass%, which was an
improvement over the starting materials used by [1923Aus]. Thermal analysis, metallography and X-ray
powder diffraction techniques were used to elucidate the equilibria. Both liquidus and solidus surfaces were
reported in addition to five isothermal sections in the range 500-900°C. Thirteen vertical sections at constant
Al or Ni content and the section NiAl-Cu3Al were presented. The liquidus of the Cu3Al-NiAl section shows
good agreement with that of [1923Aus]. An invariant reaction, L+Ni3Al (Ni,Cu)+NiAl, is found to occur
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at 1250°C. The corresponding liquid composition is not given by [1938Ale] but a small region of primary
Ni3Al is shown in the vertical section at 60 mass% Ni. The most significant finding of [1938Ale] was of a
complete solid solution series between ordered bcc phase ( ,NiAl) and the disordered bcc phase ( ,Cu3Al)
with the appearance of solid immiscibility at 800°C with breakdown of the solid solution into two phases.
[1938Bra] used X-ray diffraction techniques to determine the phases present in the complete ternary system.
Very pure materials were used (99.992% Al, electrolytic Cu, 99.97% Ni) and all alloys were annealed for
72 h at temperatures that varied with composition. Powders were prepared from bulk samples and heated to
various temperatures (470-950°C), followed by cooling to room temperature at 10 K/h. They did not detect
the ( ) phase, but observed three related type phases (denoted , 1 and 2). The extent of the ternary
phase was delineated for the first time and its structure given as a deformed bcc. The simplest formula
proposed by [1938Ale] was NiCu3Al6. In a later paper [1940Bra] estimated that the constitution represented
the state of affairs at a temperature between 500 and 700°C. [1940Rap] determined the constitution from 0
to 40 mass% Cu, 0 to 30 mass% Ni using thermal, microscopic and X-ray techniques. A total of 162 alloy
compositions, prepared from 99.996 mass% Al, electrolytic Cu and 99.8 mass% Ni, were studied as-cast,
after slow cooling and after annealing at 530°C for 2 to 6 weeks followed by water quenching. Surprisingly
little detail is given of the results of this work. A liquidus projection is also reported by [1940Rap], but no
isothermal or vertical sections are given to substantiate the liquidus proposed. The projection shows five
ternary phases, designated X, Y, Z, T and U, with regions of primary separation within the range 1 to 10
mass% Ni. Eight invariant reactions are proposed. The ternary eutectic reaction at 546.6°C is the only
reaction that has been confirmed and is well-established. [1941Tur] examined the Cu3Al-NiAl section and
reported a value of 585°C for the ternary eutectoid temperature. [1946Smi] determined the ternary eutectoid
temperature by dilatometry and quoted 597 to 603°C. [1954Hay] re-determined the binary Al-Cu eutectoid
temperature as 565 ± 2°C and reported the ( ,Cu3Al) phase to have a composition 12.1Al-3.1Ni (mass%)
at the four-phase plane (605 ± 2°C). [1979Kuz] also found 605°C for the eutectoid temperature when 2
mass% Ni was added to the binary eutectoid. A major contribution was also made by [1948Koe]. A total of
250 alloy compositions in the region AlCu3Al-NiAl were studied. The region Cu-Ni-NiAl-Cu3Al was
excluded in the study and the liquidus isotherms down to 1000°C were taken from [1923Aus]. [1948Koe]
accepted the transition reaction L+Ni3Al (Ni,Cu)+ , reported by [1938Ale] and placed it at 10Al-47Ni
(mass%). [1948Koe] also determined the primary solidification fields in alloys cooled from the melt.
Isothermal sections were also determined at 900°C (48 h anneal), 700°C (72 h), 500°C (672 h) and 600°C
(unspecified annealing time). In a review of work on Al-rich alloys [1952Han] re-determined the
temperature and location of three invariant reactions near the Al-corner, established by previous
investigators. The transition reaction L+NiAl3 (Al)+Ni2Al3 was placed at 598.8°C, but it differs
substantially from the 630°C found by [1948Koe] and confirmed by [1982Ask]. The transition reaction
L+Ni2Al3 (Al)+ was placed at 561°C compared with 585°C [1923Aus] and [1928Nis] and ~590°C
[1948Koe]. Whereas the liquid phase composition quoted by [1952Han] for L+NiAl3 (Al)+Ni2Al3 agrees
closely with [1948Koe], 81.2Al-4.7Ni as against 80Al-4Ni (mass%), the liquid composition for the reaction
L+Ni2Al3 (Al)+ is 4 to 5 mass% Al lower than that reported by [1928Nis, 1948Koe]. [1957Ray]
questioned how accurately the boundaries of primary separation were determined by [1948Koe] and they
reinvestigated the region of primary separation of using 40 alloy compositions. It is a reflection of the
inconsistency between results in the Al-rich alloys that led [1961Phi] to conclude that it was not possible to
draw liquidus isotherms. [1952Haw] determined the phase boundaries adjoining the (Ni,Cu) and ( ,Cu3Al)
phase regions up to 1.5 at.% Ni at 672°C. For this very small composition range, 0 to 1.5 at.% Ni, 64 alloy
compositions were studied. The results agree with the phase boundaries of [1938Ale] at 700°C. [1956Bow]
examined the crystal structure of the ternary phase, using crystals extracted from slowly cooled melts. He
found evidence for two modifications. The 1 phase has a rhombohedral unit cell and corresponds to the
formula Ni1.2Cu4.8Al7. The 2 phase is cubic, a superstructure of the CsCl type, with the formula NiCu3Al6,
as noted for by [1938Bra]. Both 1 and 2 are based on a CsCl type arrangement of Al and heavy atoms,
the large unit cells being produced by two different ordered distributions of vacancies in place of heavy
atoms. [1957Lu1] and [1957Lu2] studied the phase region using 58 alloy compositions prepared from
very pure materials (99.992% Al, 99.999% Cu, 99.99 mass% Ni). All alloys were homogenized for 1680 h
at 650°C, powdered and the powders annealed for 24 h at 600°C, followed by cooling at 5 to 10 K/h to room
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temperature. Eight types of closely-related structures were found in the region. [1972Bed] studied the
effect of Ni additions on the extent of the 1 phase region at room temperature. Alloys were prepared from
high-purity elements, homogenized for 12 h at 900°C, cooled to 850°C and held for 24 h, then cooled to
750°C and held for a further 24 h. This stepwise cooling was continued with the temperature being dropped
by 50°C and the sample held for 48 h each temperature from 700 to 100°C. In total, alloys were soaked for
720 h throughout the temperature range. Alloys were examined by X-ray diffraction and metallography.
The solubility of Ni in the 1 phase was 3.4 at.% Ni on the section from 33.33Al-66.67Cu (at.%) towards
Ni, 1.8 at.% Ni on the 66.67 at.% Cu section and 5.4 at.% Ni on the 33.33 at.% Al section. This data is in
excellent agreement with [1938Bra] and [1948Koe]. Alloys in the Al-rich corner, with up to 33Cu-10Ni
(mass%) were homogenized at 375°C by [1983Haf]. Metallography was used to identify the phases in two-
and three-phase regions. Of 25 alloy compositions studied, 23 fell into the phase regions given by
[1938Bra]. [1983Rud] used microprobe analysis of a diffusion couple held for 8 h at 600 to 900°C between
5Al-90Cu (mass%) and Ni. There is fair agreement between [1983Rud] and [1938Ale] for the phase
boundary between (Ni,Cu) and (Ni,Cu)+Ni3Al at 900°C, but differs considerably at lower temperatures.
The (Ni,Cu)+Ni3Al boundary with Ni3Al is placed at higher Al contents by [1983Rud], who shows that Cu
substitutes for Ni in Ni3Al. This agrees with the data of [1985Mis]. [1985Li] examined an alloy containing
14.2Al-4.3Ni (mass%). At 900°C, only ( , Cu3Al) was observed; from 800 to 600°C ( ,Cu3Al)+ 1 coexist
and at 500°C (Ni,Cu)+ 1+( ,NiAl) are in equilibrium. This data agrees with results of [1938Ale].
[1988Ahm] reported that an alloy containing 14Al-10Ni (mass%) after heating to 350°C formed
(Ni,Cu)+ 1+( ,NiAl). This is in agreement with the 500°C section of [1948Koe] and the data of [1938Bra].
[1990Sun] reported that as-cast alloys 0.1-4.5Al86.4-90.7Cu9.1-9.7Ni (mass%) contained a martensite
phase, which transformed into equilibrium phases (Cu,Ni), 1 and the NiAl on tempering in the temperature
range 540-750°C. [1990Sun] also observed that Ni addition to Al-Cu pushes (Cu,Ni)/(Cu,Ni)+ 1 phase
boundary towards Al-end and the solubility of Ni in (Cu,Ni) increases with temperature. [1994Jia] reported
tie lines in the (Ni,Cu)+Ni3Al and Ni3Al+NiAl phase fields, occurring near the Al-Ni side of the system.
Samples were diffusion couples, annealed in sealed quartz capsules for 10-1000 h in the temperature range
800-1300°C and were subjected to microstructure as well as EPMA examination. [1998Pel] observed that
an alloy 3Ni-Cu-12Al (mass%) annealed at temperature greater than 415°C contained two phases consisting
of 1 and Cu-rich (Ni,Cu). [2001Liu] established tie lines in (Ni,Cu)+ 1 and ( 1+ ) phase fields, occurring
near the Al-Cu side of the system, at 700 and 800°C by preparing diffusion couples. EDS was used to
determine the phase compositions. [2003Wan] examined 112 water quenched samples prepared by
arc-melting and annealing in vacuum (10–3 torr) at 800°C for 30 days, using metallography, XRD and
EPMA. In three samples they observed NiAl coexisting as a separate phase with the disordered Cu-rich bcc
phase ( ,Cu3Al). They reported an isothermal section at 800°C with an unusual shape for the NiAl
phase-field.
Publication up to the year 1988 have been reviewed thoroughly by Alan Prince within the MSIT Evaluation
Program [1991Pri]. The present work proceeds with the evaluation, taking into account the new ternary and
edge binary data.
Binary Systems
Binary systems are accepted from the MSIT Binary Evaluation Program: Al-Cu from [2003Gro], Al-Ni
from [2003Sal] and Cu-Ni from [2002Leb].
Solid Phases
In addition to the solid phases associated with the binary systems a ternary phase region, designated in
Figs. 1, 3 to 5, has been well-established [1938Bra, 1948Koe, 1955Bow, 1956Bow, 1957Lu1, 1957Lu2,
1957Ray]. The definitive work is that of [1957Lu1, 1957Lu2]. They found 8 types of closely-related
structures of the phase; all show lines of the CsCl structure with superlattice reflections. The phase
structures are described as being based on the sequence of occupation of the cube centre position in the CsCl
lattice by heavy atoms (M = Cu or Ni) or by vacancies (V). Conventionally, the subscript of the notation i
is the number of layers in the unit cell. The 2 structure reported by [1955Bow, 1956Bow] is 5 of [1957Lu1,
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1957Lu2] and can be represented by the sequence (V)(M)(M)(M)(V) repeated, where M = Cu or Ni and V
= vacancy. The structure identified by [1955Bow, 1956Bow] is same as 8 of [1957Lu1, 1957Lu2]. It can
be represented by the sequence (V)(M)(M)(M)(M)(M)(M)(V) repeated. The region of homogeneity of
was originally determined by [1938Bra], Fig. 3. There is good agreement between this work and that of
[1948Koe], Fig. 4 and [1957Lu1, 1957Lu2], Fig. 5. [1957Lu1, 1957Lu2] also established the equilibrium
ranges of the different stacking variants of in this field (Fig. 5). [1957Ray] chemically extracted primary
crystals of from solidified melts and analyzed their compositions. Analyses were given for two crystals of
which the first lies within the phase region defined by [1938Bra, 1948Koe, 1957Lu1, 1957Lu2]; its
composition was 58Al-33.4Cu-8.6Ni (at.%). The second crystal contained 60.3Al-31.0Cu-8.7Ni (at.%) and
is within the phase region given by [1948Koe], just within the + region of [1938Bra] and on the / +
boundary of [1957Lu1, 1957Lu2].
Pseudobinary Systems
There are no pseudobinary sections in the system, though the section Cu3Al-NiAl may be treated as a
pseudobinary above 800°C (Fig. 14). This is discussed below in “Temperature-Composition Sections”.
Invariant Equilibria
The invariant equilibria associated with the liquid phase are given in Table 2. This table is an assimilation
of results from [1923Bin, 1928Nis, 1938Ale, 1940Rap, 1948Koe, 1952Han, 1982Ask], with amendments
to incorporate the Al-Cu phases that are known to be in equilibrium with the melt in the binary system.
Although [1923Aus] gave no ternary invariant reactions, re-interpretation of the original data, with the
benefit of the knowledge gained from later works, indicates the presence of an invariant reaction at ~ 600°C
which can be identified as reaction U5 in Table 2. [1923Bin] found an invariant transformation reaction at
585 ± 5°C; it would currently be equated with U7, Table 2. As [1948Koe] only recognized the ( ,Cu3Al),
, and phases from the Al-Cu system, the reaction they proposed for U2, L+ +NiAl, has been
changed to L+ 0 1+( ,NiAl) and the reaction at U4, L+NiAl + according to [1948Koe] has been
altered to L+( ,NiAl) 2+ . Reactions U3 and U6 are additional to those given by [1948Koe]. The reaction
scheme is given in Fig. 6. It takes no account of the 0 1, 1 2 and 1 2 transformation in the Al-Cu
binary system.
An important invariant equilibrium is the one concerned with the eutectoidal decomposition of ( ,Cu3Al)
in the ternary system. There is general agreement on the effect of Ni in raising the binary eutectoid
temperature from 559°C [1938Ale, 1941Tur, 1946Smi, 1954Hay, 1979Kuz]. At higher temperatures the tie
triangles (Ni,Cu)+( ,Cu3Al)+( ,NiAl) and 1+( ,Cu3Al)+( ,NiAl) exist. The formation of these tie
triangles originates with the occurrence of a solid-state miscibility gap in the ( ,Cu3Al)/( ,NiAl) solid
solution at below 800°C, whereby equilibrium is established between the disordered ( ,Cu3Al) phase and
the ordered ( ,NiAl) phase. The tie lines in this two-phase region lie in the direction Cu3Al-NiAl but do not
coincide with the binary compositions. The two-phase region coalesces with the (Ni,Cu)+( ,NiAl)
two-phase region and with the 1+( ,NiAl) two-phase region to produce the tie triangles. The two tie
triangles meet at about 600°C, defining the four phase plane representing the transition reaction
( ,Cu3Al)+( ,NiAl) 1+(Ni,Cu). As shown by [1954Hay] the composition of the ( ,Cu3Al) phase at
600°C lies near the (Ni,Cu)- 1 tie line. Below 600°C the (Ni,Cu)+ 1+( ,NiAl) equilibrium is established
and the ( ,Cu3Al)+(Ni,Cu)+ 1 tie triangle descends to the binary Al-Cu eutectoid reaction.
Liquidus and Solidus Surfaces
Figure 1 is the liquidus surface mainly based on the data from [1948Koe], but incorporating the data of
[1938Ale] for the Ni-Cu-Cu3Al-NiAl region, the data of [1957Ray] for the region of primary separation of
the phase and the amendments to provide consistency with the accepted binary phase diagrams. It shows
the dominating role played by the surface of primary separation of the phase. The liquidus projection
reported by [1940Rap] is not considered in view of major disagreement with other works. Figure 2 is the
solidus surface, primarily based on the data of [1938Ale].
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Isothermal Sections
Majority of the published isothermal sections concentrate on the region of the ternary system defined by
Cu-Cu3Al-NiAl-Ni. In this category, the major work has been reported by [1937Ale, 1938Ale, 1941Tur,
1945Tur, 1978Tho] and [1983Rud]. The remaining portion of the ternary system has been studied primarily
by [1938Bra] and [1948Koe], with contributions from [1952Haw, 1972Bed, 1983Rud, 1985Li, 1988Ahm,
2001Liu] and [2003Wan]. All isothermal sections are amended to match with the accepted binary systems.
Figure 3 summarizes the phase observations by [1938Bra] of slowly-cooled alloys. It approximately
corresponds to phase relations at 500°C. As mentioned in the section “Literature Data”, [1938Bra] did not
observe the phase, but found three variants of the phase. Figure 4 is the isothermal section at 500°C
based on diagrams given by [1938Ale] and [1948Koe]. It agrees fairly well with Fig. 3. The section includes
three tie triangles 1+ + , + 2+ , 2+ 2+ in place of the + + tie triangle shown by [1948Koe]. The
Ni5Al3 and Ni3Al4 phases, which were not observed by [1938Ale] and [1948Koe], are also included in the
diagram. At 500°C the equilibrium between (Ni,Cu), 1 and ( ,NiAl) is well-established [1938Ale,
1985Li]. Figure 7 is the isothermal section at about 600°C, based on the data from [1938Ale], [1948Koe]
and [1983Rud]. This section is very close to four phase invariant planes for reactions L+ 1 + (U8),
( ,NiAl)+ 1+Ni2Al3, 1+ 2 + , ( ,NiAl)+( ,Cu3Al) 1+(Ni,Cu) and L+Ni2Al3 (Al)+ (U7). It
should be noted that [1938Ale] did not detect the reaction of ( ,NiAl) and ( ,Cu3Al) in the 600°C
isothermal section. As discussed under “Invariant Equilibria” 600°C is accepted in this assessment as the
transition temperature. Figure 7 should be regarded as relating to a temperature slightly above 600°C. Figure
8 is the isothermal section at 700°C, based on studies by [1938Ale], [1941Tur], [1945Tur], [1948Koe],
[1983Rud] and [2001Liu]. The isothermal section at 700°C reported by [1948Koe] showed a continuous
solution phase, designated between ( ,Cu3Al) and ( ,NiAl). This is contrary to the findings of [1938Ale]
and [1941Tur], who observed a two-phase ( ,Cu3Al)+( ,NiAl) region. It is not clear how much study was
made of this part of the ternary system by [1948Koe]. According to the vertical sections reported by
[1938Ale] and [1941Tur] and isothermal sections at 700°C, there exists at this temperature a tie triangle
(Ni,Cu)+( ,Cu3Al)+( ,NiAl). The latter equilibrium is accepted, with modifications to obey the
Schreinemakers rule. There is an obvious need for a re-determination of the equilibria between the phases
( ,Cu3Al), 1 and ( ,NiAl) using alloys of a higher Al content than those examined by [1938Ale]. It should
be noted that [1948Koe] designated the 2 phase region as . The isothermal section at 800°C is shown in
Fig. 9. It is based on data from [1938Ale], [1983Rud], [2001Liu] and [2003Wan]. This isothermal section
is very close to the critical region corresponding to the demixing ( ,NiAl)+( ,Cu3Al). Therefore, two tie
triangles on either side of ( ,Cu3Al) phase region is shown as degenerated. According to the Al-Cu binary,
at this temperature there should be a very small region of 0 near the ( 1) phase field. It is omitted for the
sake of clarity. The 900°C isothermal section, Fig. 10, is based on data from [1938Ale], [1948Koe] and
[1983Rud]. It is above the region of demixing of the ( ) phase. As with the 700°C section, the phase
(reported by [1948Koe]) has been replaced by the ( 1) phase. Partial isothermal sections are reproduced for
550°C [1945Tur], Fig. 11; 650°C [1941Tur], Fig. 12; 1000°C [1941Tur], Fig. 13.
Temperature – Composition Sections
Vertical section through Cu3Al-NiAl is depicted in Fig. 14. It has been drawn on the basis of data provided
by the works of [1938Ale, 1941Tur, 1946Smi, 1954Hay, 1979Kuz]. Although [1938Ale] considered this
section to be pseudobinary throughout the temperature range, this is not accepted due the presence of the
three-phase regions associated with the invariant reaction ( ,NiAl)+( ,Cu3Al) 1+(Ni,Cu) at lower
temperatures. [1938Ale] regarded the ( ,Cu3Al)-( ,NiAl) tie line of the (Ni,Cu)+( ,Cu3Al)+( , NiAl) tie
triangle as lying on the plane of Cu3Al-AlNi section. [1941Tur], showed the Cu3Al-NiAl section as
intersecting the ( ,Cu3Al)+ 1+( ,NiAl) tie triangle. Also shown was a necessary ( ,Cu3Al)+ 1 phase
region. It would seem that there should be an order-disorder phase boundary between the disordered
( ,Cu3Al) and ordered ( ,NiAl) phases in what [1938Ale] reported as the solid solution series. The lower
part of this boundary would form a tri-critical point at about 800°C where phase separation occurs. In the
section on “Invariant Equilibria” the formation of the two triangles (Ni,Cu)+( ,Cu3Al)+( ,NiAl) and
1+( ,Cu3Al)+( ,NiAl) and the subsequent eutectoidal decomposition of ( ,Cu3Al) were discussed. It is
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concluded that the Cu3Al-NiAl section published by [1941Tur] is more probable than that reported by
[1938Ale]. Fig. 14 represents the preferred section.
Early work [1924Iit] on vertical sections at constant Ni contents in Cu-Ni rich alloys was superseded by
publications of [1938Ale, 1941Tur] and [1945Tur]. Sections at 4 mass% Al [1941Tur] and [1938Ale], 10Al
[1938Ale], 14Al [1938Ale], 3Ni [1938Ale], 4Ni [1945Tur], 6Ni [1938Ale] and [1941Tur], 8Ni [1945Tur],
10, 20, 40 and 60 mass% Ni [1938Ale] and sections Cu-Ni3Al and Cu-NiAl have been reported. The 4 and
10 mass% Al sections are given in Fig. 15 and Fig. 16, respectively. Sections at 6 and 60 mass% Ni are
reproduced in Fig. 17 and Fig. 18, respectively.
Thermodynamics
A direct determination of the enthalpy of formation of ternary alloys was made by [1937Koe]. Isoenthalpy
curves relating to the as-cast condition, i.e. non-equilibrium, were given. Alloying of Al-Ni with Cu lowers
the enthalpy of formation. [1975Hen] determined precisely by solution calorimetry the enthalpy of
formation of the ( ,NiAl) phase as a function of concentration and with addition of Cu. [1993Sto] measured
enthalpy of mixing of liquid Al-Cu-Ni alloys at 1427°C along eight isopleths using a high-temperature
mixing calorimeter. An analysis of the data by [2000Wit] revealed that the enthalpy of mixing has a
minimum at -42.8 kJ mol-1 corresponding to the stoichiometry Ni45Cu10Al45.
Miscellaneous
Extensive data have been reported on the lattice parameters of the (Al) phase [1952Han] and the (Ni,Cu)
phase [1938Bra, 1936Gri1] and [1941Tur]. The effect of Cu additions on the structure of NiAl was studied
by [1939Lip]. The number of atoms in the unit cell decreases across the ( ,NiAl) phase region as the Al
content increases. Vacant lattice sites are formed on the Al-rich side of the NiAl stoichiometry. [1971Jac]
measured the lattice spacings in the ( ,NiAl) phase along sections from 16.67Cu-83.33Ni (at.%) to Al and
8.33Cu-91.67Ni (at.%) to Al and on the 50 at.% Al section. Alloys were annealed 7 days at 1050°C and
cooled to room temperature at a rate of 100 K/h. [1985Mis] examined the effect of Cu additions on the
lattice parameter of Ni3Al at a constant Al content of 25 at.%. The lattice parameter was increased by Cu
up to the 15 at.% Cu limit studied. This finding agrees with data summarized by [1984Och]. Magnetic
properties of the (Ni,Cu) phase along the 77 and 87 at.% Ni sections were determined for alloys quenched
from 1100°C by [1983Lup]. The Curie temperature of alloys on a section from Ni towards 25Al-75Cu
(at.%) were studied by [1952Mar]. A linear decrease in Curie temperature from 361°C at Ni to 90°C at 20
at.% Al+Cu was observed.
References
[1923Aus] Austin, C.R., Murphy, A.J., “The Ternary System Cu-AlNi”, J. Inst. Met., 29, 327-367
(1923) (Equi. Diagram, Experimental, 19)
[1923Bin] Bingham, K.E., Haughton, J.L., “The Constitution of Some Alloys of Al with Cu and Ni”,
J. Inst. Met., 29, 71-112 (1923) (Equi. Diagram, Experimental, 13)
[1924Iit] Iitaka, I., “Investigation of the Ternary Cu-Al-Ni System” (in Japanese), Tetsu to Hagane,
10, 1-32 (1924) (Equi. Diagram, Experimental)
[1928Nis] Nishimura, H., “Investigations of Al-Base Al-Cu-Ni Alloys” (in Japanese), Suiyokwai-Shi,
5, 616-626 (1928) (Equi. Diagram, Experimental, 3)
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1936Gri1] Gridnev, V., Kurdjumov, G., “The Influence of Ni on the Solubility Limits of the -Phase
in Cu-Al Alloys” (in German), Metallwirtschaft, 15, 229-231, 256-259 (1936) (Crys.
Structure, Equi. Diagram, Experimental, 6)
[1936Gri2] Gridnev, V., Kurdjumov, G., “The Effect of a Third Element on the Aging of Binary
Systems. Cu-Al-Ni System” (in Russian), Teor. Prakt. Metall., (2), 100-109 (1936) (Crys.
Structure, Equi. Diagram, Experimental, 1)
110
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
[1937Ale] Alexander, W.O., Hanson, D., “Cu-Rich Ni-Al-Cu Alloys. Part 1. The Effect of
Heat-Treatment on Hardness and Electrical Resistivity”, J. Inst. Met., 61, 83-99 (1937)
(Experimental, 8)
[1937Koe] Koerber, F., Oelsen, W., Lichtenberg, H., “On the Thermochemistry of Alloys. II. Direct
Determination of the Heat of Formation of Ternary Alloys of the System Fe-Ni-Al,
Fe-Co-Al, Cu-Ni-Al, Fe-Al-Si, as well as Certain Alloys of the Cu-Mn-Al System” (in
German), Mitt. K.-W.-Inst. Eisenforschung, 19, 131-159 (1937) (Experimental,
Thermodyn., 50)
[1938Ale] Alexander, W.O., “Cu-Rich Ni-Al-Cu Alloys. Part II. The Constitution of the Cu-Ni-Rich
Alloys”, J. Inst. Met., 63, 163-183 (1938) (Crys. Structure, Equi. Diagram,
Experimental, 14)
[1938Bra] Bradley, A.J., Lipson, H. “An X-Ray Investigation of Slowly Cooled Cu-Ni-Al Alloys”,
Proc. Roy. Soc., 167A, 421-438 (1938) (Crys. Structure, Equi. Diagram, Experimental, 13)
[1939Lip] Lipson, H., Taylor, A., “Defect Lattices in Some Ternary Alloys”, Proc. Roy. Soc., 173A,
232-237 (1939) (Crys. Structure, Experimental, 8)
[1940Bra] Bradley, A.J., Bragg, W.L., Sykes, C., “Researches Into the Structure of Alloys”, J. Iron
Steel Inst., London, 141, 104-163 (1940) (Crys. Structure, Equi. Diagram, Experimental,
Review, 61)
[1940Rap] Rapp, A., “The Al Corner of the Ternary System Al-Cu-Ni” (in German), Alum. Arch., (28),
1-17 (1940) (Crys. Structure, Equi. Diagram, Experimental, 9)
[1941Tur] Turkin, V.D., “Investigation of Alloys of the Cu-Ni-Al System” (in Russian), Tsvetn. Met.,
17, 26-34 (1941) (Crys. Structure, Equi. Diagram, Experimental, 11)
[1945Tur] Turkin, V.D., “Investigation of Alloys of the Cu-Ni-Al System” (in Russian), Struk. Legkih
Splavov Tsvetnikh Metallov, 5-21 (1945) (Crys. Structure, Equi. Diagram, Experimental,
33)
[1946Smi] Smiryagin, A.P., “Boundaries of the Solid Solution Phase in the Cu-Al-Ni System” (in
Russian), Izv. Sekt. Fiz.-Khim. Anal., 16, 180-196 (1946) (Equi. Diagram, Experimental, 40)
[1948Koe] Koester, W., Zwicker, U., Moeller, K., “Microscopic and X-Ray Studies Towards the
Understanding of the Cu-Ni-Al System” (in German), Z. Metallkd., 39, 225-231 (1948)
(Crys. Structure, Equi. Diagram, Experimental, 10)
[1952Han] Hanemann, H., Schrader, A., “Al-Cu-Ni”, in “Ternary Alloys of Al”, Atlas
Metallographicus, Verlag Stahleisen M.B.H., Duesseldorf, 3(2), 85-90 (1952) (Crys.
Structure, Equi. Diagram, Review, 3)
[1952Haw] Haworth, J.B., Hume-Rothery, W., “The Effect of Four Transition Metals on the / Brass
Type of Equilibrium”, Philos. Mag., 43, 613-629 (1952) (Equi. Diagram, Experimental, 23)
[1952Mar] Marian, V., Maxim, I., Tintea, M., “Curie Points for Ni-Cu-Al Solid Solutions. Preliminary
Note” (in Romanian), Comm. Acad. Rep. Populare Romine, Fiz., 11, 527-531 (1952)
(Experimental, 0)
[1954Hay] Haynes, R., “Isothermal Transformations of Eutectoid Al Bronzes”, J. Inst. Met., 83,
105-114 (1954) (Experimental, 23)
[1955Bow] Bown, M.G., “The Crystal Structures of Certain Metallic Phases”, Thesis, Univ. Cambridge,
289 (1955) (Crys. Structure, Experimental, 116)
[1956Bow] Bown, M.G., “The Structure of Rhombohedral T(NiCuAl)”, Acta Crystallogr., 9, 70-74
(1956) (Crys. Structure, Experimental, 9)
[1957Lu1] Lu, S.S., Chang, T., “Systematic Structure Changes in a Single-Phase Field - an
Extraordinary Phenomenon Observed in Al-Cu-Ni Alloys”, Sci. Rec., Peking, 1, 41-44
(1957) (Crys. Structure, Experimental, 3)
[1957Lu2] Lu, S.S., Chang, T., “Crystal Structure Changes in the J-Phase of Al-Cu-Ni Alloys” (in
Chinese), Acta Phys. Sin. (Chin. J. Phys.), 13, 150-178 (1957) (Crys. Structure, Equi.
Diagram, Experimental, 12)
[1957Ray] Raynor, G.V., Ward, B.J., “Al-Rich Alloys of the Quarternary System Al-Fe-Cu-Ni”,
J. Inst. Met., 86, 135-144 (1957-1958) (Equi. Diagram, Experimental, 20)
111
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
[1961Phi] Phillips, H.W.L., “Al-Cu-Ni”, in “Equilibrium Diagrams of the Al-Alloy Systems”,
Information Bulletin 25, Aluminium Development Association, London, 67-69 (1961)
(Review, 3)
[1971Jac] Jacobi, H., Engell, M.J., “Defect Structure in Non-Stoichiometric -(Ni,Cu)Al”, Acta
Metall., 19, 701-711 (1971) (Crys. Structure, Experimental, Theory, 19)
[1972Bed] Bedel'baev, G.E., Begimov, T.B., Melikhov, V.D., Presnyakov, A.A., Ashirimbetov, Yh.A.,
“Study of the Structure of the Compound Cu9Al4 With Ni Additions” (in Russian), Prikl.
Teor. Fiz., (3), 276-281 (1972) (Crys. Structure, Experimental, 4)
[1975Hen] Henig, E.-Th., Lukas, H.L., “Calorimetric Determination of the Enthalpy of Formation and
Description of the Defect Structure of the Ordered -Phase (Ni,Cu)1-xAlx” (in German),
Z. Metallkd., 66, 98-106 (1975) (Thermodyn., Experimental, 22)
[1978Tho] Thomson, R., Edwards, J.O., “The P Phase in Ni-Al Bronzes. I. Slow-Cooled
Microstructures”, Amer. Foundrymen's Soc. 82nd Annual Conf. Detroit, Mich., 385-394
(1978) (Equi. Diagram, Experimental, 23)
[1979Kuz] Kuznetsov, G.M., Fedorov, V.N., Nikonova, I.V., Trofimova, E.A., “Investigation of the
Cu-Ni-Al System” (in Russian), Izv. Vyss. Uchebn. Zaved., Tsvetn. Metall., (4), 98-100
(1979) (Equi. Diagram, Experimental, Thermodyn., 6)
[1982Ask] Askarov, M.S., Smagulov, D.U., Omarov, A.K., “Study of the Phase Diagram, Phase
Composition and Alloy Structure in the Al-Ni-Cu System” (in Russian), Vopr. Teo. Prakt.
Per. Syr. Prod. Tsv. Met. Kaz., 98-103 (1982) (Equi. Diagram, Experimental, 11)
[1983Haf] Hafez, H.A., Taha, M.A., El-Sabagh, A.S., “The Microstructure of Al-Rich Al-Cu-Ni
Alloys”, Prakt. Metallogr., 20, 507-533 (1983) (Experimental, Crys. Structure, 14)
[1983Lup] Lupsa, I., Burzo, E., “Magnetic Properties of NiCuAl Solid Solutions”, J. Magn. Magn.
Mater., 37, 147-154 (1983) (Experimental, Magn. Prop., 34)
[1983Rud] Rudolph, G., “Microprobe Measurements to Determine Phase Boundaries and Diffusion
Paths in Ternary Phase Diagrams taking a Cu-Ni-Al System as an Example”, Mikrochimica
Acta, Suppl., 10, 241-251 (1983) (Equi. Diagram, Experimental, 8)
[1984Hus] Husain, S.W., Clapp, P.C., Ahmed, M., “Phase Transformations on Aging
Copper-Aluminum-Nickel Phase Alloys”, Mater. Res. Soc. Symp. Proc., 21, 729-734
(1984) (Crys. Structure, Experimental, 15)
[1984Och] Ochiai, S., Mishima, Y., Suzuki, T., “Lattice Parameters of Ni( ), Ni3Al( ') and Ni3Ga( ')
Solid Solutions”, Bull. P.M.E., (53), 15-28 (1984) (Crys. Structure, Experimental, 66)
[1985Li] Li, S., Sum, X., Qian, C., “X-Ray Diffraction Analysis of the Martensitic Transformation in
Cu-Ni-Al Alloy” (in Chinese), J. Cent.-South Inst. Min. Metall. (China), (1), 71-77 (1985)
(Crys. Structure, Experimental, 11)
[1985Mis] Mishima, Y., Ochiai, S., Suzuki, T., “Lattice Parameters of Ni( ), Ni3Al( ') and Ni3Ga( ')
Solid Solutions With Additions of Transition and B-Sub Group Elements”, Acta Metall., 33,
1161-1169 (1985) (Crys. Structure, Experimental, 64)
[1985Mur] Murray, J.L., “The Aluminium-Copper System”, Int. Met. Rev., 30, 211-233 (1985) (Equi.
Diagram, Review, #, 230)
[1988Ahm] Ahmed, M., Husain, S.W., Iqbal, Z., Hashmi, F.H., Khan, A.Q., “Phase Transformations in
Rapidly Solidified Cu-Al-Ni Phase Alloys”, Scr. Metall., 22, 803-808 (1988)
(Experimental, 11)
[1989Ell] Ellner, M., Kek, S., Predel, B., “Ni3Al4 - A Phase with Ordered Vacancies Isotypic to
Ni3Ga4”, J. Less-Common Met., 154(1), 207-215 (1989) (Experimental, Crys. Structure, 26)
[1989Mee] Meetsma, A., de Boer, J.L., van Smaalen, S., “Refinement of the Crystal Structure of
Tetragonal Aluminum-Copper (Al2Cu)”, J. Solid State Chem., 83(2), 370-372 (1989) (Crys.
Structure, Experimental, 17)
[1990Sun] Sun, Y.S., Lorimer, G.W., Ridley, N., “Microstructure and its Development in Cu-Al-Ni
Alloys”, Metall. Trans., 21A, 575-588 (1990) (Experimental, 16)
112
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
[1990Ye] Ye, J., Tokonami, M., Otsuka, K., “Crystal Structure Analysis of 1' Cu-Al-Ni Martensite
Using Conventional X-Ray and Synchrotron Radiations”, Metall. Trans., 21A, 2669-2678
(1990) (Calculation, Crys. Structure, Experimental, 37)
[1991Pri] Prince, A., ”Aluminium - Copper - Nickel”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.12729.1.20, (1991) (Crys. Structure, Equi. Diagram,
Assessment, 43)
[1993Sto] Stolz, U.K., Arpshofen, I., Sommer, F., “Determination of the Enthalpy of Mixing of Liquid
Aluminium-Copper-Nickel Ternary Alloys”, Z. Metallkd., 84, 552-556 (1993) (Calculation,
Equi. Diagram, Experimental, Thermodyn., 8)
[1994Jia] Jia, C.C., Ishida, K., Nishizawa, T., “Partition Of Alloying Elements Between (A1),
'(L12) and (B2) Phases in Ni-Al Base Systems”, Metall. Mater. Trans., 25A, 473-485
(1994) (Crys. Structure, Equi. Diagram, Experimental, 25)
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)”, in “Phase Diagrams of Binary Copper
Alloys”, Subramanian,. P.R., Chakrabarti,. D.J., Laughlin, D.E (Eds.), ASM International,
Materials Park, OH, 18-42 (1994) (Equi. Diagram, Crys. Structure, Thermodyn., Review, #,
*, 226); similar to [1985Mur]
[1996Pau] Paufler, P., Faber, J., Zahn, G., “X-Ray Single Crystal Diffraction Investigation on
Ni1+xAl1-x”, Acta Crystallogr., Sect. A: Found. Crystallogr., A52, C319 (1996) (Crys.
Structure, Experimental, Abstract, 3)
[1996Vik] Viklund, P., Häußermann, U., Lidin, S., “NiAl3: A Structure Type of its Own”, Acta
Crystallogr., Sect. A: Found. Crystallogr., A52, C-321 (1996) (Crys. Structure,
Experimental, Abstract, 0)
[1997Bou] Bouche, K., Barbier, F., Coulet, A., “Phase Formation During Dissolution of Nickel in
Liquid Aluminium”, Z. Metallkd., 88(6), 446-451 (1997) (Thermodyn., Experimental, 15)
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264, 201-208 (1998) (Equi. Diagram,
Experimental, #,*,25)[1998Pel] Pelosin, V., Riviere, A., “Structural and Mechanical Spectroscopy Study of the 1’
Martensite Decomposition in Cu-12% Al-3% Ni (wt.%) Alloy”, J. Alloys Compd., 268,
166-172 (1998) (Crys. Structure, Experimental, Mechan. Prop., 10)
[1998Rav] Ravelo, R., Aguilar, J., Baskes, M., Angelo, J.E., Fultz, B., Holian, B.L., “Free Energy and
Vibrational Entropy Difference between Ordered and Disordered Ni3Al”, Phys. Rev. B,
57(2), 862-869 (1998) (Thermodyn., Theory, Calculation, 43)
[2000Wit] Witusiewicz, V.T., Arpshofen, I., Seifert, H.-J., Sommer, F., Aldinger, F.,
“Thermodynanmics of Liquid and Undercooled Liquid Al-Cu-Ni-Si Alloys”, Thermochim.
Acta, 356, 39-57 (2000) (Calculation, Experimental, Thermodyn., 41)
[2001Liu] Liu, X.J., Wang, C.P., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Stability Among the
(A1), (A2) and (D83) Phases in the Cu-Al-X System”, J. Phase Equilib., 22, 431-438
(2001) (Equi. Diagram, Experimental, 14)
[2001Mot] Motoyasu, G., Kaneko, M., Soda, H., McLean, A., “Continuously Cast Cu-Al-Ni Shape
Memory Wires with a Unidirectinal Morphology”, Metall. Mater. Trans., 32A, 585-593
(2001) (Crys. Structure, Equi. Diagram, Experimental, Phys. Prop., 15)
[2002Gul] Gulay, L.D, Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. “Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Leb] Lebrun, N., “Cu-Ni (Copper-Nickel)”, MSIT Binary Evaluation Program,in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 20.14832.1.20, (2002) (Crys. Structure, Equi. Diagram,
Assessment, 51)
113
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Al–Cu–Ni
[2003Gro] Gröbner, J., “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 68)
[2003Sal] Saltykov, P., Cornish, L., Cacciamani, G., “Al-Ni (Aluminium-Nickel)”, MSIT Binary
Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science
International Services GmbH, Stuttgart; to be published, (2003) (Crys. Structure, Equi.
Diagram, Assessment, 164)
[2003Wan] Wang, C-H., Chen, S-W., Chang, C-H., Wu, J-C., “Phase Equilibria of the Ternary
Al-Cu-Ni System and Interfacial Reactions of Related System at 800°C”, Metall. Mater.
Trans. A, 34A, 199-209 (2003) (Equi. Diagram, Experimental, 30)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Ni1-x,Cux)
Ni
< 1455
Cu
< 1084.62
cF4
Fm3m
Cu
a = 352.40
a = 361.46
0 < x < 1
at 25°C [Mas2]
at 25°C [Mas2]
melting point [1994Mur]
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
NiAl3< 856
oP16
Pnma
NiAl3oP16
Pnma
Fe3C
a = 661.3 ± 0.1
b = 736.7 ± 0.1
c = 481.1 ± 0.1
a = 659.8
b = 735.1
c = 480.2
[1996Vik]
[1997Bou, V-C]
Ni2Al3< 1138
hP5
P3m1
Ni2Al3
a = 402.8
c = 489.1
59.5 to 63.2 at.% Al [Mas]
[1997Bou, V-C]
Ni3Al4< 702
cI112
Ia3d
Ni3Ga4
a = 1140.8 ± 0.1 [1989Ell, V-C]
( ,NiAl)
< 1651
cP2
Pm3m
CsCl
a = 288.72 ± 0.02 at 50 at.% Ni [1996Pau].
In the ternary this phase forms a
continuous series of solid solution with
,Cu3Al above 800°C.
[1938Ale, 1941Tur]
Ni5Al3< 723
oC16
Cmmm
Pt5Ga3
a = 744
b = 668
c = 372
32 to 36 at.% Al [Mas] [V-C]
Ni3Al
< 1372
cP4
Pm3m
Cu3Au
a = 357.92
24 to 27 at.% Al [Mas2]
[1998Rav]
114
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
, ( , Cu3Al)
1049-559
cI2
Im3m
W
a = 295.64
70.6 to 82 at.% Cu, [1985Mur, 1998Liu]
at 672°C in +(Cu) alloy.
In the ternary this phase forms a
continuous series of solid solution with
( ,NiAl) above 800°C.
[1938Ale, 1941Tur]
2, Cu1-xAlx< 363
~TiAl3long period
superlattice
a = 366.8
c = 368.0
0.22 x 0.235 [Mas, 1985Mur]
at 76.4 at.% Cu
(subcell only)
0, Cu1-xAlx1037-800
cI52
I43m
Cu5Zn8
- 0.31 x 0.402 [Mas2]
32 to 38 at.%Al, [1998Liu]
1, Cu9Al4< 890
cP52
P43m
Cu9Al4
a = 870.68
a = 871.32
at 33.8 at.% Al, [V-C] from single
crystal [V-C]
, Cu1-xAlx< 686
hR*
R3m a = 1226
c = 1511
0.38.1 x 0.407 [Mas2, 1985Mur]
at x = 38.9 [V-C]
1, Cu1-xAlx958-848
c**? - 0.379 x 0.406
[Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.47 x 0.78
55.0 to 61.1 at.% Cu
[Mas, 1985Mur, V-C2]
NiAs in [Mas2, 1994Mur]
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2
Cu47.8Al35.5
a = 812
b = 1419.85
c = 999.28
55.2 to 59.8 at.% Cu, [Mas2, 1994Mur]
structure: [2002Gul]
2, Cu11.5Al9(r)
< 570
oI24 - 3.5
Imm2
Cu11.5Al9
a = 409.72
b = 703.13
c = 997.93
55.2 to 56.3 at.% Cu, [Mas2, 1985Mur]
structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]
Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu
[V-C2]
, CuAl2< 591
tI12
I4/mcm
CuAl2
a = 606.3
c = 487.2
31.9 to 33.0 at.% Cu [1994Mur]
Single crystal
[V-C2, 1989Mee]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
115
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
a) The i phases are stacking variants in the range assigned to a single phase by other authors. They are derived
from the CsCl structure with ordered vacancies (V) on the (Ni,Cu) sublattice (occupied sites designated by M).
i is the number of layers per unit cell.
Table 2: Invariant Equilibria
* a5, (Ni,Cu)3Al5
11, (Ni,Cu)6Al11
6, (Ni,Cu)4Al6
13, (Ni,Cu)8Al13
7, (Ni,Cu)5Al7
15, (Ni,Cu)10Al15
8, (Ni,Cu)6Al8
17, (Ni,Cu)12Al17
hR8
(Ni,Cu)3Al5(pseudo?) cubic
hP51
(Ni,Cu)6Al11
hP30
(Ni,Cu)4Al6hR21
(Ni,Cu)8Al13
hP36
(Ni,Cu)5Al7hP75
(Ni,Cu)10Al15
hR14
(Ni,Cu)6Al8hP87
(Ni,Cu)12Al17
a = 411.19
c = 2512.5
a = 1460
a = 411.41
c = 5528.9
a = 411.32
c = 3013.5
a = 411.33
c = 6517.3
a = 410.62
c = 3493.8
a = 409.58
c = 7464.5
a = 410.45
c = 3985.0
a = 410.5 ± 0.01
c = 3997 ± 0.01
a = 410.14
c = 8449.9
stacking sequence VMMMV [1957Lu2]
[1955Bow, 1956Bow]
stacking sequence
VMMMVVVMMMV [1957Lu2]
stacking sequence VMMMMV
[1957Lu2]
stacking sequence
VMMMMVVVMMMMV [1957Lu2]
stacking sequence VMMMMMV
[1957Lu2]
stacking sequence
VMMMMMVVVMMMMMV
[1957Lu2]
stacking sequence VMMMMMMV
[1957Lu2] [1955Bow, 1956Bow]
stacking sequence VMMMMMMVVV-
MMMMMMV [1957Lu2]
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Ni
L + Ni3Al (Ni,Cu) + 1250 U1 L 20 40 40
L+ 0 1 + a) ~ 880 U2 L
0
1
48
37
48
40
50
58
40
59
2
5
12
1
L + 1 2 + ? U3
L + + Ni2Al3 ~ 820 P L
Ni2Al3
64
57
60
62
32
24
23
28
4
19
17
10
L + 2 + b) ~ 650 U4 L
2
63
30
49
59
36
40
50
34
1
30
1
7
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
116
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
a) L + + NiAl according to [1948Koe] b) L + NiAl + according to [1948Koe]
L + NiAl3 (Al) + Ni2Al3 630 U5 L
NiAl3(Al)
Ni2Al3
90
74
99.6
62
8
1
0.2
14
2
25
0.2
24
L + 2 + ? U6
L + Ni2Al3 (Al) + ~ 590 U7 L
Ni2Al3(Al)
88
62
98.7
62
11
21
1.1
27
1
17
0.2
11
L + + 585 U8 L 67
50.2
66.5
59
32
49
33
37
1
0.8
0.3
4
L (Al) + + 546 E L
(Al)
82.3
98.3
67.6
64
17.1
1.5
32.1
29
0.6
0.2
0.3
7
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Ni
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
e2
p3
p4
p5
e
p7
p6
e4
e3
p2
e1p1
U1
U2
U3
U4
U8
P
E
U5
U6
(Al)NiAl3
Ni2Al3
β
(Ni,Cu)
β,NiAl
β,Cu3Al
γ0
ε2
η1
1400
1300 12001100
1600
1500
1400
1300
800
9001000
700
U7
ε1
11001200
Ni3Al
τθ
Fig. 1: Al-Cu-Ni.
Liquidus surface
117
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
(β,NiAl)
(β,Cu3Al)
(Ni,Cu)
1050
11001200
1250
13001400
1200
1250
1400
1500
1600
Ni3Al
Fig. 2: Al-Cu-Ni.
Solidus surface for
Cu-Ni rich alloys
[1938Ale]
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
(Ni,Cu)
Ni3Al
Ni5Al3
(β,NiAl)
Ni2Al3
NiAl3
(Al)
η2
ζ2
γ1
τ
θNi3Al4
δ
Fig. 3: Al-Cu-Ni.
Constitution of slowly
cooled alloys, after
[1938Bra]
118
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
(Ni,Cu)
Ni3Al
Ni5Al3
(β,NiAl)
Ni2Al3
(Al)
θ
η2
ζ2
δγ
1
τ
NiAl3
Ni3Al4
Fig. 4: Al-Cu-Ni.
Isothermal section at
500°C [1948Koe]
10
20
30 40
60
70
Ni 30.00Cu 20.00Al 50.00
Ni 0.00Cu 50.00Al 50.00
Ni 0.00Cu 20.00Al 80.00 Data / Grid: at.%
Axes: at.%
τ
τ5
τ11
τ6
τ13
τ7
τ15
x τ8
* τ17
xx
* **
Fig. 5: Al-Cu-Ni.
Extent of phase
region and
distribution of
stacking variants
[1957Lu1, 1957Lu2]
119
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
Fig
. 6a:
A
l-C
u-N
i. T
he
reac
tion s
chem
e, p
art
1
Al-
Ni
Al-
Cu
Al-
Cu
-Ni
lβ
+ N
i 3A
l
13
69
e 1
L +
γε 1
+β
ca.
88
0U2
l +
(N
i)
Ni 3
Al
13
72
p1
L+
Ni 3
Al
(N
i,C
u)
+ β
12
50
U1
l +
Ni 2
Al 3
NiA
l 3
85
6p5
β +
Ni 3
Al
Ni 5
Al 3
72
3p
l (
Al)
+ N
iAl 3
64
4e 3
l +
β N
i 2A
l 3
11
38
p2
γ +
ε 1ε 2
85
0p
l +
γε 1
95
8p4
l (
Cu
) + β
10
32
e 2
l +
βγ
10
37
p3
γ +
ε2
δ6
86
p
ε 1l
+ ε2
84
8e
L +
βε 2
+ τ
ca.
65
0U4
L +
ε1
ε 2 +
βU3
L+
β +
Ni 2
Al 3
τca
. 8
20
P
L+
NiA
l 3(A
l)+
Ni 2
Al 3
63
0U5
ε 1ε 2
+ γ
+ β
E
L+
γ +
β
Ni 3
Al
+ (
Ni,
Cu)
+ β
γ +
ε 1+
βL
+ ε 1
+ β
L +
τ +
Ni 2
Al 3
β +
Ni 2A
l 3 +
τ
β +
Ni 3
Al
+ N
i 5A
l 3
L+
τ +
β
L+
ε 2+
βε 1
+ ε2 +
β
NiA
l 3 +
(A
l) +
Ni 2
Al 3
L +
(A
l) +
Ni 2
Al 3
L+
ε 2 +
τ
β +
ε 2+
τε 2 +
γ +
β
β,C
u3A
l+β,
NiA
l+(N
i,C
u)
β,C
u3A
l+β,
NiA
l+γ
ca.
80
0
γ +
ε 2 +
δ
120
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Ni
Fig
. 6b
:
Al-
Cu
-Ni.
The
reac
tion s
chem
e, p
art
2
Al-
Ni
Al-
Cu
Al-
Cu
-Ni
l +
ε2
η6
24
p6
L +
ε2
η +
τU6
L +
ητ
+ θ
58
5U8
L +
Ni 2
Al 3
(A
l) +
τ5
90
U7
β,C
u3A
l+β,
NiA
lγ+
(Ni,
Cu)
ca.
60
0U
ε 2 +
β
γ +
τ6
20
U
ε 2 +
ηζ
+ τ
U
τ +
β γ
+ N
i 2A
l 3ca
. 5
80
U
ε 2
τ +
ζ +
δE
L (
Al)
+ θ
+ τ
54
6E
ε 2
δ +
ζ5
60
e
ε 2+
ηζ
59
0p
l +
ηθ
59
1p7
β (
Cu)
+ γ
55
9e
l (
Al)
+ θ
548.2
e 4
γ +
ε 2
τ +
δU
L+
τ+N
i 2A
l
3L
+ ε 2
+ τ
ε 2 +
γ +
β
β +
ε 2 +
τ
L+
(Al)
+N
i 2A
l 3L+
η +
τβ,
Cu3A
l+β,
NiA
l+γ
β,C
u3A
l+β,
NiA
l+(N
i,C
u)
β,N
iAl+
γ+(N
i,C
u)
β +
γ +
τ
ε 2+
γ +
τ
β +
Ni 2
Al 3
+τ
γ +
ε 2+
δε 2
+ η
+ τ
γ +
τ +
δε 2
+ τ
+ δ
ε 2 +
ζ +
τη
+ ζ
+ τ
τ +
ζ +
δ
β +
γ +
Ni 2
Al 3
τ +
γ +
Ni 2
Al 3
L+
τ +
θ
η +
τ +
θN
i 2A
l 3+
(A
l) +
τ
L +
(A
l) +
τ
(Al)
+ θ
+ τ
121
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
(Ni,Cu)
(β,Cu3Al)
γ1
δ
ε2
η1
L
(Al)
NiAl3
Ni2Al3
τ
(β,NiAl)
Ni3Al4
Ni3Al
Ni5Al3
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
(Ni,Cu)
β
γ1
ε2
L
NiAl3
Ni2Al3
(β,NiAl)
τ
Ni5Al3
Ni3Al
Ni3Al4
Fig. 7: Al-Cu-Ni.
Isothermal section at
approximately 600°C
[1948Koe]
Fig. 8: Al-Cu-Ni.
Isothermal section at
700°C [1948Koe]
122
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
L
ε2
(Ni,Cu)
(β,Cu3Al)
γ1
Ni2Al3
NiAl3
(β,NiAl)
Ni3Al
τ
β
20
40
60
80
20 40 60 80
20
40
60
80
Ni Cu
Al Data / Grid: at.%
Axes: at.%
L
ε1
(Ni,Cu)
(β,Cu3Al)
γ0
β(β,NiAl)
Ni2Al3
Ni3Al
Fig. 9: Al-Cu-Ni.
Isothermal section at
800°C
Fig. 10: Al-Cu-Ni.
Isothermal section at
900°C
123
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
10
20
30
40
60 70 80 90
10
20
30
40
Ni 50.00Cu 50.00Al 0.00
Ni 0.00Cu 50.00Al 50.00 Data / Grid: at.%
Axes: at.%
γ1γ
1+(Ni,Cu)+(β,NiAl)
(Ni,Cu)+(β,NiAl)
(Ni,Cu)(Ni,Cu)+Ni3Al
Cu
10
20
30
40
60 70 80 90
10
20
30
40
Ni 50.00Cu 50.00Al 0.00
Ni 0.00Cu 50.00Al 50.00 Data / Grid: at.%
Axes: at.%
γ1
(β,Cu 3Al)
(Ni,Cu)+(NiAl)
(Ni,Cu)(Ni,Cu)+Ni3Al
γ1+(β,Cu3Al)
Cu
Fig. 11: Al-Cu-Ni.
Cu-Ni rich isothermal
section at 550°C
[1945Tur]
Fig. 12: Al-Cu-Ni.
Cu-Ni rich isothermal
section at 650°C
[1941Tur]
124
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Ni
10
20
30
40
60 70 80 90
10
20
30
40
Ni 50.00Cu 50.00Al 0.00
Ni 0.00Cu 50.00Al 50.00 Data / Grid: at.%
Axes: at.%
(Ni,Cu)
β
γ0
(Ni,Cu)+β
(Ni,Cu)+Ni3Al
Cu
40 20500
750
1000
1250
1500
Ni 50.00Cu 0.00Al 50.00
Ni 0.00Cu 75.00Al 25.00Ni, at.%
Tem
pera
ture
, °C
β
disorderedordered(β,Cu3Al)(β,NiAl)
(β,Cu3Al)
L
β+γ1
+(β,NiAl)
(Ni,Cu)+γ1
600
1049°C
1651°C
Fig. 13: Al-Cu-Ni.
Cu-Ni rich isothermal
section at 1000°C
[1941Tur]
Fig. 14: Al-Cu-Ni.
The NiAl-Cu3Al
section
125
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ni
20 40 60 80500
750
1000
Ni 91.70Cu 0.00Al 8.30
Ni 0.00Cu 91.10Al 8.90Cu, at.%
Tem
pera
ture
, °C
(Ni,Cu)
Ni3Al+(Ni,Cu)
(β,NiAl)+(Ni,Cu)
(Ni,Cu)+Ni3Al+(β,NiAl)
20 40 60500
750
1000
1250
1500
Ni 80.50Cu 0.00Al 19.50
Ni 0.00Cu 79.30Al 20.70Cu, at.%
Tem
pera
ture
, °C
(Ni,Cu)
Ni3Al+(Ni,Cu)
(β,NiAl)(Ni,Cu)+(β,NiAl)
(Ni,Cu)+γ1
(Ni,Cu)
L+(β,NiAl)
L+(Ni,Cu) L
1250
600
+(β,NiAl)+Ni3Al
Fig. 15: Al-Cu-Ni.
Vertical section at 4
mass% Al
Fig. 16: Al-Cu-Ni.
Vertical section at 10
mass% Al
126
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Ni
10 20400
500
600
700
800
900
1000
1100
Ni 6.50Cu 93.50Al 0.00
Ni 5.40Cu 65.40Al 29.20Al, at.%
Tem
pera
ture
, °C
(Ni,Cu) (β,Cu3Al)
(Ni,Cu)
(β,Cu3Al)+γ1
γ1+(Ni,Cu)+(β,NiAl)
(Ni,Cu)+Ni3Al
(Ni,Cu)+(β,Cu3Al)
+(β,Cu3Al)
+(β, NiAl)
(β,Cu3Al)+γ1+(β,AlNi)
10 20 30 40700
800
900
1000
1100
1200
1300
1400
1500
Ni 61.90Cu 38.10Al 0.00
Ni 46.80Cu 10.80Al 42.40Al, at.%
Tem
pera
ture
, °C
L+(Ni,Cu) L+(β,NiAl)
L+Ni3Al
(β,NiAl)(Ni,Cu)
Ni3Al+(Ni,Cu) Ni3Al+(β,NiAl)
1250
L
Fig. 17: Al-Cu-Ni.
Vertical section at 6
mass% Ni
Fig. 18: Al-Cu-Ni.
Vertical section at 60
mass% Ni
127
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Sc
Aluminium – Copper – Scandium
Alexander Pisch
Literature Data
The present evaluation updates and completes the evaluation made earlier by Q. Ran in the MSIT
Evaluation Program [1991Ran].
Two phases ScCuAl and ScCu2Al were early reported by [1965Tes] who prepared the ScCuAl alloy from
98.2% pure Sc and Cu and Al of higher purity, in an electric arc furnace and under helium atmosphere. The
powder X-ray diffraction pattern shows nearly a single phase of MgZn2 structure with traces of another
phase. For the ScCu2Al compound two possible structure types were considered by [1965Tes], the BiF3 and
the CsCl type structure. A later reinvestigation by [1965Tes] using single crystal method and a refinement
determined its structural type as MnCu2Al, although the authors explicitly did not exclude that it could
belong to the BiF3 type. The MgZn2 type structure of ScCuAl and the BiF3 type structure of ScCu2Al were
confirmed by [1968Dwi] and [1987Dwi], respectively, with considerable difference in the lattice
parameters reported for ScCuAl. [1996Nak] than reported a new ternary phase 2, ScCu0.6Al1.4 detected
from single crystal investigations.
[1988Kha] studied two polythermal sections at (a) constant 4 mass% Sc and up to 10 mass% Cu and (b) at
constant 20 mass% Cu up to 6 mass% Sc, by thermal analysis, metallography and X-ray phase analysis.
Samples were melted in an electric resistance furnace in corundum crucibles and cast into a thick-walled
copper mold. Besides some known elemental solid solution and binary compounds, a phase with unknown
composition was observed. [1988Kha] proposed that this phase, not reported earlier by [1965Tes], is a new
ternary compound. Later [1991Kha] could confirm this and determined its nominal composition as
ScCu4+xAl8–x where 0 x 2.6. [1997Sus] determined magnetic and electrical properties of this
compound.
[1991Kha] studied alloys in the Al-rich corner up to 40 mass% Cu and 6 mass% Sc at 450°C and 500°C by
optical microscopy, SEM coupled with EDX, microhardness and electrical resistivity measurements.
Samples have been prepared from the high purity metals (Al 99.99%, Sc 99.875%, Cu 99.996%) in an
electrical resistance furnace, for higher Sc contents in an electrical arc furnace under Ar atmosphere. The
liquidus surface in the Al-rich corner have been studied by [1992Yun, 1992Tor], with different results. As
the diagrams presented by [1992Yun] violate Gibbs phase rule and the results have not been considered.
The available data has been reviewed and compared to other Al-Sc-X systems by [1997Rok].
Binary Systems
The description of the binary Al-Sc system has been accepted from [1999Cac], Al-Cu from [2003Gro] and
Cu-Sc from [2002Wat].
Solid Phases
Four ternary compounds have been reported. Table 1 gives crystallographic data of these phases and all
binary phases from [1988Kha, 1991Kha, 1999Cac, 2003Gro, 2002Wat]. The ternary 4, ScCu4+xAl8–x
phase has a ThMn12 type structure with composition range from 0 < x < 2.6 [1991Kha].
Invariant Equilibria
Two four phase equilibria, L (Al)+ + 4 at 546°C and L+ScAl3 (Al)+ 4 at 572°C, were reported by
[1988Kha]. The compositions of the phases involved in the reactions were not determined.
Liquidus Surface
[1992Tor] established the liquidus surface in the Al-rich part of the diagram which is presented in Fig. 1.
128
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Sc
Isothermal Sections
The isothermal sections at 450 and 500°C, as determined by [1991Kha] are reproduced in Fig. 2a and 2b.
The maximum solubility for Al in the (Al)+CuAl2+ 4 three-phase equilibrium is 1.0 at.% Cu, 0.01 at.% Sc
at 450°C and 1.67 at.% Cu, 0.05 at.% Sc at 500°C. The maximum solubility for Al in the (Al)+ 4+ScAl3three phase equilibrium is 0.19 at.% Cu, 0.05 at.% Sc at 450°C and 0.21 at.% Cu, 0.05 at.% Sc at 500°C.
Temperature – Composition Sections
A partial vertical section at constant 20 mass% Cu with up to 6 mass% Sc, given in Fig. 3, was constructed
based on results of DTA, metallography and X-ray phase analysis [1988Kha]. The data given at constant 4
mass% Sc are not sufficient for constructing any diagram. [1992Tor] determined a partial vertical section
from 40 mass% Cu to 2 mass% Sc which is reproduced in Fig. 4.
Notes on Materials Properties and Applications
4, ScCu4+xAl8-x phase shows paramagnetic behavior at low temperature and becomes diamagnetic above
about 70 K [1997Sus]. The electrical resistivity as a function of the temperature is linear from 50 K to 300
K and the RT/ 4.2K values are 1.61 (x = 2.15), 1.69 (x = 1.5), 1.64 (x = 0.85) and 1.82 (x = 0).
3, ScCu2Al phase is also paramagnetic [1996Nak], measured magnetic susceptibility showed very weak
temperature dependence.
Miscellaneous
[2003Kan] studied crystal structure of the ternary 4, ScCu4+xAl8-x phase theoretically. The properties
related to the lattice vibration, such as phonons, density of states, specific heat and vibrational entropy were
calculated.
References
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1965Tes] Teslyuk M.Yu., Protasov, V.S. “The Crystal Structure of Ternary Phases in the Sc-Cu-Al
System”, Sov. Phys. Crystallogr., 10, 470-471 (1966), translated from Kristallografiya, 10,
561 (1965) (Crys. Structure, Experimental, 7)
[1968Dwi] Dwight, A.E., Mueller, M.H., Conner, R.A., Downey Jr., J.W., Knott, H., “Ternary
Compounds with the Fe2P-Type Structure”, Trans. Met. Soc. AIME, 242, 2075-2080 (1968)
(Crys. Structure, Experimental, 14)
[1985Mur] Murray, J.L., “The Aluminium-Copper System”, Int. Met. Rev., 30, 211-233 (1985) (Equi.
Diagram, Review, #, 230)
[1987Dwi] Dwight, A.E., Kimball, C.W., “ScT2X and LnT2X Compounds with the MnCu2Al-Type
Structure”, J. Less-Common Met., 127, 179-182 (1987) (Crys. Structure, Experimental, 9)
[1988Kha] Kharakterova, N.L., Dobatkina, T.V., “Polythermal Sections of the Al-Cu-Sc System”,
Russ. Metall., (6), 175-178 (1988), translated from Izv. Akad. Nauk SSSR, Met., (6), 180-182
(1988) (Equi. Diagram, Experimental, #, 5)
[1988Sub] Subramanian, P.R., Laughlin, D.E., Chakrabarti, D.J., “The Cu - Sc (Copper - Scandium)
System”, Bull. Alloy Phase Diagrams, 9, 378-382 (1988) (Equi. Diagram, Thermodyn.,
Review, 20)
[1991Kha] Kharakterova, M.L., “Phase Composition of Al-Cu-Sc Alloys at Temperature of 450 and
500°C”, Russ. Metall. (Engl. Transl.), 2, 195-199 (1991), translated from Izv. Akad. Nauk
SSSR, Met., (4), 191-194 (1991) (Crys. Structure, Equi. Diagram, Experimental, Mechan.
Prop., 9)
129
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Sc
[1991Ran] Ran, Q., ”Aluminium - Copper - Scandium”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.10210.1.20, (1991) (Equi. Diagram, Assessment, 18)
[1992Yun] Yunusov, I., Ganiyev, I.N., Vakhobov, A.V., “The Al-CuAl2-ScAl2 System” (in Russian),
Metally, 6, 196-199 (1992) (Crys. Structure, Equi. Diagram, Experimental, 4)
[1992Tor] Toropova, L.S., Kharakterova, M.L., Eskin, D.G., “The Surface Solidification Projection
Al-Cu-Sc System in Aluminium-Rich Range” (in Russian), Metally, 3, 207-212 (1992)
(Equi. Diagram, Experimental, 6)
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)”, in “Phase Diagrams of Binary Copper
Alloys”, Subramanian,. P.R., Chakrabarti,. D.J., Laughlin, D.E (Eds.), ASM International,
Materials Park, OH, 18-42 (1994) (Equi. Diagram, Crys. Structure, Thermodyn., Review, #,
*, 226)
[1996Nak] Nakonechna, N.Z., Shpyrka, Z.M., “The Crystal Structure of the ScCu2Al and ScCu0.6Al1.4
Compounds”, Vestn. L’vov. Univ, Ser. Khim., 36, 29-33 (1996) (Crys. Structure,
Experimental, Magn. Prop., 7)
[1997Rok] Rokhlin, L.L., Dobatkina, T.V., Kharakterova, M.L., “Structure of the Phase Equilibrium
Diagrams of Aluminum Alloys with Scnadium”, Powder Metall. Met. Cer., 36, 128-132
(1997) (Equi. Diagram, Experimental, 18)
[1997Sus] Suski, W., Cichorek, T., Wochowski, K., Badurski, D., Kotur, B.Ya., Bodak, O.I.,
“Low-Temperature Electrical Resistance of the U(Cu,Ni)4Al8 System and Magnetic and
Electrical Properties of ScCu4+xAl8-x”, Physica B (Amsterdam), 230-232, 324-326 (1997)
(Crys. Structure, Experimental, Electr. Prop., 10)
[1999Cac] Cacciamani, G., Riani, P., Borzone, G., Parodi, N., Saccone, A., Ferro, R., Pisch, A.,
Schmid-Fetzer, R., “Thermodynamic Measurements and Assessment of the Al-Sc System”,
Intermetallics, 7, 101-108 (1999) (Experimental, Crys. Structure, Equi. Diagram,
Thermodyn., 26)
[2002Gul] Gulay, L.D, Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. “Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Wat] Watson, A., Wagner, S., Lysova, E., Rokhlin, L., “Cu-Sc (Copper-Scandium)”, MSIT
Binary Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials
Science International Services GmbH, Stuttgart; Document ID: 20.20091.1.20, (2002)
(Crys. Structure, Equi. Diagram, Assessment, 14).
[2003Gro] Gröbner, J., “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 68)
[2003Kan] Kang, Y., Chen, N., “Site Preference and Vibrational Properties of ScCuxAl12-x”, J. Alloys
Compd., 349(1-2), 41-48 (2003) (Calculation, Crys. Structure, Experimental, Phys. Prop.,
29)
130
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Sc
Table 1: Crystallographic Data of Solid Phase
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Cu)
< 1084.62
Cu1-xAlx
cF4
Fm3m
Cu
a = 361.46
a = 361.52
a = 365.36
at 25°C [Mas2], melting point [1994Mur]
0 to 19.7 at.% Al, [Mas2]
x = 0, quenched from 600°C
x = 0.152, quenched from 600°C, linear
da/dx
dissolves ~ 0.5 at.% Sc (865°C)
[1988Sub]
(Al)
< 660.45
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2],
0 to 2.48 at.% Cu [2003Gro]
( Sc)
< 1337
hP2
P63/mmc
Mg
a = 330.88
c = 526.80
25°C [Mas2]
( Sc)
1541-1337
cI12
Im3m
W
a = 373 [2002Wat], negligible (?) solid solubility
of Cu in ( Sc)
, Cu3Al(h)
1049-559
cI2
Im3m
W
a = 295.64
70.6 to 82 at.% Cu, [2003Gro]
at 672°C in + (Cu) alloy
2, Cu100-xAlx< 363
-
TiAl3long period
super-lattice
-
a = 366.8
c = 368.0
22 x 23.5 [2003Gro]
76.5 to 78.0 at.% Cu
at 76.4 at.% Cu
(subcell only)
0, Cu100-xAlxCu 2Al
1037-800
cI52
I43m
Cu5Zn8
- 31 x 40.2 [Mas2],
62 to 68 at.% Cu [2003Gro]
1, Cu9Al4< 890
cP52
P3m
Cu9Al4
a = 870.23
a = 870.68
62 to 68 at.% Cu [Mas2]
powder and single crystal, [V-C2]
from single crystal [V-C]
, Cu100-xAlx< 686
hR*
R3m
a = 1226
c = 1511
38.1 x 40.7 [Mas2]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C]
1, Cu100-xAlx958-848
cubic? - 37.9 x 40.6
59.4 to 62.1 at.% Cu, [Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.47 x 0.78
55.0 to 61.1 at.% Cu, [Mas2, V-C2],
1, Cu47.8Al35.5(h)
590-530oF88 - 4.7
Fmm2Cu47.8Al35.5
a = 812
b = 1419.85c = 999.28
55.2 to 59.8 at.% Cu [Mas2, 1994Mur]structure: [2002Gul]
2, Cu11.5Al9(r)
< 570oI24 - 3.5
Imm2Cu11.5Al9
a = 409.72
b = 703.13c = 997.93
55.2 to 56.3 at.% Cu [Mas2, 1985Mur]structure: [2002Gul]
131
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Sc
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200c = 863.5
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu
[V-C2]
, CuAl2< 591
tI12
I4/mcm
CuAl2
a = 606.7
c = 487.7
31.9 to 33.0 at.% Cu, [2003Gro]
single crystal [V-C2]
ScCu
< 1125
cP2
Pm3m
CsCl
a = 324 to 326 [V-C2]
ScCu2
< 990
t16
I4/mmm
MoSi2
a = 329.0
c = 838.8
[2002Wat]
ScCu4
< 925
tI* a = 491
c = 698
[Mas2, 2002Wat]
ScAl3< 1320
cP4
Pm3m
AuCu3
a = 410.5 [Mas, V-C]
ScAl2< 1420
cF24
Fd3m
MgCu2
a = 757.8 [1999Cac]
ScAl
< 1240
cP2
Pm3m
CsCl
oP8
Cmcm
CrB
a = 354.0
a = 398.8
b = 988.2
c = 365.2
[V-C]
[V-C]
Sc2Al
< 1300
hP6
P63/mmc
Ni2In
a = 488.8
c = 617.3
[1999Cac]
* 1, ScCuAl hP12
P63/mmc
MgZn2
a = 504
c = 824
a = 523
c = 849
[1965Tes]
[1968Dwi]
* 2, ScCu0.6Al1.4 hP24
P63/mmc
MgNi2
a = 525.2
c = 1711.3
[1996Nak]
* 3, ScCu2Al cF16
Fm3m
MnCu2Al
a = 619.9
a = 620
a = 620.3
[1996Nak]
* 4, ScCu4+xAl8-x tI26
I4/mmm
ThMn12
a = 863 to 866
c = 510 to 443
[1991Kha, 1992Yun, 1997Sus]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
132
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Sc
(Al)
1.0·10-30.75·10-30.5·10-30.25·10-3 1.5·10-31.25·10-3Al
Sc, at.%
e2
5
10
20
15
ScAl3
(Al)
U, 572°C
e1
E, 546°C
Cu,at.%
q
t
Fig. 1: Al-Cu-Sc.
Partial liquidus
surface of the Al-rich
corner [1992Tor]
Sc 3.00Cu 0.00Al 97.00
Sc 0.00Cu 3.00Al 97.00
Al Data / Grid: at.%
Axes: at.%
(Al)+ScAl3+τ4
(Al)
(Al)+τ
4
(Al)+
ScA
l 3
(Al)+θ+τ
4
(Al)+θ
Fig. 2a: Al-Cu-Sc.
Partial isothermal
section of the Al-rich
corner at 450°C
[1991Kha]
133
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Sc
Sc 4.00Cu 0.00Al 96.00
Sc 0.00Cu 4.00Al 96.00
Al Data / Grid: at.%
Axes: at.%
(Al)+
ScA
l 3
(Al)
(Al)+ScAl3+τ4(A
l)+τ4
(Al)+θ
(Al)+θ+τ
4
Fig. 2b: Al-Cu-Sc.
Partial isothermal
section of the Al-rich
corner at 500°C
[1991Kha]
500
600
Sc 0.00Cu 9.60Al 90.40
Sc 4.18Cu 9.86Al 85.96Sc, at.%
Tem
pera
ture
, °C
(Al)+θ (Al)+θ+τ4
(Al)+τ4
(Al)+ScAl3+τ4
546°C
L+(Al)+τ4
572°CL+(Al)+ScAl3
L+ScAl3
L
L+(Al)
1.0 4.02.0 3.0
Fig. 3: Al-Cu-Sc.
Partial polythermal
section at 20
mass% Cu
134
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Sc
400
500
600
700
Sc 0.00Cu 22.06Al 77.94
Sc 1.21Cu 0.00Al 98.79Sc, at.%
Tem
pera
ture
, °C
(Al)+θ
L+(Al)+τ4
L
L+θ
L+τ4+ScAl3
L+ScAl3
(Al)+θ+τ4
(Al)+τ4
(Al)+ScAl3
(Al)+τ4+ScAl3
L+(Al)+ScAl3L+τ4
L+θ+τ4L+(Al)+θ
572°C
546°C
1.00.5
Fig. 4: Al-Cu-Sc.
Partial vertical section
of the Al-rich corner
from 40 mass% Cu to
2 mass% Sc
[1992Tor]
135
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
Aluminium – Copper – Silicon
Hans Leo Lukas, Nathalie Lebrun
Literature Data
In the early work the Al corner was investigated by thermal analysis, by optical micrographs [1923Wet,
1928Gwy, 1931Ura, 1953Phi, 1975Kuz] and by measuring the electric resistivity [1940Wie]. A ternary
eutectic L +(Al)+Si was found at 525°C [1923Wet, 1928Gwy, 1931Ura, 1975Kuz], at 524°C [1953Phi]
or 522°C [1936His]. The temperature given by [1984Oya], 512°C, deviates considerably. The growth of
this eutectic is complex due to the coarsening during solidification [1983Sch]. Liquidus as well as solidus
and solvus of the (Al) solid solution were determined in very detail by [1953Phi]. The papers agree well.
[1968Epi] gave three vertical sections at 5, 8 and 10 mass% Si up to 55 mass% Cu. The eutectic agrees well
with the previously mentioned papers, whereas the liquidus surface disagrees. In the section at 8 mass% Si
the boundary of L against L+Si in the interval 29 to 39 mass% Cu go from 580 to 590°C. L+Si tie lines go
from the points of this boundary to pure Si and pass the 10 mass% Si section between 30 and 40 mass% Cu.
In the 10 mass% Si section, however, for this whole range of Cu contents above 580°C single phase liquid
is shown. This is a severe contradiction exceeding by far the limits of accuracy of the drawings. The whole
ternary system was investigated by thermal analysis and by interpretation of microstructures recorded in
micrographs [1934Mat] and [1936His]. Matsuyama [1934Mat] presented 12 vertical sections, a projection
of the liquidus surface with the Cu corner enlarged in an extra diagram, and an isothermal section at room
temperature. Hisatsune [1936His] reported 16 vertical and four isothermal sections as well as the lines of
double saturation of the liquidus. No ternary phase exists in the system. The later detected phase of the
binary Cu-Si system in both papers was not distinguished from the (Cu) solid solution. Between the
phases of Cu-Al and Cu-Si, continuous solid solubility was found. [1934Mat] assumed complete solid
solubilities between the 0 (CuAl) and (CuSi) phase, whereas [1936His] reported it between in CuSi
and 1 in CuAl. However, these three phases have different crystal structures [V-C], which makes complete
miscibility unlikely. The two papers disagree in the 70 to 90 mass% Cu region of the liquidus surface.
[1934Mat] shows a large field of primary crystallization of 0- and a separate one for 1. [1936His] shows
smaller fields of primary crystallization for the 0 and 1 phases, but a large one for 1- . Both papers agree
that all binary Al-Cu phases containing more Al than 1 dissolve less than 1 mass% Si. The Cu-Si phase
dissolves about 1 mass% Al, whereas , ' and " dissolve between 2 and 3 mass% Al. Part of the Cu-rich
corner was investigated by [1948Wil]. The phase is stabilized by Al and seems to be stable to room
temperature inside the ternary system. This was confirmed by [1974Llo]. The phase is also stabilized, but
decomposes eutectoidally at 545°C [1974Llo] into (Cu), and 1 (named 2 by [1974Llo]) below both
binary eutectoids.
Literature published until 1986 is carefully reviewed by [1992Luk] and further updated by the present
evaluation.
Binary Systems
Assessments of the Al-Cu system by [2003Gro], of the Al-Si system by [2003Luk] and of the Cu-Si system
by [2002Leb] form the binary edge boundary consistent with the ternary data. They are based on [1994Mur,
1998Liu] for Al-Cu, [1984Mur] for Al-Si and [1994Ole, 2000Yan] for Cu-Si, respectively. For the Al-Cu
system recent crystal structure investigations of the 1 and 2 phases [2002Gul] are taken into account. For
the solubilities of Cu and Si in Al the thermodynamic calculations of the COST 507 action [1998Ans] are
accepted, as they provide numerically a much better resolution than the above mentioned graphic
assessments can do.
136
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
Solid Phases
No ternary phase was found. The stable binary phases are listed in Table 1. The Greek letters for
abbreviation of the phases are those used by the accepted binary diagrams, except 1, to distinguish it from
of the Cu-Si system. All phases except of the binary Al-Cu system have a numerical subscript; the
phases of the Cu-Si system are indexed by a prime or double prime instead of a subscript.
Invariant Equilibria
A tentative reaction scheme is shown in Fig. 1a and Fig. 1b. The non-dashed four-phase equilibria
containing liquid are taken from [1936His]. The eutectic E5 is more accurately given by [1953Phi], it agrees
with that of [1936His]. The equilibrium E4 is taken from [1974Llo]. The dashed equilibria are attempts to
complete the reaction scheme. P2 and U3 are introduced to distinguish from 1. As the phase may be
stable down to room temperature [1974Llo], the three phase equilibria reported by [1936His] to contain the
(Cu) solid solution at 400°C are assumed to contain instead of (Cu). Of the three phase equilibria at room
temperature, Si+(Al)+ is well-established [1928Gwy, 1936His, 1953Phi, 1986Che]. + 2+Si, 2+ 2+Si,
2+ 1+Si, 1+ 1+Si, and 1+ "+Si are reported by [1936His]. The transformations 1 2, 1 2 of Al-Cu
and ' " of the Cu-Si binary system are neglected in Fig. 1 for clarity. The compositions of the liquid
in the invariant equilibria, given by [1936His], are summarized in Table 2.
Liquidus Surface, Solidus and Solvus Surfaces
The liquidus surface of the whole system is shown in Fig. 2. The lines of double saturation of liquid are
taken from [1936His], except those between and 1. The isotherms in the Cu corner are derived from the
vertical sections given by [1936His]. The isotherms of the primary crystallization of Si are taken from
[1934Mat], except at 800°C and below, which are adjusted to fit with the isotherms derived from the data
of [1936His]. The liquidus surface of the Al corner in Fig. 3 is thermodynamically calculated using the
binary thermodynamic descriptions of Al-Cu and Al-Si from the COST 507 database [1998Ans] adding
ternary terms to the Gibbs energy description of liquid reproducing temperature and composition of liquid
of the eutectic L (Al)+Si+ as given by [1953Phi] the most detailed experimental investigation of the
Al-rich part. ternGliq = xAl xCu xSi (27000 xAl+100000 xCu+8000 xSi) J (mole of atoms)-1
This ternary term is tentative and must not be taken in the range with less than about 75 at.% Al. The
calculated liquidus agrees very well with the graph of [1953Phi] within the accuracy of the drawing.
The solidus and solvus surfaces of the (Al) solid solution in Figs. 4 and 5 are also thermodynamically
calculated using the same data set that was used to calculate the liquidus, yielding virtually identical results
as given by [1953Phi], whereas the solvus after [1940Wie] shows about 5 to 10% higher solubilities in (Al).
Isothermal Sections
In Fig. 6 the 400°C isothermal section of the Cu corner is given. The concentrations of the (Cu)+ + 1
equilibrium are taken from [1948Wil], those of the + 1+ ", 1+ "+Si, + "+ , and + + 1 equilibria
from [1936His], although [1936His] assumed the (Cu) phase at the concentrations ascribed to . The
remaining lines are interpolated between these concentrations and those taken from the accepted binary
systems. The isothermal section therefore must be taken as tentative. Although [1934Mat, 1936His] and
[1948Wil] gave more isothermal and vertical sections, too much speculation is needed to draw isothermal
sections at higher temperatures which agree with the three papers. At room temperature all phases with less
than 70 at.% Cu are in equilibrium with Si [1934Mat, 1936His].
137
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
Temperature – Composition Sections
Several polythermal sections were reported by [1936His]. They suffer from the non-distinguishing of the
(Cu) and phases and therefore are not reproduced here. [1986Gul] reported a polythermal section at 40
mass% Cu determined by thermal analysis and X-ray diffraction techniques. The point of double saturation
of liquid with respect to and Si deviates significantly from that shown in Fig. 2 based on [1936His,
1953Phi].
Thermodynamics
The heat of melting of the eutectic in the Al corner was measured by [1986Che] and [1984Mar] to be
364 J g-1 and 357 J g-1 respectively, which corresponds to 11.6 and 11.4 kJ mol-1. [1985Far] used an ideal
model to determine the heat of mixing at the eutectic composition. The calculated value found to be
422 J g-1 (13.5 kJ mol-1) is overestimated.
[1984Ber] reported from emf measurements the activities of Al in Al-Cu-Si alloys at 660, 700, 800 and
900°C.
[2000Wit] measured the partial and the integral enthalpies from liquid Al-Cu-Si alloys at 1302 ± 3°C using
a high temperature calorimeter only 3 vertical sections (xAl : xSi = 0.8 : 0.2, 0.5 : 0.5, 0.2 : 0.8 with
0 xCu 1). The thermodynamic functions of mixing were calculated from the partial measured enthalpies
using a regular association model. Minimum of enthalpy varies from -14.5 kJ mol-1 (Cu-25 Si (at.%)) to
-17.3 kJ mol-1 (Al - 60Cu (at.%)).
Notes on Materials Properties and Applications
Using a grain and pore formation, [2002Chi] studied the micro-porosity in an 3Cu-Al-7Si (mass%) alloy
containing soluble hydrogen.
Si additions were found to lead to a very slight increase in corrosion resistance, while Cu additions were
found to lower the overall corrosion resistance significantly [1994Gri, 2001Tra]. This is probably due to the
large percentage of primary silicon phase in that alloys [2001Tra]. Moreover, Si accelerates the
age-hardening of the Al-Cu-Si alloys [1994Gri]. Corrosion can occur when alloys are exposed to
photolithographic processing [1990Wes].
[2000Zho] investigated the creep behavior in 0.5Cu-Al-1Si (mass%) alloys with thickness ranging from 10
to 500 m.
In compressed samples of high purity aluminium alloys, with hard precipitates 0.5Cu-Al-1Si (mass%), a
variety of deformation band patterns has been observed, including occasional exquisite detailed structuring
[1998Kul].
Miscellaneous
[1991Sta] studied the precipitation of Si and Cu in alloys 1.3Cu-Al-19.1Si (at.%). From liquid quenched of
this alloy composition, a transition ’ is observed ( ’ intermediate and equilibrium phase). For heating
rates less than 20°C/min, Cu precipitates as the ’, while for heating rates more than 40°C/min, Cu
precipitates mainly as the phase. In solid quenched samples, Guinier-Preston (GP) zone formation
occurred during annealing at room temperature with a rate of 104 time slower than in the corresponding
Al-Cu binary.
[1990Yam] studied the solid solubilities of Cu and Si in Al under high pressure to 3 Gpa using the diffusion
couple method. It was found an increase of the solubilities with high pressure.
[1985Oko] investigated the solidification structures of gasifiable pattern cast 4.25Cu-Al-1.03Si (at.%) alloy
to establish an influence of variations in casting conditions on such structure.
138
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
References
[1923Wet] Wetzel, E., “Progress in Aluminium Investigation, Copper and Silicon in Aluminium” (in
German), Metallboerse, 13, 936-938 (1923) (Equi. Diagram, Experimental, 5)
[1928Gwy] Gwyer, A.G.C., Philips, H.W.L., Mann, L., “The Constitution of the Alloys of Aluminium
with Copper, Silicon and Iron”, J. Inst. Met., 40, 297-358 (1928) (Equi. Diagram,
Experimental, 33)
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1931Ura] Urazov, G.G., Pogodin, S.A., Zomornev, G.M., “Physico-Chemical Investigations of
Ternary Alloys of Aluminium with Silicon and Copper” (in Russian), Izv. Inst.
Fiziko-Khimich. Analiza, 5, 157-200 (1931) (Equi. Diagram, Experimental, 30)
[1934Mat] Matsuyama, K., “Ternary Diagram of the Al-Cu-Si System” (in Japanese), Kinzoku no
Kenkyu, 11, 461-490 (1934) (Equi. Diagram, Experimental, #, *, 8)
[1936His] Hisatsune, C., “Constitution Diagram of the Copper-Silicon-Aluminium System” (in
Japanese), Mem. Coll. Eng. Kyoto Imp. Univ., 9(1), 18-47 (1935), translated from Tetsu to
Hagane, 22, 597-622 (1936) (Equi. Diagram, Experimental, #, *, 12)
[1940Wie] Wiehr, H., “Contribution to the Knowledge of the Aluminium-Copper-Silicon and
Aluminium-Copper-Iron Systems” (in German), Alum. Arch., 31, 5-14 (1940) (Equi.
Diagram, Experimental, 14)
[1948Wil] Wilson, F.H., “The Copper-Rich Corner of the Copper-Aluminium-Silicon Diagram”,
Trans. Amer. Inst. Met. Eng., Inst. Metals Div., 175, 262-282 (1948) (Equi. Diagram,
Experimental, 10)
[1953Phi] Philips, H.W.L., “The Constitution of Aluminium-Copper-Silicon Alloys”, J. Inst. Met., 82,
9-15 (1953) (Equi. Diagram, Experimental, 16)
[1968Epi] Epikhin, M.A., Zaboleev-Zotov, V.V., Mishchenko, Yu.N., Tsymlov, A.I., Shashin, A.V.,
“Vertical Sections of the Equilibrium Diagram Aluminium-Copper-Silicon” (in Russian),
Metallovedenie Proch. Mater., Pashkov, (Ed.), Volgograd, (1968) (Equi. Diagram,
Experimental, 0)
[1974Llo] Lloyd, B.A., Pyemont, J.W., “Phase Equilibrium Diagram for 2% Silicon Isopleth in
Copper-Aluminium-Silicon Alloys in the Range 5 to 11 % Al”, Met. Tech., 534-537 (1974)
(Equi. Diagram, Experimental, 14)
[1975Kuz] Kuznetsov, G.M., Smagulov, D.U., Vasenova, S.V., “Experimental Determination of the
Direction of Tie Lines in the Two Phase Fields (Al)+Liquid in the Al-Cu-Mg and Al-Cu-Si
System” (in Russian), Izv. V. U. Z. Tsvetn. Met., (4), 96-100 (1975) (Equi. Diagram,
Experimental, 14)
[1983Sch] Schnake, W., Abaud, S., “Solidification of the Al-Cu-Si Ternary Eutectic”, Uni. Chile,
Conf.: CONAMET 83, Santiago, A474-A482 (1983) (Experimental, 14)
[1984Ber] Berecz, E., Bader, I., Weberne, Kovaks, E., Horvath, J., Gabor, Z., “Thermodynamic
Examination of Aluminium Alloys by the Electrochemical Method”, Banyasz. Kohasz.
Lapok, Kohasz., 117(9), 413-417 (1984) (Experimental, Thermodyn., 10)
[1984Mar] Martynova, N.M., Rodionova, E.K., Tishura, T.A., Cherneeva, L.I., “Enthalpy of Melting
of Metallic Eutectics”, Russ. J. Phys. Chem. (Engl. Transl.), 58(4), 616-617 (1984),
translated from Zh. Fiz. Khim., 58(4), 1009-1010 (1984) (Thermodyn., 6)
[1984Mur] Murray, J.L., Mcalister, A.J., “The Al-Si (Aluminum-Silicon) System”, Bull. Alloy Phase
Diagrams, 5, 74-84 (1984) (Equi. Diagram, Review, #, 73)
[1984Oya] Oya, S., Fujii, T., Ohtaki, M., Baba, S., “Solidified Structure and Hot Tearing of Al-4.5%
Cu and Al-4.5% Cu-5% Si Alloys Containing Various Additives” (in Japanese), J. Japan
Inst. Light Metals, 34(9), 511-516 (1984) (Experimental, 18)
[1985Far] Farkas, D., Birchenall, C.E., “New Eutectic Alloys and Their Heats of Transformation”,
Met. Trans. A, 16A, 323-328 (1985) (Experimental, Thermodyn., 12)
139
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
[1985Mur] Murray, J.L., “The Aluminium-Copper System”, Int. Met. Rev., 30, 211-233 (1985) (Equi.
Diagram, Review, #, 230)
[1985Oko] Okorafor, O.E., “Solidification Structures and Gasfiable Pattern Casting of
Al-4.25Cu-1.03Si”, Trans. Indian Inst. Met., 38(5), 415-422 (1985) (Experimental, 11)
[1986Che] Cherneeva, L.I., Martynova, N.M., Rodionova, E.K., “Energy Capacity of Metallic Alloys
as Promising Heat-Storing Materials” (in Russian), Izv. Vyss. Uchebn. Zaved., Energia, 12,
78-82 (1986) (Thermodyn., 7)
[1986Gul] Gul’din, I.T., Zakharov, A.M., Arnold, A.A., “The Effect of Iron and Silicon on the
Liquidus Temperature and Phase Composition of an Aluminium Alloy with 40% Copper”
(in Russian), Izv. V. U. Z. Tsvetn. Met., 4, 90-95 (1986) (Equi. Diagram, 8)
[1989Mee] Meetsma, A., de Boer, J.L., van Smaalen, S., “Refinement of the Crystal Structure of
Tetragonal Aluminum-Copper (Al2Cu)”, J. Solid State Chem., 83(2), 370-372 (1989) (Crys.
Structure, Experimental, 17)
[1990Wes] Weston, D., Wilson, S. R., Kottke, M., “Microcorrosion of Al-Cu and Al-Cu-Si Alloys:
Interaction of the Metallization with Subsequent Aqueous Phototithographic Processing”,
J. Vac. Sci. Technol., A8(3), 2025-2032 (1990) (Experimental, Thermodyn., 0)
[1990Yam] Yamane, T., Minamino, Y., Sato, T., Itaya, E., Miyamoto, Y., Koizumi, M., “Solid
Solubility Chages in Aluminium Base Binary Alloys under High Pressure Measured by
Diffusion Couple Method”, Met. Abstr. Light Metals and Alloys, 23, 80 (1990) (Equi.
Diagram, Experimental,0)
[1991Ell] Ellner, M., Kolatschek, K., Predel, B., “On the Partial Atomic Volume and the Partial Molar
Enthalpy of Aluminium in some Phases with Cu and Cu3Au Structures”, J. Less-Common
Metals, 170, 171-184 (1991) (Experimental, Crys. Struct., 57)
[1991Sta] Starink, M.J., Mourik, P.V., “A Calorimetric Study of Precipitation in an Al-Cu Alloy with
Silicon Particles”, Metall. Trans. A, 22A, 665-674 (1991) (Calculation, Crys. Structure,
Experimental, 40)
[1992Luk] Lukas, H.L., ”Aluminium - Copper - Silicon”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.15417.1.20, (1992) (Crys. Structure, Equi. Diagram,
Assessment, 15)
[1994Gri] Griffin, A.J., Brotzen, F.R., Dunn, C.F., “Impedance-Spectroscopy Response of
Aluminium-Copper-Silicon Alloys”, J. Electrochem. Soc., 141(12), 3473-3479 (1994)
(Corrosion, Crys. Structure, Experimental, 19)
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)” in “Phase Diagrams of Binary Copper Alloys”,
Subramanian, P.R., Chakrabarti D.J., Laughlin, D.E., (Eds.), ASM International, Materials
Park, OH, 18-42 (1994) (Equi. Diagram, Cryst. Struct., Thermodyn., Review, 226)
[1994Ole] Olesinski, R.W., Abbaschian, G.J., “Cu-Si (Copper-Silicon)” in “Phase Diagrams of Binary
Copper Alloys”, Subramanian, P.R., Chakrabarti D.J., Laughlin, D.E., (Eds.), ASM
International, Materials Park, OH, 398-405 (1994) (Review, Equi. Diagram, Cryst. Struct.,
Thermodyn., 60)
[1998Ans] Ansara, I., Dinsdale, A.T., Rand, M.H., COST507. Thermochemical Database for Light
Metal Alloys, Vol. 2, European Communities, Luxemburg, (1998) (Equi. Diagram,
Thermodyn., Calculation)
[1998Kul] Kulkarni, S.S., Starke, E.A., Kuhlmann-Wilsdorf, D., “Some Observation on Deformation
Banding and Correlated Microstructures of Two Aluminium Alloys Compressed at
Different Temperatures and Strain Rates”, Acta Mater., 46(15), 5283-5301 (1998) (Crys.
Structure, Experimental, Theory, 40)
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-Rich Portion of
the Al-Cu Binary System”, J. Alloys Comp., 264, 201-208 (1998) (Equi. Diagram,
Experimental, 25)
[2000Wit] Witusiewicz, V.T., Arpshofen, I., Seifert, H.-J., Aldinger, F., “Enthalpy of Mixing of Liquid
Al-Cu-Si Alloys”, J. Alloys Compd., 297, 176-184 (2000) (Experimental, Thermodyn., 11)
140
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
[2000Yan] Yan, X., Chang, Y.A., “A Thermodynamic Analysis of the Cu-Si System”, J. Alloys
Compd., 308(1-2), 221-229 (2000) (Equi. Diagram, Thermodyn., 41)
[2000Zho] Zhou, Q., Itoh, G., “Creep Behavior of Aluminum Alloy Foils for Microelectronic Circuits”,
Key Eng. Mater., 171-174, 633-638 (2000) (Experimental, Mechan. Prop., 12)
[2001Tra] Traldi, S.M., Costa, I., Rossi, J.L., “Corrosion of Spray Formed Al-Si-Cu Alloys in Ethanol
Automobile Fuel”, Key Eng. Mater., 189-191, 352-357 (2001) (Corrosion,
Experimental, 11)
[2002Chi] Chirazi, A., Atwood, R.C., Lee, P.D., “Micro-Macro Modelling of Microstructure and
Microporosity in Al-Si-Cu Alloys”, Mater. Sci. Forum, 396-402, 661-666 (2002) (Crys.
Structure, Experimental, Theory, 10)
[2002Gul] Gulay, L.D., Harbrecht,B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, in “Crystal Chemistry of Intermetallic Compounds”, Abstr. VIII Int. Conf. Lviv,
P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Leb] Lebrun, N., Dobatkina, T., Kuznetsov, V., “Cu-Si (Copper-Silicon)”, MSIT Binary
Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science
International Services GmbH, Stuttgart; Document ID: 20.12505.1.20, (2002) (Crys.
Structure, Equi. Diagram, Assessment, 23)
[2003Gro] Gröbner, J., “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 68)
[2003Luk] Lukas, H.L., “Al-Mg (Aluminium-Magnesium)”, MSIT Binary Evaluation Program, in
MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 49)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Cu)
< 1084.62
Cu1-xAlx
cF4
Fm3m
Cu
a = 361.46
a = 361.52
a = 365.36
at 25°C [Mas2], 0 to 19.7 at.% Al
[Mas2]
melting point [1994Mur]
[1991Ell], x = 0, quenched from 600°C
[1991Ell], x = 0.152, quenched from
600°C, linear da/dx
(Al)
< 660.45
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
0 to 2.48 at.% Cu [Mas2]
(Si)
< 1414
cF8
Fd3m
C (diamond)
a = 543.06 0 to 0.003 at.% Cu [1994Ole]
, Cu1-x-yAlxSiy Cu3Al
1049-559
Cu6Si
853-787
cI2
Im3m
W
a = 295.64
a = 285.4
70.6 to 82 at.% Cu [1985Mur, 1998Liu]
at 672°C in + (Cu) alloy
14.2 to 16.2 at.% Si [1994Ole]
at 14.9 at.% Si [1994Ole]
141
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
2, Cu100-xAlx< 363
TiAl3long period
superlattice a = 366.8
c = 368.0
22 x 23.5 [Mas, 1985Mur]
76.5 to 78.0 at.% Cu
at 76.4 at.% Cu (subcell only)
0, Cu1-x-yAlxSiy Cu2Al
1037-800
cI52
I43m
Cu5Zn8
31 x 40.2 [Mas]
62 to 68 at.% Cu [1998Liu]
1, Cu9Al4< 890
cP52
P43m
Cu9Al4
a = 870.23
a = 870.68
62 to 68 at.% Cu [Mas2, 1998Liu]
powder and single crystal [V-C2]
from single crystal [V-C]
1, Cu100-xAlx< 686
hR*
R3m
a = 1226
c = 1511
38.1 x 40.7 [Mas2, 1985Mur]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C]
1, Cu100-xAlx958-848
cubic ? - 37.9 x 40.6
[Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6 or hP4
P63/mmc
Ni2In or NiAs
a = 414.6
c = 506.3
0.47 x 0.78
55.0 to 61.1 at.% Cu
[Mas, 1985Mur, V-C2]
NiAs type in [Mas2, 1994Mur]
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2Cu47.8Al35.5
a = 812
b = 1419.85c = 999.28
55.2 to 59.8 at.% Cu [Mas2, 1994Mur]structure: [2002Gul]
2, Cu11.5Al9(r)
< 570
oI24 - 3.5
Imm2Cu11.5Al9
a = 409.72
b = 703.13c = 997.93
55.2 to 56.3 at.% Cu [Mas2, 1985Mur]structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu [Mas2, 1985Mur]
Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu
[V-C2]
, CuAl2< 591
tI12
I4/mcm
CuAl2
a = 606.7
c = 487.7
31.9 to 33.0 at.% Cu [1994Mur]
Single crystal [V-C2, 1989Mee]
, Cu100-xSix
Cu7Si
842-552
hP2
P63/mmc
Mg
a = 256.05
c = 418.46
11.05 x 14.5 at.% Si [1994Ole]
at 14.9 at.% Si [1994Ole]
, Cu5Si(r)
< 729
cP20
P4132
Mn
a = 619.8 17.15 to 17.6 at.% Si [1994Ole]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
142
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
Table 2: Invariant Equilibria
, Cu5Si (h)
824-711
t**
a = 881.5
c = 790.3
17.6 to 19.6 at.% Si [1994Ole]
sample was annealed at 700°C [V-C2]
, Cu15Si4< 800
cI76
I43d
Cu15Si4
a = 961.5 21.2 at.% Si [1994Ole, V-C2]
, Cu3Si(h2)
859-558
hR*
R3m
or t**
a = 247
= 109.74°
a = 726.7
c = 789.2
23.4 to 24.9 at.% Si [1994Ole]
[V-C2]
', Cu3Si(h1)
620-467
hR*
R3
a = 472
= 95.72°
23.2 to 25.2 at.% Si [1994Ole]
", Cu3Si(r)
< 570
o** a = 7676
b = 700
c = 2194
23.3 to 24.9 at.% Si [1994Ole]
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Si
L + + 0 1 980 P1 L 24.3 69.2 6.5
L + 0 1+ 1 910 U1 L 39.5 57.4 3.1
1 L + 1 840 E1 L 38.2 54.3 7.5
L + 1 2 + Si 760 U3 L 37 50.1 12.9
L + + Si 727 E2 L 10.6 68.1 21.3
L + 2 1 + Si 608 U8 L 60.1 31.7 8.2
L + 1 + Si 573 U9 L 68.2 25.1 6.7
L + (Al) + Si 524 E5 L
(Al)
80.6
96.8
13.4
2.1
6.0
1.1
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
143
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
Fig
. 1a:
Al-
Cu
-Si.
Rea
ctio
n s
chem
e, p
art
1
Al-
Cu
Cu
-Si
l +
βγ 0
10
37
p1
β +
(C
u)
κ8
42
p6
Lγ 1
+ (
Si)
ca.
80
0e 5
Al-
Cu
-Si
L +
β +
γ0
γ 19
80
P1
Al-
Si
l +
(C
u)
β8
52
p4
l +
γ0
ε 1
95
8p2
lβ
+ (
Cu)
10
32
e 1
ε 1 l
+ ε2
84
8e 2
γ 0γ 1
+ β
78
0e 7
ε 1 +
γ1
ε 2
85
0p5
γ 0 +
ε 1γ 1
87
3p3
ε 1 L
+ γ1 +
ε2
84
0E1
L +
β +
γ1 +
ε1
δca
. 9
00
P2
L +
γ0
γ 1 +
ε1
91
0U2
Lη
+δ
+ (
Si)
72
7E2
L +
γ1
δ +
(S
i)?
U3
L +
γ1
ε2 +
(S
i)7
60
U4
δ +
κγ
72
9p9
βδ
+κ
78
5e 6
η +
δε
80
0p8
l S
i +
η8
02
e 4
lδ
+ η
82
0e 3
l + β
δ8
24
p7
L +
γ0
+γ 1
L +
γ1
+ε 1
L +
β +
γ 1
L +
γ1 +
ε2
L +
γ1
+δ
β +
γ 1+
δ
γ 1 +
δ +
(S
i)
L +
δ +
(S
i)
β+(C
u)+
κ
δ+κ+
γ
β+δ+
κ
η+δ+
ε
η +
δ +
(S
i)L
+ ε2 +
(S
i)γ 1+
ε 2+
(S
i)
144
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
Fig
. 1b
: A
l-C
u-S
i. R
eact
ion s
chem
e, p
art
2
Al-
Cu
Cu
-Si
Al-
Cu
-Si
Al-
Si
ε 2+
γ 1δ 1
68
6p10
δ +
(Si)
γ 1 +
η?
U5
δ +
β γ
1 + κ
?U6
ε 2 +
γ1
δ 1+
(S
i)6
80
D1
δ +
γ 1
κ +
η?
U7
δ +
γκ
+ ε
67
5U8
δγ+
ε7
10
e 8
βγ 1
+ (
Cu)
55
9e 12
ζ 1+
µ 1ζ 2
57
0p
ε 2+
η 1ζ 1
59
0p12
lη 1
+ θ
59
1p
l +
ε2
η1
62
4p11
δκ
+ ε
+ η
?E3
L +
ε2
η 1 +
(S
i)6
08
U9
γ 1 +
(C
u)
α 2
36
3p13
ζ 1ζ 2
+δ
53
0e ?
lθ
+ (
Al)
548.2
e 14
ε 2ζ 1
+δ
56
0e 11
η 1+
θη 2
56
3p
L +
η1
θ +
(S
i)5
73
U10
ε 2+
η 1ζ 1
+ (
Si)
59
0D2
ε 2δ 1
+ζ 1
+(S
i)5
60
D3
β γ 1
+κ
+ (
Cu)
54
5E4
Lθ
+ (
Al)
+ (
Si)
52
4E5
γ 1+η
+(S
i)
l (
Al)
+ (
Si)
57
7e 10
η' (
Si)
+ η'
'
46
7e
κ γ+
(Cu)
55
2e 13
η (
Si)
+ η
'
55
8e
η' +
εη'
'
57
0p
η +
εη'
62
0p
γ 1+
κ +
η
γ 1+δ
1+
(Si)
κ+
ε +
η
η 1+ζ
1+
(Si)
δ 1+
ζ 1 +
(S
i)
θ+(A
l)+
(Si)
γ 1+
(C
u)
+ α2
γ 1+
κ +
(C
u)
κ +
γ +
(C
u)
η 1+
θ+(S
i)
η+δ+
(Si)
γ 1+
δ+(S
i)γ 1
+ε2+(
Si)
L+ε2+(
Si)
δ +
γ 1+
η
β +
γ 1+
δβ
+ δ
+ κ
δ+
κ +
γ
δ +
κ +
η
δ +
γ 1+
ηη+
δ+ε
δ +
κ +
ε
γ +
κ +
εε 2
+η1+
(Si)
L+
η 1+(S
i)
ε 2+
ζ 1+
(S
i)ε 2+δ
1+
(Si)
L+
θ+(S
i)
β +
(Cu
) +κ
β +
γ 1+
κ
145
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
10
20
80 90
10
20
Cu 25.00Al 75.00Si 0.00
Cu 0.00Al 75.00Si 25.00 Data / Grid: at.%
Axes: at.%
(Si)
(Al)
650
64063
062061
0600
590
57056
055054
0
550
560
570
740
720
680
660640
620
600
580
700
θ
580
E5
Al
20
40
60
80
20 40 60 80
20
40
60
80
Cu Al
Si Data / Grid: at.%
Axes: at.%
(Cu)
β P2
P1
δ
η E2 U2
γ1
E1
U1
U3
U8
U9E5
(Al)θ
η1ε2
ε1
1400
1300
1200
1100
1000
900
800
700
600
(Si)
γ0
e4
p7p4
e1 p1 p2 e2p12 p13 e14
e10
e3
Fig. 3: Al-Cu-Si.
Liquidus projection of
the Al-rich corner
Fig. 2: Al-Cu-Si.
Liquidus surface
146
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
Cu 4.00Al 96.00Si 0.00
Al
Cu 0.00Al 96.00Si 4.00 Data / Grid: at.%
Axes: at.%
550
560
570
540
530
580
590
600
610
620
630
640
650
(Al)
Al
Cu 4.00Al 96.00Si 0.00
Al
Cu 0.00Al 96.00Si 4.00 Data / Grid: at.%
Axes: at.%
550
525
500475450425 400
(Si)
θ300350
Al
Fig. 4: Al-Cu-Si.
Solidus surface of the
(Al) solid solution
Fig. 5: Al-Cu-Si.
Solvus surface of the
(Al) solid solution
147
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Si
80
20
20
Cu Cu 60.00Al 40.00Si 0.00
Cu 60.00Al 0.00Si 40.00 Data / Grid: at.%
Axes: at.%
(Cu)
γ
κ
γ1
η" γ1+η"+(Si)
κ+η"+γ1
(Cu)+γ1
ε
κ+ε+
η"
δ1
η´´+ε
κ+γ1
(Cu)+κ
η´´+
(Si)
γ1+(Si)
Fig. 6: Al-Cu-Si.
Isothermal section at
400°C
148
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
Aluminium – Copper – Terbium
Riccardo Ferro, Paola Riani
Literature Data
This evaluation is part of the MSIT Ternary Evaluation Program and incorporates and continues the critical
evaluation made by [1992Ran] considering a fast amount of new published data. Different compounds have
been identified and their crystal structures determined: TbCuAl [1968Dwi, 1973Oes, 1995Kuz] (the high
pressure modification of this compound and its structure were reported by [1987Tsv1, 1987Tsv2]),
TbCuAl3 [1988Kuz], TbCu4Al [1978Tak], Tb2Cu7Al10 [1982Pre, 1995Kuz], TbCu4Al8 [1979Fel,
1995Kuz], TbCu6Al6 [1980Fel] and TbCu0.9Al2.1 [1995Kuz].
The alloys were prepared under protective atmosphere by arc melting or induction melting followed by
homogenization heat treatments. High pressure modification of TbCuAl was made by rapid quenching from
the melt under a pressure of 7.7 GPa.
A partial isothermal section, from 0 to 50 at.% Tb, was built at 650°C or at 400°C in the Al-rich region by
[1995Kuz]. To this end 103 alloys were prepared by arc melting, under purified argon, from 99.5 mass%
Tb and 99.99 mass% Cu and Al. They were then annealed at 650 or 400°C for 1000h. Powder diffraction
techniques were used for phase and structure analysis. Lattice parameters trends for a number of solid
solutions have been reported. Differential thermal analysis was also used.
Binary Systems
The binary systems Al-Tb [2002Gro1], Al-Cu [2003Gro] and Cu-Tb [2002Gro2] are used as boundary
systems.
Solid Phases
Table 1 shows the crystal structure data of the solid phases. Following remarks may be useful.
In the determination of the isothermal section at 650°C of the Al-Cu-Tb system [1995Kuz] identified the
ThMn12 structure for a phase having a small range of compositions 1,Tb(CuxAl1–x)12 (0.4 x 0.43).
The ideal BaCd11 type structure corresponds to a tetragonal body-centered cell, in the space group I41/amd
with Ba in 4a and Cd in 4b, 8d and 32i. A co-ordination of 22 is observed around Ba, and from 10 to 14
around Cd. For Tb an orthorhombic variant of this structure was observed ( 2,TbCu6.4Al4.6 [1995Kuz])
with similar values of the co-ordination numbers.
[1995Kuz] discussing the structure of the Tb compounds proposed the structure La3Al11 type for the
4,Tb3Cu1.2Al9.8 composition, instead of the BaAl4 type previously proposed by [1988Kuz] for TbCuAl3.
For the 5 TbCu0.9Al2.1 phase the hR36 PuNi3 type (or NbBe3 type) was observed [1992Kuz, 1995Kuz]. In
a refinement of the structure of ~HoCuAl2 the following positions were observed [1992Kuz] in the space
group R3m: Ho in 3a + 6c, Cu in 6c, Al in 3b and (Al+Cu) in 18h. The large atoms have co-ordination
number 16 and 20, and the others 12.
Isothermal Sections
A partial isothermal section (from 0 to 50 at.% Tb) was built by [1995Kuz] at 650°C but at 400°C in the
Al-rich region. These are reported in Figs. 1 and 2. Note that in the Cu-Tb edge the Tb2Cu9 compound,
assumed by analogy with the other heavy rare earths, is missing; moreover the TbCu5 compound dissolves
up to ~45 at.% Al. Several ternary phases have been identified; the 2,TbCu6.4Al4.6, 5,TbCu0.9Al2.1 and
4,Tb3Cu1.2Al9.8 (La3Al11 type) phases have been described as point compounds [1995Kuz, 1996Ste]. For
the other phases the following composition ranges have been proposed: 1,Tb(CuxAl1–x)12 with
0.40 x 0.43 (ThMn12 type); 3,Tb2Cu17–xAlx with 5.5 x 9.4 (Th2Zn17 type) and 6,TbCu2–xAlx with
0.85 x 1.15 (Fe2P or ZrNiAl type) [1995Kuz]. Subsequently [1996Ste], using single crystal X-ray
149
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
diffraction, determined the crystal structure of 3 Tb2Cu8Al9 as pertaining to Th2Zn17 type and refined by
the Rietveld method the atomic parameters of 2 TbCu6.4Al4.6, a new structural type related to the BaCd11
type. This phase was previously identified by [1995Kuz].
Notes on Materials Properties and Applications
[1977Bas] found that Neel temperature of the solid solution of the binary compound TbCu with Al
decreases and the Curie temperature reverses sign at 16 at.% Al, i.e. at this composition a transformation
from anti-ferromagnetic to ferromagnetic occurs.
[1998Jav] studied the magnetic properties of the RCuAl (R = Y, Ce to Sm, Gd to Tm and Lu) intermetallic
compounds by means of susceptibility, magnetization and specific heat measurements and observed a
magnetic ordering at low temperatures in most of these materials: PrCuAl and NdCuAl showed an
antiferromagnetic behavior while in the heavy rare-earth compounds (R=Gd-Er) a ferromagnetic coupling
was found.
Magnetization and neutron diffraction measurements conducted by [1996Ehl] showed that TbCuAl orders
ferromagnetically with a Curie temperature of TC = 51K.
References
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1968Dwi] Dwight, A.E., Mueller, M.H., Conner, R.A.Jr., Downey, J.W., Knott, H., “Ternary
Compounds with the Fe2P-Type Structure”, Trans. Met. Soc. AIME, 242, 2075-2080 (1968)
(Crys. Structure, Experimental, 14)
[1973Oes] Oesterreicher, H., “Structural and Magnetic Studies on Rare Earth Compounds RNiAl and
RCuAl”, J. Less-Common Met., 30, 225-236 (1973) (Crys. Structure, Experimental, Magn.
Prop., 21)
[1977Bas] Basha, A.F., Chechernikov, V.I., Sinanyan, L.G., Tavansi, A., “Magnetic Properties of
Certain Terbium Alloys with CsCl Structure”, Sov. Phys. - JETP, 45(4), 808-809 (1977)
(Crys. Structure, Experimental, Magn. Prop., 5)
[1978Tak] Takeshita, T., Malik, S.K., Wallace, W.E., “Crystal Structure of RCu4Ag and RCu4Al (R =
Rare Earth) Intermetallic Compounds”, J. Solid State Chem., 23, 225-229 (1978) (Crys.
Structure, Experimental, 8)
[1979Fel] Felner, I., Nowik, I., “Magnetism and Hyperfine Interactions of 57Fe, 151Eu, 155Gd, 161Dy,166Er and 170Yb in RM4Al8 Compounds (R = Rare Earth or Y, M = Cr, Mn, Fe, Cu), J. Phys.
Chem. Solids, 40, 1035-1044 (1979) (Crys. Structure, Experimental, Magn. Prop., 8)
[1980Fel] Felner, I., “Crystal Structure of Ternary Rare Earth - 3d Transition Metal Compounds of the
RT6Al6 Type”, J. Less-Common Met., 72, 241-249 (1980) (Crys. Structure, Experimental,
10)
[1982Pre] Prevarskiy, A.P., Kuz'ma, Yu.B., “New Compounds with Th2Sn17 Type Structure in
REM-Al-Cu Systems”, Russ. Metall., (6), 155-156 (1982) (Crys. Structure, Experimental,
5)
[1985Mur] Murray, J.L., “The Aluminum-Copper System”, Int. Met. Rev., 30(5), 211-233 (1985) (Equi
Diagram, Crys. Structure, Review, 230)
[1987Tsv1] Tsvyashchenko, A.V., Fomicheva, L.N., “High Pressure Synthesis and Structural Studies of
Rare Earth (R) Compounds RCuAl”, J. Less-Common Met., 134, L13-L15 (1987) (Crys.
Structure, Experimental, 10)
[1987Tsv2] Tsvyashchenko, A.V., Fomicheva, L.N., “New Polymorphic Modifications of the
Compounds RTAl (R = r.e.m., T = Cu, Ni)”, Inorg. Mater., 23, 1024-1027 (1987), translated
from Izv. Akad. Nauk SSSR, Neorg. Mater., 23, 1148-1152 (1987) (Crys. Structure,
Experimental, 15)
150
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
[1988Kuz] Kuz'ma, Yu.B., Stel'makhovich, B.M., “New RCuAl3 Compounds (R = Tb, Dy, Ho, Er, Tm,
Yb) and Their Crystal Structure” (in Russian), Dop. Akad. Nauk Ukr. SSR B, Geol. Khim.
Biol., (11), 40-43 (1988) (Crys. Structure, Experimental, 4)
[1989Mee] Meetsma, A., de Boer, J.L., van Smaalen S., “Refinement of the Crystal Structure of
Tetragonal Al2Cu”, J. Solid State Chem., 83(2), 370-372 (1989) (Crys. Structure,
Experimental, 17)
[1992Kuz] Kuz’ma, Yu.B., Stel’makhovych, B.M., Babizhetsky, V.S., “New Compounds with
PuNi3-Type Structure in REM-Cu-Al Systems”, Russ. Metall., (2), 196-199 (1992),
translated from Izv. Ross. Akad. Nauk, Metally, (2), 227-230 (1992) (Experimental, Crys.
Structure, 4)
[1992Ran] Ran, Q., ”Aluminium-Copper-Terbium”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), Materials Science International Services GmbH, Stuttgart;
Document ID: 10.12789.1.20 (1992) (Equi. Diagram, Assessment, 10)
[1994Mur] Murray, J.L., “Al-Cu (Aluminum-Copper)” in “Phase Diagrams of Binary Copper Alloys”,
Subramanian, P.R., Chakrabarti, D.T., Laughlin, D.E. (Eds.), ASM International, Materials
Park, OH, 18-42 (1994) (Equi. Diagram, Review, 226)
[1994Sub] Subramanian, P.R., Laughlin, D.E., “The Cu-Tb (Copper-Terbium) System”, in “Phase
Diagrams of Binary Copper Alloys”, Subramanian, P.R., Chakrabarti, D.T., Laughlin, D.E.
(Eds.), ASM International, Vol. 10, 428-431 (1994) (Equi. Diagram, Review, 23)
[1995Kuz] Kuz’ma, Yu.B., Stel’makhovych, B.M., Vasyunyk, M.I., “Phase Equilibria and Crystal
Structure of Tb-Cu-Al Compounds in the Region up to 50 at.% Tb” (in Russian), Russ.
Metal., (5) 130-136 (1995), translated from Izv. Ross. Akad. Nauk, Metally, (5), 162-169
(1995) (Equi. Diagram, Crys. Structure, Experimental, *, #, 13)
[1996Ehl] Ehlers, G., Maletta, H., “Magnetic Order in TbNiAl and TbCuAl Intermetallic
Compounds”, Z. Phys. B: Condens. Matter, 99(2), 145-150 (1996) (Experimental, Magn.
Prop., 8)
[1996Goe] Goedecke, T., Sommer, F., “Solidification Behaviour of the Al2Cu Phase”, Z. Metallkd.,
87(7), 581-586 (1996) (Experimental, Crys. Structure, 8)
[1996Ste] Stel’makhovych, B.M., Aksel’rud, L.G., Kuz’ma, Yu.B., “The Tb2(Cu0.47Al053)17 and
Tb(Cu0.58Al0.42)11 Aluminides and Their Crystal Structures”, J. Alloys Compd., 234,
167-170 (1996) (Experimental, Crys. Structure, 4)
[1998Jav] Javorský, P., Havela, L., Sechovský, V., Michor, H., Jurek, K., “Magnetic Behaviour of
RCuAl Compounds”, J. Alloys Compd., 264, 38-42 (1998) (Experimental, Crys. Structure,
15)
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264(1-2), 201-208 (1998) (Experimental,
Equi. Diagram, 25)
[2002Gro1] Gröbner, J., Matusch, D., Turkevich, V., “Al-Tb (Aluminium - Terbium)” MSIT Binary
Evaluation Program, in MSIT Workplace, MSI, Stuttgart, Document ID: 20.12179.1.20,
MSI, Stuttgart, (2002) (Equi. Diagram, Assessment, 5)
[2002Gro2] Gröbner, J., Matusch, D., Turkevich, V., “Cu-Tb (Copper - Terbium)” MSIT Binary
Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science
International Services GmbH, Stuttgart; Document ID: 20.13888.1.20 (2002) (Equi.
Diagram, Assessment, 5)
[2002Gul] Gulay, L.D., Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. ”Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2003Gro] Gröbner, J, “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart, to be published, (2003) (Equi. Diagram, Assessment, 68)
151
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Al)
< 660.45
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2],
0 to 2.48 at.% Cu [Mas2]
(Cu)
< 1084.62
Cu1–xAlx
cF4
Fm3m
Cu
a = 361.46
a = 361.52
a = 365.36
at 25°C [Mas2],
0 to 19.7 at.% Al [Mas2]
no appreciable solubility of Tb [1994Sub]
x = 0, quenched from 600°C [2003Gro]
x = 0.152, quenched from 600°C [2003Gro]
( Tb)
1356-1289
cI2
Im3m
W
a = 402 [Mas2]
copper solubility in the different terbium
form is very small or negligible
( Tb)
1289-(–53)
hP2
P63/mmc
Mg
a = 360.55
c = 569.66
at 25°C [Mas2]
the and ’ designations have been
interchanged in some compilations
( ’Tb)
< –53
oC4
Cmcm
’Dy
a = 360.5
b = 624.4
c = 570.6
[Mas2]
, Cu3Al(h)
1049-559
cI2
Im3m
W a = 295.64
70.6 to 82 at.% Cu [1985Mur], [1998Liu]
at 672°C
2, Cu100–xAlx< 363
t**
TiAl3long period
super-lattice
a = 366.8
c = 368.0
22 x 23.5 [1985Mur]
76.5 to 78.0 at.% Cu
at 76.4 at.% Cu
(subcell only)
0, Cu100–xAlx Cu~2Al
1037-800
cI52
I43m
Cu5Zn8
37 x 31.5 [Mas2],
38 x 32 [1998Liu]
1, Cu9Al4< 890
cP52
P4m
Cu9Al4 a = 870.23
a = 870.68
62 to 68 at.% Cu
[Mas2, 1998Liu];
from single crystal [V-C2] at 68 at.% Cu
from single crystal [V-C2]
, Cu100–xAlx< 686
hR*
R3m
a = 1226
c = 1511
40.7 x 38.1 [1985Mur]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C]
1, Cu100–xAlx958-848
cubic? 40.6 x 37.9
59.4 to 62.1 at.% Cu [Mas2, 1985Mur]
2, Cu2–xAl
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.78 x 0.45
55 to 61 at.% Cu [Mas2, 1985Mur, V-C2],
NiAs in [Mas2,1994Mur]
152
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
1, Cu47.8Al35.5 (h)
590-530
oF88 - 4.7
Fmm2
Cu47.8Al35.5
a = 812
b = 1419.85
c = 999.28
55.2 to 59.8 at.% Cu [Mas2, 1994Mur]
structure: [2002Gul]
2, Cu11.5Al9 (r)
< 570
oI24 - 3.5
Imm2
Cu11.5Al9
a = 409.72
b = 703.13
c = 997.93
55.2 to 56.3 at.% Cu
[Mas2, 1985Mur]
structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu
[Mas2, 1985Mur]
Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu [V-C2]
, CuAl2< 591
tI12
I4/mcm
CuAl2 a = 606.7
c = 487.7
31.9 to 33.0 at.% Cu [12994Mur]
32.4 to 32.8 at.% Cu at 250°C [1996Goe]
single crystal [V-C2,1989Mee]
TbAl4<420
oI20
Imma
Al4U
a = 443.0
b = 626.1
c = 1370.6
[V-C2]
not confirmed, possibly impurity stabilized
phase
TbAl3<1108
hR36
R3m
BaPb3
a = 617.6
c = 2116.5
[Mas2]
TbAl3(HP) hR60
R3m
Al3Ho
a = 609.5
c = 3596
High-pressure phase
[V-C2]
Tb(CuxAl1–x)2
TbAl2< 1514
cF24
Fd3m
Cu2Mg
a = 778.9
a = 785.9
0 x 0.2 at 650°C [1995Kuz]
at x = 0.2 [1995Kuz]
at x = 0 [Mas2]
TbAl
< 1079
oP16
Pmma
AlEr
a = 583
b = 1137
c = 562
[V-C2]
Tb3Al2< 986
tP20
P42/mnm
Al2Zr3
a = 825.5
c = 756.8
[V-C2]
Tb2Al
< 960
oP12
Pnma
Co2Si
a = 659.2
b = 511.3
c = 944.0
[Mas2]
Tb3Al cP4
Pm3m
AuCu3
a = 479.4 [V-C2]
not confirmed, possibly impurity stabilized
phase
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
153
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
TbCu1–xAlxTbCu
900-(–157)
cP2
Pm3m
CsCl
a = 347.8 to 348.4
a = 348.0
a = 349.9
a = 351.8
a = 354.0
a = 354.7
a = 354.9
a = 356.8
at x = 0 [1994Sub]
0 x 0.35? (annealing temperature not
specified) [1977Bas]
at x = 0
at x = 0.1
at x = 0.2
at x = 0.3
at x = 0.4
at x = 0.5 [1977Bas]
0 x 0.5 at 650°C [1995Kuz]
at x = 0.5
TbCu
< –157
tP2
P4/mmm
MnHg
a = 345.7
c = 349.8
[V-C2]
Tb(Cu1–xAlx)2
TbCu2
< 870
oI12
Imma
CeCu2
a = 433.2
b = 683.0
c = 732.7
a = 431.0
b = 682.5
c = 732.0
0 x 0.075 at 650°C [1995Kuz]
at x = 0.075 [1995Kuz]
at x = 0 [1994Sub]
Tb2Cu7
890-850
? high temperature phase [1994Sub]
Tb2Cu9
< 950
? [1994Sub]
TbCu5(h)
940-895
TbCu5–xAlx
TbCu4Al
hP6
P6/mmm
CaCu5
a = 496 to 503
c = 409 to 415
a = 529.1
c = 409.3
a = 507.3
c = 414.9
[1994Sub] [V-C2]
A homogeneity range of 0 x 2.8
reported by [1995Kuz] and presented in his
isothermal section at 650°C. However, at
650°C, TbCu5, should be metastable
according to [2002Gro2]
at x = 2.8 [1995Kuz]
at x = 1 [1978Tak]
TbCu5
< 895
cF24
F43m
AuBe5
a = 704.1 [1994Sub] [V-C2]
TbCu7
?–~700
hP8
P6/mmm
TbCu7
(closely related to
CaCu5)
a = 494.2
c = 416.4
high temperature phase
[1994Sub]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
154
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
Tb6Cu23 cF116
Fm3m
Th6Mn23
a = 1220 high pressure phase, prepared at 7.7 GPa
[1994Sub]
* 1, Tb(CuxAl1–x)12
TbCu4Al8
TbCu6Al6
tI26
I4/mmm
ThMn12
a = 868.8
c = 511.9
a = 874.2
c = 514.2
a = 875.2
c = 513.4
a = 865.7
c = 505.3
0.40 x 0.43 [1995Kuz] at 650°C
at x = 0.40 [1995Kuz]
at x = 0.43 [1995Kuz]
observed on a sample at x = 0.33 [1979Fel]
observed on a sample at x = 0.5 annealed at
~800°C [1980Fel]
* 2, TbCu6.4Al4.6 oF*
Fddd
Tb(Cu0.58Al0.42)1
1
a =1427.9
b =1489.2
c = 656.44
[1995Kuz]
* 3, Tb2(CuxAl1–x)17 hR57
R3m
Th2Zn17
a = 871.7
c = 1271
a = 885.2
c = 1289
a = 882.6
c = 1286
0.45 x 0.676 at 650°C [1995Kuz]
at x = 0.676 [1995Kuz]
at x = 0.45 [1995Kuz]
observed on a sample at x = 0.41 annealed
at 500°C [1982Pre]
* 4 Tb3Cu1.2Al9.8 oI12
Immm
La3Al11
a = 422.9
b = 1252.8
c = 994.0
[1995Kuz]
* 5 TbCu0.9Al2.1 hR36
R3m
PuNi3
a = 547.5
c = 2539.3
[1995Kuz]
* 6 TbCu2–xAlx hP9
P62m
Fe2P or ZrNiAl
a = 701.0 to 704.1
c = 405.0 to 405.4
a = 704.06
c = 404.39
0.85 x 1.15 [1995Kuz]
at x = 1 [1968Dwi]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
155
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Tb
20
40
60
80
20 40 60 80
20
40
60
80
Tb Cu
Al Data / Grid: at.%
Axes: at.%
τ1
ε2
δγ1
β
τ4
τ5
τ2
τ3
TbAl3
TbAl2
TbAl
τ6
TbCu TbCu2 TbCu5
(Cu)
L
(Al)
?
Fig. 1: Al-Cu-Tb.
Partial isothermal
section at 650°C
10
20
30
40
50
10 20 30 40 50
50
60
70
80
90
Tb 60.00Cu 0.00Al 40.00
Tb 0.00Cu 60.00Al 40.00
Al Data / Grid: at.%
Axes: at.%
η
τ1
θτ4
TbAl3
(Al)Fig. 2: Al-Cu-Tb.
Partial isothermal
section at 400°C
156
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
Aluminium – Copper – Titanium
Rainer Schmid-Fetzer
Literature Data
Phase equilibria in the entire ternary system have been studied by [1971Vir] and [1973Mar]. [1971Vir]
prepared the samples either from the metallic elements (99.9% Cu, 99.99% Al, Ti purity not given) or from
a Cu50Ti50 master alloy. About 100 alloys were melted in an electric arc furnace under pure Ar. Most of the
samples weighed 10 g, but 7 in the Ti corner and 11 in the Cu corner were prepared as 100 g bars. The
Cu-rich bars were homogenized at 850°C for 21 h, quenched in water, rolled or hammered and annealed at
different temperatures. The Ti-rich samples were hot rolled at 950°C and heat treated (950°C/15 min or
900°C/30 min or 850°C/1 h or 800°C/2 h). About 10 of the other samples were examined in the as-cast state.
Samples were examined by metallography for constructing the partial isothermal sections at 950, 900, 850
and 800°C, by X-ray diffraction for determining the crystal structures of the ternary compounds, and by
direct observation of the melting for the determination of the liquidus surface. [1973Mar] homogenized
more than 200 samples at 800°C for 600 to 900 h and at 500°C for 1000 h, and determined the 800 and
500°C isothermal sections by microstructural and X-ray analysis. Phase regions of controversy between
[1971Vir] and [1973Mar] were studied by [1997Dur] with 1 g samples arc melted from high purity metals
(Ti 99.9%, Cu and Al 99.999%), heat treated in evacuated silica tubes at 850°C for 120 h or even 430 h and
water quenched. Phase analysis was done by XRD, optical microscopy and SEM/EDX and electron
microprobe. Similar experiments were reported by [1994Lug] with 35 samples equally distributed in the
range > 50 mass% Ti, heated at 600 and 800°C for 6 h and 12 h. Many investigators give information on
phase equilibria in limited regions [1936Nis, 1943Mon, 1958Vig1, 1958Vig2, 1958Vig3, 1966Zwi,
1960Emo, 1962Pan, 1963Luz, 1965Ram2, 1966Zwi, 1969Hor, 1979Sei, 1981Sei, 1983Bru, 1984Guz,
1985Guz, 2000Kai, 2001Liu]. From differential thermal and microstructural analysis [1936Nis] derived
two partial polythermal sections at 6 and 10 mass% Cu with up to 1 mass% Ti. A ternary eutectic was
concluded. Phase equilibria were reported by [1958Vig1] at 850 and 500°C in the Cu corner from
microhardness measurements and by [1958Vig2] for some more temperatures by metallography. Including
the results of [1958Vig1] and [1958Vig2], [1958Vig3] reported details on their studies. 30 alloy
compositions with up to 7 mass% Ti and 14 mass% Al were studied by metallography and microhardness
measurements. The samples were heat treated at different temperatures: 300°C/360 h, 400°C/240 h, 500°C/
200 h, 600°C/100 h, 700°C/50 h, 800°C/20 h, 850°C/16 h, 900°C/10 h, 950 and 980°C/7 h. From the results,
phase relationships were established for the examined composition range for 980, 700, 600 and 500°C and
reported as isothermal sections, 1, 2 and 3 mass% Ti vertical sections and a diagram of joint solubility of Ti
and Al in (Cu) from 500 to 980°C. From microradiography and microhardness determinations, [1960Emo]
plotted sketches for the Cu corner which do not agree everywhere with the phase rule. [1962Pan] studied
the microstructure of 15 alloy compositions at different temperatures and constructed the partial (up to 3
mass% Ti) polythermal sections at 5 and 10 mass% Al. [1963Luz] determined the solubility of Cu in a
Ti-6Al (mass%) alloy by electrical resistance measurements. Samples with 0.5, 0.8, 1.2, 1.6, 2.0, 2.4, 3.4
and 5% Cu were vacuum melted, homogenized 125 h at 930°C, furnace cooled, annealed at 600°C/105 h,
700°C/100 h, 800°C/75 h and finally quenched. [1969Hor] studied the effect of Ti on the temperature of the
1+(Cu) eutectoid reaction in the Al-Cu system by differential dilatometry, differential thermal analysis
and metallography. [1979Sei] determined the liquidus surface of the Ti-CuAl-FeAl partial system by
microstructure and melting observation. [1981Sei] studied the composition of platelet precipitates in a
91.2Ti-6.9Al-1.9Cu (at.%) alloy after annealing at 475°C/8 h or 600°C/140 h using TEM with EDX and
found the Al-content much reduced (< 2.5 at.% Al with 24.5 at.% Cu) compared to the Ti-matrix (7.5 to 8.5
at.% Al with 0.8 at.% Cu). [2000Kai] prepared arc melted samples in the range Ti-(35-47)Al -(0.5-12)Cu
(at.%), checked for low levels of O (250 ppm) and N (50 ppm), wrapped in Mo foil and heated in evacuated
silica capsules at 1000°C for 168 or 504 h, at 1200°C for 168 h, and at 1300°C for 24 h. Microstructural and
electron microprobe analysis of the two- and three-phase samples was performed.
157
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
Equilibrium relations in the Cu corner were studied by metallography, electron microprobe analysis, X-ray
diffraction, electron diffraction and electrical resistivity measurements for four temperatures between 600
and 850°C [1983Bru]. Samples were prepared from metals of 99.5% purity by induction melting under Ar
in a water-cooled Cu boat, holding the melt in levitation for several minutes, casting in a Cu mold, and
annealing 2 h at 900°C. The samples were then further annealed 25 h at 850°C, or 50 h at 800°C, or 30 days
at 700°C, or 30 days at 600°C. [2001Liu] studied Al-Cu-rich two-phase equilibria with Ti addition of 0.5
and 1 at.%, heated at 700 and 800°C for 48 to 100 h in two Cu-Ti / Cu-Al-Ti diffusion couples using SEM/
EDX.
[1984Guz] and [1985Guz] reported the determination of the solubility of Ti and Cu in (Al) at 500°C by
microstructural and X-ray analysis and electrical resistance measurements, on samples of 40 alloy
compositions ranging from 0 to 0.35 Ti and from 0 to 3.5 mass% Cu. All other works are on ternary
compounds and their crystal structures. The first work in this ternary system at all, [1935Bac1, 1935Bac2],
reports studies of crystal structure of two single-crystal ternary compounds by Laue and rotating single
crystal diffraction. For the two phases, cubic and hexagonal unit cells were revealed, respectively, and
lattice spacing parameters were given. [1957Gru] claimed to have found a body-centered tetragonal phase
in a copper base alloy with 1.13Ti-0.69Al (mass%) by Debye-Scherrer X-ray diffraction. The sample was
prepared from electrolytic Cu and a master alloy by melting and holding at 1200°C and annealing 1000 h
at 500°C after casting. [1958Vig3] at 600°C observed a phase called containing >12.8 mass% Al and >3.5
mass% Ti and suggested it to be a ternary phase. Several ternary compounds and their structures were
reported by [1960Moe] and [1962Hei] (TiCu2Al) and [1964Sch] (TiCuAl, Ti2CuAl5, Ti25Cu4Al71,
Ti25Cu2Al73) without giving information on the experimental procedures. The crystal structure of the
compound TiCuAl was completely determined by [1964Kry] and [1964Rie] using powder X-ray
diffraction. [1964Mar] arc melted the component metals of 99.9% purity under He, annealed the sample
20 days at 800°C, followed by water quenching. The existence of the compound TiCu2Al was confirmed
by X-ray and microstructural analysis. [1965Ram1] made X-ray analysis of a sample Ti25Cu3Al72 after
annealing for 7.5 days at 700°C. This work was continued and extended to several other compositions with
different heat treatment. [1967Hof] prepared TiCu2Al by melting in evacuated silica ampoules and
determined the structure in the as-cast state. Both [1971Vir] and [1973Mar] observed three ternary
compounds, TiCuAl, TiCu2Al and Ti2CuAl5 with lattice parameters determined for TiCuAl [1973Mar] and
structures determined for all the three compounds [1971Vir]. [1973Mar] concluded homogeneity along a
line only, whereas [1971Vir] suggested remarkable homogeneity regions for all the three phases. The
homogeneity range of 1, TiCu2Al, was studied with XRD on arc melted samples, annealed at 800°C for
>72 h and finally at 600°C for only 48 h [1990Mey]. [1989Miz] found Ti(Cu1-xAlx)2 alloys annealed at
800°C for 24 h to be single phase 2 with C14 structure for 0.45 < x < 0.7 and measured the lattice
parameters, increasing slightly and linearly with x, the magnetic susceptibility and, for stoichiometric
TiCuAl, the specific heat at 1.5-6 K. Earlier reviews of the ternary system [1979Cha, 1979Dri] are mostly
based on the work of [1971Vir]. The extensive review by [1992Ran] forms an important basis for the
present assessment even though the conclusions had to be revised in view of more recent data.
Much of the more recent work in the Al-Cu-Ti system is devoted to the L12 type phase 3 [1989Maz,
1991Fra, 1991Hon, 1991Mab, 1991Nic, 1991Win, 1992Dur, 1992Ma, 1992Mor, 1992Pot, 1992Win,
1993Nak, 1997Fan], which is considered as an interesting low density intermetallic compound [1990Kum].
Improved mechanical properties of 3 as compared to TiAl3 are expected since the L12 structure has the
required five independent slip systems [1992Win].
A sample Ti23.8-Cu13.4-Al62.8 (all at.%) was found single phase 3 [1992Ma], and Ti25-Cu12.5-Al62.5
shows nearly no second phase after 48 h at 1150°C but about 5% CuAl2 in as-cast state [1993Nak].
Mechanical alloying of Ti25-Cu8-Al67 produced nanocrystalline disordered (Al) solid solution in which
simultaneously grain growth and transformation to L12 was observed upon tempering in the range
400-700°C [1997Fan]. Further studies on the L12 type phase 3 regard the solubility range at 1200°C
[1989Maz], lattice parameter variations [1991Fra], atomic locations and ordering behavior [1992Ma,
1992Mor, 1992Win], TiAl2 precipitates forming in L12 matrix [1992Pot], theoretical stability calculations
[1991Hon, 1991Fre], and mechanical properties [1991Nic, 1991Win].
158
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
Binary Systems
The three binary systems are accepted in the recently revised versions given in [2002Ans, 2003Gro,
2003Sch].
Solid Phases
Crystallographic data for all solid phases are given in Table 1. [1935Bac1] first reported two ternary
compounds, a cubic one and a hexagonal one. Neither composition was identified. From the structure type
and lattice parameters reported, however, these phases can be specified as TiCuAl [1964Kry, 1964Rie,
1964Sch, 1965Ram2] and Ti2CuAl5 [1964Sch, 1965Ram2, 1971Vir]. After the report of a CsCl type
structure for TiCu2Al [1960Moe], its crystallographic data have been determined further by [1962Hei,
1964Mar, 1965Ram2, 1967Hof]. Whereas [1960Moe, 1962Hei] and [1964Mar] gave the structure type as
CsCl, [1965Ram2] and [1967Hof] established the MnCu2Al structure and suggested that incomplete
ordering was the reason for reporting CsCl structure in earlier works. All three phases were also found by
[1971Vir] and [1973Mar] while constructing the isothermal sections at 800, 540 and 500°C. [1973Mar]
gave line-compound homogeneity ranges for TiCuAl and Ti2CuAl5 and a nearly linear range for TiCu2Al,
all with constant Ti content, whereas [1971Vir] also proposed considerable homogeneity regions for Ti for
all three phases. For Ti2CuAl5, the result of [1973Mar] is preferred, because 1) [1973Mar] investigated
more samples; 2) [1973Mar] was aware of the work of [1971Vir]; and 3) the homogeneity “areas” drawn
by [1971Vir] are not necessarily conclusions from experimental results. The homogeneity range for TiCuAl
from [1971Vir] is extended to include the composition after [1973Mar]. This is appropriate because the
structure determination of this phase was reported for the stoichiometric composition very close to the
Al-poor end of the range given by [1973Mar]. According to [1971Vir], the Ti2CuAl5 and TiCuAl phases
are formed by ternary peritectic reactions at 1280 and 1150°C, respectively. The compositions of the phases
taking part in the reactions make the peritectics improbable, but the stability of these two phases at these
temperatures, reflected in the assessed transition type reactions U1 and U3, is quite sure. As a consequence
a congruent melting is assumed to be likely for 3, Ti2CuAl5 (1350°C actually given by [1971Vir]) and 2,
TiCuAl ( 1160°C, slightly above max2). The congruent melting point for 1, TiCu2Al ( 1125°C) is from
[1971Vir], it must be above 1100°C.
The compound “Ti25Cu4Al71” has the ZrAl3 structure and is most probably a solid solution of Ti5Al11(h)
[1965Ram2]. The alloys Ti25Cu2Al73 [1964Sch] and Ti8CuAl23 [1965Ram1, 1965Ram2] have
compositions very close to the binary phase Ti9Al23 and an identical structure. They are therefore
considered to be solid solutions of this phase. [1957Gru] proposed the existence of another ternary phase of
a tetragonal body-centered lattice structure (a = 356, c = 463 pm) for which there is no further evidence.
The sample conditions suggest that this phase is most likely the binary TiCu4 phase.
The ternary phase called X, proposed by [1958Vig3], is considered not to be an additional phase, but to be
the TiCu2Al compound as indicated by the isothermal section of [1971Vir] and [1973Mar].
The (Ti,Al) phase referred to as 2 by [1971Vir] was not recognized as Ti3Al because the strong X-ray
reflections coincide with those of ( Ti). As a consequence “ 2” is Ti3Al in the low temperature isotherms,
but it has to be interpreted as ( Ti) in the liquidus projection.
The , Cu3Al(h) phase is claimed to be stabilized by solution of 5 at.% Ti (“Ti0.2Cu2.8Al”) and shown in
the “540°C” section of [1971Vir], whereas [1962Pan] have it decomposed at 560°C. The latter is accepted
since a large Ti-solubility of would be in conflict with the experimental partition ratio of Ti in the +(Cu)
equilibrium, which has an atomic value of about unity [2001Liu].
A high solubility of Al in a metastable ” ’ TiCu4” phase is suggested from a TEM study [1980Psh].
Invariant Equilibria
[1936Nis] suggested a ternary eutectic reaction in the Al-rich corner at 540°C: L (Al)+ +TiAl3 based on
his study of the partial vertical sections with 6 and 10 mass% Cu up to 10 mass% Ti
The vertical section at 1 mass% Ti of [1960Emo] demands a ternary reaction in the solid state at 570°C
where the phases (Cu), , 1 and TiCu4 participate, but the reaction type cannot be identified. This is in
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agreement with the 10 mass% Al partial vertical section of [1962Pan]. The extensive investigations of
[1971Vir] revealed two maxima, one eutectic, two peritectic and 18 transition reactions. Contrary to
[1936Nis], [1971Vir] gave the last reaction with liquid as a transition type, L+TiAl3 (Al)+ , at 555°C. The
result of [1936Nis] is more reliable since [1936Nis] used more samples (11) than [1971Vir] (2), and
[1936Nis] made both DTA and metallographic examinations. The new interpretation of the 2Ti phase and
its region of primary solidification as that of ( Ti) (see also”Solid Phases”), as well as the acceptance of the
new binary systems make the modification and introduction of several ternary reactions necessary, though
the work of [1971Vir] remains essential.
Two additional major changes made to the interpretation of [1971Vir] will be highlighted below. Firstly,
they plotted the liquidus surface with a small intersection of Ti2Cu and 2 primary phase fields. This is in
conflict with the recent experimental data on 1+Ti3Al equilibrium at 850°C [1997Dur]. This is resolved by
the modified reactions U8 and U9 in Table 2 and also an intersection of the 1 and Ti3Al primary phase fields
in Fig. 1, following essentially the interpretation of [1997Dur]. This modification is still in accord with the
actual data points of [1971Vir]. The second major point is that both [1971Vir] and [1997Dur] show an
intersection of the ( 0, 2) and the 2 primary fields from 930 to 830°C [1971Vir]. This is in conflict with
the fact that none of the Al-Cu solid phases is in equilibrium with 2 but rather the 1+ 3 equilibrium is
firmly established at 850°C [1997Dur] and also at lower temperature [1973Mar, 1971Vir]. This requires the
intersection of 1 and 3 fields shown in Fig. 2 and the reaction U15, above 850°C. Reflecting the above
comments and the additional influence of the generally not well known solid solution ranges in this ternary
it must be stated that there are still substantial uncertainties in the invariant equilibria. It is therefore
refrained from updating and reproducing the bulky Scheil reaction scheme of [1971Vir]. The reactions
which are at least partially experimentally verified are listed in Table 2 with the compositions of the liquid
taken from the modified liquidus surface of [1971Vir] shown in Fig. 1.
Liquidus Surface
The liquidus surface given in Fig. 1 is mainly based on the work of [1971Vir], but, as discussed in the
section “Invariant Equilibria”, it is changed in some areas and adapted to the accepted binary systems and
the primary solidification of ( Ti) instead of Ti3Al. Large regions of primary crystallization were observed
for the ternary compounds TiCu2Al ( 1), TiCuAl ( 2) and Ti2CuAl5 ( 3). [1979Sei] confirms the liquidus
surface of [1971Vir] on the Ti - CuAl section.
A possible inconsistency around the reaction U5 should be noted. This U5-liquid may well be located
relative to the composition of the solid phases in a manner to flip the reaction to L+ 3 TiAl+ 2, reversing
the temperature levels of U3 and U5. Also an additional maximum in the line L+ 3+ 2 is well conceivable.
This cannot be resolved without better experimental data on the solid phase compositions of 3+ 2+TiAl.
Isothermal Sections
Partial isothermal sections at 1300, 1200 and 1000°C in Figs. 2, 3, 4 show the ( Ti)+( Ti)+TiAl equilibria
and also with 2, measured by microprobe [2000Kai]. It is established that the Cu-solubility in the
( Ti)+TiAl+( Ti) phases decreases in that sequence. The extension of the 3 phase is much larger at
1200°C (25-29 at.% Ti taken from graph, but 11.5 at.% width along a constant line of 27 at.% Ti in text)
[1989Maz] compared to the 800°C data of [1973Mar].
The isothermal section at 800°C is constructed in Fig. 5, mainly based on [1973Mar]. The composition
ranges of the ternary compounds are estimated from different works, as discussed in the section “Solid
Phases”. The Ti3Al+ 1 equilibrium is firmly established by [1973Mar, 1994Lug] and also at 850°C by
[1997Dur]. Therefore the conflicting Ti2Cu+ 2 equilibrium, deduced by [1971Vir] from their liquidus
surface, is not accepted. This is corroborated by the Ti2Cu+ 1+Ti3Al equilibrium found at 800°C
[1994Lug]. The 1+ 2+ 3 equilibrium is also confirmed at 850°C [1997Dur] and the fact that the
stoichiometric TiCuAl composition of 2 is not single phase but 2+ 1. By contrast, [1989Miz] found a
larger single phase region of 2 ranging from at least 30 to 47 at.% Al at constant 33.3 at.% Ti. The 2+ 1+ 3
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equilibrium is from [1965Ram2], whereas [1997Dur] did find the 1+ 1+ 3 equilibrium at 850°C. They
could not detect the 1 or 2 phase in equilibrium with 1+ 3 (as shown in Fig. 5) and question the existence
of the binary 1/2 phase.
The isothermal section at 500°C, Fig. 6, is again mainly based on [1973Mar] and other data given in “Solid
Phases”, and it includes the accepted information from [1971Vir]. Their isothermal section at ”about
540°C” [1971Vir] is not reproduced here since it does not contain additional viable information. It was not
based on experiments at 540°C but was deduced from the liquidus surface and the solution ranges of solid
phases appear schematic and exaggerated. The appearance of phase well below the binary decomposition
temperature, as shown in the “540°C” section of [1971Vir], cannot be accepted since the partition ratio of
Ti in the (Cu)+ and + 1 equilibria is close to unity, as discussed above [2001Liu]. The extension of the
1 phase field given by [1990Mey] (50-53Cu, 24.5-25.25Ti, 25-22.2 Al (at.%)) is smaller than in both Fig.
6 and Fig.5, however, their annealing at 600°C was for only 48 h and their plotted ”phase diagram” violates
rules, for example the three-phase field (Cu) + TiCu4 + 1 does not touch the 1 phase field [1990Mey],
suggesting a possibly larger solution range. [1958Vig3] presented isothermal diagrams for the Cu-rich
corner in the temperature range 980 to 500°C with a three-phase equilibrium (Cu)+ + TiCu4. This is not
accepted because it contradicts other works [1971Vir, 1973Mar, 1983Bru, 1990Mey] which support each
other in the (Cu)+ 1 equilibrium. The precipitate found by [1981Sei] in a ( Ti) matrix is probably a
metastable “Ti3Cu” phase, also found by [1994Lug] at 600°C and initially at 800°C (6 h), but disappearing
after 12 h at 800°C. The low Cu-solubility in TiAl3 in equilibrium with (Al) is supported by TEM/EDX
analysis of precipitates, Ti24.5Al75.1Cu0.4, after annealing a Ti0.6-Al96.7-Cu2.7 (at.%) arc melted alloy
at 425°C up to 475 h [1997Mah].
Sections at 900 and 950°C in the Ti corner from [1971Vir] suffer from the uncertain identification of ( Ti)
vs Ti3Al and are not given here. Their section at 800°C is integrated into Fig. 5.
Temperature – Composition Sections
Several partial vertical sections were investigated. The 10 mass% Cu polythermal section with up to 1
mass% Ti drawn in Fig. 7 originates from [1936Nis]. The 6 mass% Cu partial section has the same phase
relation [1936Nis]. The isopleths given by [1958Vig3] and [1960Emo] are very tentative and do not agree
fully with the phase rule. Therefore, they are not considered as reliable. The 5 mass% Al vertical cut with
up to 3 mass% Ti of [1962Pan] shows simple extensions of phase regions from the binary edge. The 10
mass% Al vertical cut is given in Fig. 8.
Miscellaneous
Amorphous Ti40Cu50Al10 alloy was produced by rapid solidification and crystallizes to TiCu+ 1
[1994Myu], in accord with the assessed phase diagram. [1985Vas] studied age-hardening behavior in
Al-Cu-Ti alloys.
References
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1935Bac1] Bachmetew, E.F., Sevastianow N.G., Kotow, N.I., ”On the X-Ray Structure Analysis of
Crystal Formation in the Ternary System Cu-Al-Ti” (in German), Acta Physicochimica
URSS, 2(5), 561-566 (1935) (Crys. Structure, Experimental, 8)
[1935Bac2] Bachmetew, E.F., Sevastianow, N.G., Kotow, N.I., “Crystal Formations in ’Copper Alutite’
(Copper-Aluminium-Titanium) and the X-ray Analysis of their Structure” (in Russian),
Zh. Fiz. Khim., 6(5), 593-596 (1935) (Crys. Structure, 9)
[1936Nis] Nishimura, H., Kagiwada, N., “Effect of Titanium upon the Aluminium Alloys”
(in Japanese), Suiyokwai-Shi, 9(2), 95-98 (1936) (Equi. Diagram, Experimental, 6)
[1943Mon] Mondolfo, L.F., “Al-Cu-Ti”, in “Metallography of Aluminium Alloys”, N. Y., 88-89 (1943)
(Equi. Diagram, Review, 1)
161
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
[1957Gru] Gruhl, W., Codier, H., “On a Hardenable Copper-Titanium-Aluminium Alloy”
(in German), Metall, 11, 928-933 (1957) (Crys. Structure, Experimental, 11)
[1958Vig1] Vigdorovich, V.N., “The Construction of Conodes from Microhardness Determinations in
the Two-Phase Regions of the State Diagrams of Metallic Systems” (in Russian), Dokl.
Akad. Nauk SSSR, 120, 1027-1030 (1958) (Equi. Diagram, Experimental, 15)
[1958Vig2] Vigdorovich, V.N., Krestovnikov, A.N., Mal'tsev, M.V., “Microhardness Investigation of
Solid Solutions of Ternary Systems” (in Russian), Izv. Akad. Nauk SSSR, Otd. Tekh. Nauk,
(3), 110-113 (1958) (Equi. Diagram, Experimental, 8)
[1958Vig3] Vigdorovich, V.N., Mal'tsev M.V., Krestovnikov, A.N., “Investigation of the Structure and
Properties of Alloys of the Ternary System Copper-Aluminium-Titanium” (in Russian), Izv.
Vyss. Uchebn. Zaved., Tsvetn. Metall., (2), 142-152 (1958) (Equi. Diagram, Experimental,
11)
[1960Emo] Emod, G., “The Phase Diagram of Copper-Aluminium-Titanium Alloys”, Ontoede, 11,
178-183 (1960) (Equi. Diagram, Experimental, 8)
[1960Moe] Moeller, K., Arndt, H.H., “A Ternary Phase in the Ternary System
Aluminium-Copper-Titanium” (in German), Naturwissenschaften, 47, 224 (1960) (Crys.
Structure, Experimental, 0)
[1962Hei] Heine, W., Zwicker, U., “Phases of B2-Structure Type (CsCl-Type) in Ternary Systems
with Copper and Nickel” (in German), Naturwissenschaften, 49, 391 (1962) (Crys.
Structure, Experimental, 1)
[1962Pan] Panseri, G., Leoni, M., “Studies on Complex Al Bronze: Ternary Equilibrium Diagram
Cu-Al-Ti” (in Italian), Alluminio, 31, 461-470 (1962) (Equi. Diagram, Experimental, 0)
[1963Luz] Luzhnikov, L.P., Novikova V.M., Mareev, A.P., “Solubility of Beta Stabilisers in
Alpha-Ti”, Metalloved. Term. Obrab. Met., 2, 78-81 (1963) (Equi. Diagram, Experimental,
4) (Experimental, 4)
[1964Kry] Krypyakevich, P.I., Markiv V.Y., Troyan, A.A., “Crystal Structures of the Ternary
Compounds TiCuAl and TiNiAl” (in Ukrainian), Dop. Akad. Nauk Ukr. RSR, A, Fiz.-Mat.
Tekh. Nauki, (7), 922-924 (1964) (Crys. Structure, Experimental, 8)
[1964Mar] Markiv, V.Ya., Voroshilov, Yu.V., Kripyakevich P.I., Cherkashin, E.E., “New Compounds
of the MnCu2Al and MgZn2 Types Containing Aluminium and Gallium”, Sov.
Phys.-Crystallogr., 9, 619-620 (1965), translated from Kristallografiya, 9, 737-738 (1964)
(Crys. Structure, Experimental, 4)
[1964Rie] Rieger, W., Nowotny, H., Benesovsky, F., “Crystal-Chemical Investigations in Systems
with Transition Metal Elements, (Cu,Ag) and (Al,Ga)” (in German), Monatsh. Chem., 95,
1573-1576 (1964) (Crys. Structure, Experimental, 7)
[1964Sch] Schubert, K., Meissner, H.G., Raman, A., Rossteutscher, W., “Several Structural Data of
Metallic Phases (9)” (in German), Naturwissenschaften, 51, 287 (1964) (Crys. Structure)
[1965Ram1] Raman, A., Schubert, K., “The Constitution of some Alloys Related to TiAl3, II,
Investigations in Some T4-Al-Si and T4...6-In Systems” (in German), Z. Metallkd., 56, 44-52
(1965) (Crys. Structure, Experimental, 16)
[1965Ram2] Raman, A., Schubert, K., “On the Crystal Structure of some Alloy Phases Related to TiAl3,
III, Investigations in Several T-Ni-Al and T-Cu-Al Alloy Systems” (in German),
Z. Metallkd., 56, 99-104 (1965) (Crys. Structure, Experimental, 14)
[1966Zwi] Zwicker, U., Kalsch, E., Nishimura, T., Ott, D., Seilstorfer, H., “The Effect of Additions on
the Equilibria of Cu-Rich Cu-Ti Alloys” (in German), Metall, 20(12), 1252-1255 (1966)
(Equi. Diagram, Crys. Structure, Review, 9)
[1967Hof] Hofer, G., Stadelmaier, H.H., “Cobalt, Nickel and Copper Phases of the Ternary MnCu2Al
Type” (in German), Monatsh. Chem., 98, 408-411 (1967) (Crys. Structure, Experimental,
9)
[1969Hor] Hori, M., “On the Effects of Chromium and Titanium on the Eutectoid Transformation of
Copper-Aluminium Binary Alloy” (in Japanese), J. Jpn Inst. Met., 33, 1073-1077 (1969)
(Experimental, 4)
162
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Al–Cu–Ti
[1971Vir] Virdis P., Zwicker, U., “Phase Equilibria in the Copper-Titanium-Aluminium System”
(in German), Z. Metallkd., 62, 46-51 (1971) (Equi. Diagram, Crys. Structure, Experimental,
*, #, 18)
[1973Mar] Markiv, V.Ya., Burnashova, V.V., Ryabov, V.R., “Ti-Fe-Al, Ti-Ni-Al and Ti-Cu-Al
Systems” (in Russian), Metallofizika, (46), 103-110 (1973) (Equi. Diagram, Experimental,
*, #, 24)
[1979Cha] Chang, Y.A., Neuman, J.P., Mikula, A., Goldberg, D., “Al-Cu-Ti”, INCRA Monograph
Series 6. Phase Diagrams and Thermodynamic Properties of Ternary Copper-Metall
Systems, 243-248 (1979) (Equi. Diagram, Crys. Structure, Review, 4)
[1979Dri] Drits, M.E., Bochvar, N.R., Guzei, L.S., Lysova, E.V., Padezhnova, E.M., Rokhlin, L.L.,
Turkina, N.I., “Cu-Al-Ti” in “Binary and Multicomponent Copper-Base Systems”
(in Russian), Nauka, Moskow, 82-83 (1979) (Equi. Diagram, Review, 4)
[1979Sei] Seibold, A., “Investigation of Titanium Ternary and Quaternary Systems for Developing
Technically Applicable Cast Alloys” (in German), Thesis, Univ. Erlangen-Nürnberg,
Erlangen, Germany (1979) (Experimental, 70)
[1980Psh] Pshenina, L.S., Korotaev, A.D., “Influence of Alloying on the Development of Precipitation
in Cu-Ti Alloys”, Sov. Phys. J. (Engl. Trans.), 23(4), 293-299 (1980) (Experimental, 23)
[1981Sei] Seibold A., von Heimendahl M., “Microanalytical Study of Titanium-Copper (Ti2Cu)
Precipitates in Titanium-Copper-Aluminum Alloys” (in German), Z. Metallkd., 72(10),
725-727 (1981) (Experimental, 14)
[1983Bru] Brun, J.-Y., Hamar-Thibault, S.-J., Allibert, C.-H., “Cu-Ti and Cu-Ti-Al Solid State Phase
Equilibria in the Cu-Rich Region”, Z. Metallkd., 74, 525-529 (1983) (Equi. Diagram,
Experimental, 24)
[1984Guz] Guzyi, L.S., Makanov, U.M., Orinbekov S.B., Sokolovskaya, E.M., “The Solubility of
Copper and Titanium in Aluminium” (in Russian), Vestn. MGU Khim., 25, 567-570 (1984)
(Equi. Diagram, Experimental, 14)
[1985Guz] Guzyi, L.S., Kuzhecov, V.N., Orinbekov, S.B., Sokolovskaya, E.M., Makanov, U.M.,
“Phase Equilibria in the Aluminium Corner of the Al-Si-Cu-Ti System” (in Russian), Vestn.
MGU Khim., 26, 393-395 (1985) (Equi. Diagram, Experimental, 5)
[1985Mur] Murray, J.L., “The Aluminium-Copper System”, Int. Met. Rev., 30, 211-233 (1985) (Equi.
Diagram, Crys. Structure, Review, 230)
[1985Vas] Vassel, A., “The Age-Hardening Behaviour in Ti-Cu-Al Ternary Titanium Alloys”,
Conference: “Titanium-Science and Technology”, (DGM), 1481-1486 (1985)
(Experimental, Mechan. Prop., 7)
[1989Maz] Mazdiyasni, S., Miracle, D.B., Dimiduk, D.M., Mendiratta, M.G., Subramanian, P.R.,
“High Temperature Phase Equilibria of the Ll2 Composition in the Al-Ti-Ni, Al-Ti-Fe and
Al-Ti-Cu Systems”, Scr. Metall., 23(3), 327-331 (1989) (Equi. Diagram, Experimental,10)
[1989Mee] Meetsma, A., de Boer, J.L., van Smaalen, S., “Refinement of the Crystal Structure of
Tetragonal Aluminum-Copper (Al2Cu)”, J. Solid State Chem., 83(2), 370-372 (1989) (Crys.
Structure, Experimental, 17)
[1989Miz] Mizutani, U., Hasegawa, M., Ohashi, S., “Enhanced Itinerant Paramegantism in C14-Type
Laves Ti(Cu1-xAlx)2Ti, x = 0.45-070, Alloys”, Solid State Commun., 69(4), 403-406 (1989)
(Crys. Structure, Experimental, 20)
[1990Kum] Kumar, K.S., “Ternary Intermetallics in Aluminium-Refractory Metal-X Systems (X = V,
Cr, Mn, Fe, Co, Ni, Cu, Zn)”, Int. Mater. Rev., 35(6), 293-327 (1990) (Crys. Structure, Equi.
Diagram, Review, 158)
[1990Mey] Meyer Zu Reckendorf, R., Schmidt, P.C., Weiss, A., “The Ternary Systems Cu-Ti-Al and
Cu-Zr-Al Around the Heusler Phase Composition Cu2XAl (X = Ti, Zr): Phase Diagrams
and Hydrogen Solubility”, J. Less-Common Met., 159, 277-289 (1990) (Equi. Diagram,
Experimental, 41)
[1990Sch] Schuster, J.C., Ipser, H., “Phases and Phase Relations in the Partial System TiAl3-TiAl”,
Z. Metallkd., 81, 389-396 (1990) (Equi. Diagram, Experimental, 33)
163
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
[1991Ell] Ellner, M., Kolatschek, K., Predel, B., “On the Partial Atomic Volume and the Partial Molar
Enthalpy of Aluminium in Some Phases with Cu and Cu3Au Structures”, J. Less-Common
Met., 170, 171-184 (1991) (Experimental, Crys. Structure, 57)
[1991Fra] Frazier, W. E., Benci, J. E., “Crystal Structure and Phase Relationships in As-Cast and Melt
Spun Titanium Aluminide (Al3Ti) and Al3Ti Plus Copper”, Scr. Metal. Mater., 25(10),
2267-2272 (1991) (Crys. Structure, Experimental, 6)
[1991Fre] Freeman, A.J., Hong, T., Lin, W., Xu, J.-H., “Phase Stability and Role of Ternary Additions
on Electronic and Mechanical Properties of Aluminum Intermetallics”, in ”High-Temp.
Ordered Intermetallic Alloys IV”, Mater. Res. Soc. Symp. Proc., 213, 3-18 (1991) (Theory,
Mechan. Prop., 57)
[1991Hon] Hong, T., Freeman, A.J., “Effect of Ternary Additions on the Structural Stability and
Electronic Structure of Intermetallic Compounds: Al3Ti+Cu”, J. Mater. Res., 6(2), 330-338
(1991) (Crys. Structure, Theory, 36)
[1991Mab] Mabuchi, H., Nakayama, Y., “Development of Al-Ti-X Ternary L12 Intermetallic
Compounds” (in Japanese), Bull. Jpn. Inst. Met., 30(1), 24-30 (1991) (Equi. Diagram,
Experimental)
[1991Nic] Nic, J.P., Zhang, S., Mikkola, D.E., “Alloying of Al3Ti with Mn and Cr to Form Cubic
L1(2) Phases”, in “High-Temp. Ordered Intermetallic Alloys IV”, Mater. Res. Soc. Symp.
Proc., 213, , 697-702 (1991) (Crys. Structure, Experimental, Mechan. Prop., 12)
[1991Win] Winnicka, M.B., Varin, R.A., in “High-Temp. Ordered Intermetallic Alloys IV”, Mater. Res.
Soc. Symp. Proc., 213, 709-714 (1991) (Experimental, Mechan. Prop., 8)
[1992Dur] Durlu, N., Inal, O.T., “L12-Type Ternary Titanium Aluminides as Electron Concentration
Phases”, J. Mater. Sci., 27(12), 3225-3230 (1992) (Assessment, Crys. Structure, 41)
[1992Kat] Kattner, U.R., Lin, J. C., Chang, Y.A., “Thermodynamic Assessment and Calculation of the
Ti_Al System”, Metall. Trans. A, 23(8), 2081-2090 (1992) (Assessment, Calculation, Equi.
Diagram, Thermodyn., #, *, 51)
[1992Ma] Ma Y., Gjonnes J., “Ternary Atom Location In L12-Structured Intermetallic Phases:
Al62.5+xTi25-Y(Fe, Ni or Cu)12.5-Z Using Alchemi.”, J. Mater. Res., 7, 8 (1992) (Crys.
Structure, Experimental, 30)
[1992Mor] Morris, D.G., Gunter, S., “Ordering Ternary Atom Location and Ageing in Ll2
Trialuminide Alloys”, Acta Metall. Mat., 40(11), 3065-3073 (1992) (Crys. Structure,
Experimental, 23)
[1992Pot] Potez, L., Loiseau, A., Naka, S., Lapasset, G., “A Study of Al2Ti Precipitation in a
Cu-Modified Al3Ti Alloy”, J. Mater. Res., 7(4), 876-882 (1992) (Crys. Structure, Equi.
Diagram, Experimental, 30)
[1992Ran] Ran, Q., Stadelmaier, H.H., “Aluminium-Copper-Titanium”, MSIT Ternary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 10.16867.1.20 (1992) (Equi. Diagram, Crys.
Structure, Thermodyn., Experimental, Review, 31)
[1992Win] Winnicka, M.B., Varin, R.A., “Microstructure and Ordering of L12 Titanium
Trialuminides.”, Metall. Trans. A, 23A(11), 2963-2972 (1992) (Crys. Structure,
Experimental, 24)
[1993Nak] Nakayama, Y., Mabuchi, H., “Formation of Ternary L1(2) Compounds in Al3Ti-Base
Alloys”, Intermetallics, 1, 41-48 (1993) (Crys. Structure, Equi. Diagram, Experimental,
Mechan. Prop., 40)
[1994Ali] Alisova, S.P., Lutskaya, N.V., Kobylkin, A.N., Budberg, P.B., “TiFe-Ti2Cu Section of the
Ti-Fe-Cu System. Conditions of the Formation of Ti2Fe Compound”, Russ. Metall., 5,
121-123 (1994) (Experimental, Equi. Diagram, 8)
[1994Lug] Lugscheider, E., Koetzing, B., “Thermochemical and Thermophysical Properties of Alloys
in the Systems Ti-Al-Cu, Ti-Al-Ni, Ti-Al-Pd, Ti-Cu-Pd and Ti-Ni-Pd” (in German), Final
Report BMFT 03K07049 and COST 507-I, RWTH Aachen, (1994) (Equi. Diagram,
Experimental, Phys. Prop., 27)
164
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Al–Cu–Ti
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)”, in “Phase Diagrams of Binary Copper
Alloys”, Subramanian, P.R., Chakrabarti, D.J., Laughlin, D.E., (Eds.), ASM International,
Materials Park, OH, 18-42 (1994) (Equi. Diagram, Crys. Structure, Thermodyn., Review, #,
*, 226); similar to [1985Mur]
[1994Myu] Myung, W-N., Battezzati, L., Baricco, M., Aoki, K., Inoue, A., Matsuo, T., “Kinetic and
Thermodynamic Aspects of Crystallization in Cu-Ti-Ni and Cu-Ti-Al Metallic Glasses”,
Mater. Sci. Eng. A, A179-180, 371-375 (1994) (Crys. Structure, Experimental, Kinetics,
Thermodyn., 8)
[1997Dur] Durlu, N., Gruber, U., Pietzka, M.A., Schmidt, H., Schuster, J.C., “Phases and Phase
Equilibria in the Quaternary System Ti-Cu-Al-N at 850 degree C”, Z. Metallkd., 97(5),
390-400 (1997) (Crys. Structure, Equi. Diagram, Experimental, Review, *, 32)
[1997Fan] Fan, G.J., Song, X.P., Quan, M.X., Hu, Z.Q., “Mechanical Alloying and Thermal Stability
of Al67Ti25M8 (M=Cr,Zr,Cu)”, Mater. Sci. Eng. A, A231, 111-116 (1997) (Crys. Structure,
Experimental, 22)
[1997Mah] Mahidhara, R.K., “Elevated-Temperature Coarsening Behaviour in Aluminum Alloys”,
J. Mater. Eng. Perform., 6, 102-105 (1997) (Crys. Structure, Experimental, 10)
[1997Sah] Sahu, P.Ch., Chandra Shekar, N.V., Yousuf, M., Govinda Rajan, K., “Implications of a
Pressure Induced Phase Transition in the Search for Cubic Ti3Al”, Phys. Rev. Lett., 78(6),
1054-1057 (1997) (Crys. Structure, Experimental, 20)
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264, 201-208 (1998) (Equi. Diagram,
Experimental, #,*,25)
[1999Abe] Abe, E., Ohnuma, M., Nakamura, M., “The Structure of a New -Phase Formed During the
Early Stage of Crystallization of Ti-48 at.% Al Amorphous Film”, Acta Mater., 47(13),
3607-3616 (1999) (Crys. Structure, Experimental)
[1999Nag] Nagarjuna, S., Sarma, D.S., “On the Variation of Lattice Parameter of Cu Solid Solution
with Solute Content in Cu-Ti Alloys”, Scr. Mater., 41(4), 359_363 (1999) (Experimental,
Crys. Structure, 12)
[2000Dub] Dubrovinskaia, N., Dubrovinsky, L., Vennstrom, M., Anderson, Y., Abrikosov, I.,
Eriksson, O., “High-Pressure, High-Temperature In-Situ Study of Alloys: Ti3Al”, Proc.
Disc. Meet. Thermodyn. Alloys, 23 , (2000) (Thermodyn.)
[2000Kai] Kainuma, R., Fujita, Y., Mitsui, H., Ishida, K., “Phase Equilibria Among Alfa (hcp), Beta
(bcc) and Gama (L1(0)) Phases in Ti-Al Base Ternary Alloys”, Intermetallics, 8, 855-867
(2000) (Crys. Structure, Equi. Diagram, Experimental, 29)
[2000Ohn] Ohnuma, I., Fujita, Y., Mitsui, H., Ishikawa, K., Kainuma, R., Ishida, K., “Phase Equilibria
in the Ti-Al Binary System”, Acta Mater., 48, 3113-3123 (2000) (Calculation, Equi.
Diagram, Experimental, Thermodyn., #, *, 37)
[2001Bra] Braun, J., Ellner, M., “Phase Equilibria Investigations on the Aluminium-Rich Part of the
Binary System Ti-Al”, Metall. Mater. Trans. A, 32A, 1037-1048 (2001) (Crys. Structure,
Equi. Diagram, Experimental, #, *, 34)
[2001Liu] Liu, X.J., Wang, C.P., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Stability Among the
(A1), (A2), and (D83) Phases in the Cu-Al-X System”, J. Phase Equilib., 22, 431-438
(2001) (Equi. Diagram, Experimental, 14)
[2002Ans] Ansara, I., Ivanchenko, V., “Cu-Ti (Copper-Titanium)”, MSIT Binary Evaluation Program,
in MSIT Workplace, Effenberg, G. (Ed.), Materials Science International Services GmbH,
Stuttgart; Document ID: 20.11457.1.20, (2002) (Equi. Diagram, Review, 26)
[2002Gul] Gulay, L.D, Harbrecht, B, “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. “Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2003Gro] Groebner, J., “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 68)
165
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
[2003Sch] Schmid-Fetzer, R., “Al-Ti (Aluminium-Titanium)”, MSIT Binary Evaluation Program, in
MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 86)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]Comments/References
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 pure Al at 25°C [Mas2]
0 to 0.6 at.% Ti [1992Kat],
0 to 2.48 at.% Cu [Mas2]
(Cu)
< 1084.62
cF4
Fm3m
Cu
a = 361.46
a = 361.52 +
25.26xAl
a = 361.47 +
33.38xTi
at 25°C [Mas2],
0 to 19.7 at.% Al [Mas2]
melting point [1994Mur]
[1991Ell], quenched from 600°C, xAl = 0
to 0.152
0 to 8 at.% Ti at 885°C [Mas2]
0 to 0.8 at.% Ti at 450°C [1999Nag]
( Ti)
1670 - 882
cI2
Im3m
W
a = 330.65 pure Ti [Mas2]
0 to 44.8 at.% Al [1992Kat] possible
ordering from A2 to B2 ( 2Ti) [2000Ohn]
dissolves 13.5 at.% Cu at 100°C [Mas2]
( Ti)
< 1490
hP2
P63/mmc
Mg
a = 295.06
c = 468.35
pure Ti(r) at 25°C [Mas2]
0 to 51.4 at.% Al [1992Kat]
dissolves 1.6 at.% Cu at 790°C [Mas2]
, Cu3Al(h)
1049 - 559
cI2
Im3m
W a = 295.64
70.6 to 82 at.% Cu [1985Mur]
at 672°C in +(Cu) alloy (Ti free)
[1998Liu]
dissolves at least 0.81 at.% Ti [2001Liu]
1 cF16
Fm3m
BiF3
a = 585 Metastable [1994Mur]
supercell of
2, Cu1-xAlx< 363
-
TiAl3long period
super-lattice
-
a = 366.8
c = 368.0
0.22 x 0.235 [Mas, 1985Mur]
76.5 to 78.0 at.% Cu
at 76.4 at.% Cu
(subcell only)
0, Cu1-xAlx Cu-2Al
1037-800
cI52
I43m
Cu5Zn8
- 0.31 x 0.40 [Mas2]
0.32 x 0.38 [1998Liu]
dissolves at least 0.78 at.% Ti [2001Liu]
1, Cu9Al4< 890
cP52
P3m
Cu9Al4
a = 870.23
a = 870.68
62 to 68 at.% Cu [Mas2, 1998Liu];
powder and single crystal [V-C2]
from single crystal [V-C]
dissolves at least 0.78 at.% Ti [2001Liu]
, Cu1-xAlx< 686
hR*
R3m
a = 1226
c = 1511
0.38 x 0.407 [Mas2, 1985Mur]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C]
166
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
1, Cu1-xAlx958-848
cubic? - 0.379 x 0.406
59.4 to 62.1 at.% Cu [Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.47 x 0.78
55.0 to 61.1 at.% Cu, [Mas, 1985Mur,
V-C2], NiAs in [Mas2, 1994Mur]
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2
Cu47.8Al35.5
a = 812
b = 1419.85
c = 999.28
55.2 to 59.8 at.% Cu [Mas2, 1994Mur]
structure: [2002Gul]
2, Cu11.5Al9(r)
<570
oI24 - 3.5
Imm2
Cu11.5Al9
a = 409.72
b = 703.13
c = 997.93
55.2 to 56.3 at.% Cu, [Mas2, 1985Mur]
structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]
Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu
[V-C2]
Cu2Al3 hP5
P3m1
Ni2Al3
a = 410.6
c = 509.4
Metastable [1994Mur]
~40 to 50 at.% Cu
, CuAl2< 591
tI12
I4/mcm
CuAl2 a = 606.7
c = 487.7
31.9 to 33.0 at.% Cu
[1994Mur]
single crystal
[V-C2, 1989Mee]
’ tP6
distorted CaF2
a = 404.82
c = 581.17
Metastable [1994Mur]
Ti3Al
< 1164
(up to 10 GPa at RT)
hP8
P63/mmc
Ni3Sn
a = 580.6
c = 465.5
a = 574.6
c = 462.4
~20 to 38.2 at.% Al, [1992Kat]
DO19 ordered phase (” 2-Ti3Al”)
[1997Sah]
at 22 at.% Al [L-B]
at 38 at.% Al [L-B]
Ti3Al (I)
15 to > 41 GPa
hP16
P63/mmc
TiNi3
a = 531.2
c = 960.4
[1997Sah] at 16 GPa,
not confirmed by [2000Dub] (0-35 GPa,
25-2250°C)
TiAl
< 1463
tP4
P4/mmm
AuCu
a = 400.0
c = 407.5
a = 398.4
c = 406.0
46.7 to 66.5 at.% Al [1992Kat]
50 to 62 at.% Al at 1200°C [2001Bra]
L10 ordered phase (” -TiAl”)
at 50.0 at.% Al [2001Bra]
at 62.0 at.% Al [2001Bra]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]Comments/References
167
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
TiAl2< 1199
oC12
Cmmm
ZrGa2
tP4
P4/mmm
AuCu
tI24
I41/amd
HfGa2
tP32
P4/mbm
Ti3Al5
a = 1208.84
b = 394.61
c = 402.95
a = 403.0
c = 395.5
a = 397.0
c = 2497.0
a = 1129.3
c = 403.8
chosen stoichiometry, [1992Kat]
summarizing several phases:
metastable modification of TiAl2 , only
observed in as-cast alloys [2001Bra];
listed as TiAl2(h) by [1990Sch]
(66 to 67 at.% Al, 1433-1214°C)
Ti1-xAl1+x ; 63 to 65 at.%Al at 1250°C,
stable range 1445-1170°C [2001Bra];
listed as othorhombic, Pmmm, with
pseudotetragonal cell by [1990Sch]
(range ~1445-1424°C).
at 1300°C [2001Bra]
stable structure of TiAl2 <1216
[2001Bra];
listed as TiAl2(r) by [1990Sch]
Ti3Al5, stable below 810°C [2001Bra];
“Ti2Al5”
1416 - 990
tetragonal
superstructure of
AuCu-type
[2001Bra]
tI16
ZrAl3
tP28
P4/mmm
“Ti2Al5”
a* = 395.3
c* = 410.4
a* = 391.8
c* = 415.4
a = 391.7
c = 1652.4
a = 390.1
c = 1660
a = 390.53
c = 2919.63
chosen stoichiometry, [1992Kat]
summarizing several Al-Ti phases:
Ti5Al11
stable range 1416- 995°C [2001Bra]
66 to 71 at.% Al at 1300°C [2001Bra]
(including the stoichiometry Ti2Al5!);
[1990Sch] claimed: 68.5 to 70.9 at.% Al
and range 1416 - 1206°C;
at 66 at.% Al [2001Bra]
* AuCu subcell only
at 71 at.% Al [2001Bra]
* AuCu subcell only
Cu free [1965Ram2]
6 at.% Cu [1965Ram2]
“Ti4CuAl11”
“Ti2Al5”
~1215-985°C [1990Sch];
included in homogeneity region of
Ti5Al11 [2001Bra]!
TiAl3 (h)
< 1393
tI8
I4/mmm
TiAl3(h) a = 384.9
c = 860.9
74.2 to 75.0 at.% Al, [1992Kat]
74.5 to 75 at.% Al,
at 1200°C [2001Bra] DO22 ordered phase
stable above 735°C (Al-rich) [2001Bra]
TiAl3 (l)
< 950 (Ti-rich)
tI32
I4/mmm
TiAl3 (l)
a = 387.7
c = 3382.8
74.5 to 75 at.% Al [2001Bra]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]Comments/References
168
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
TiAl3 (m) cP4
Pm3m
AuCu3
a = 397.2 metastable, from splat cooling
obtained at 85 at.% Al [2001Bra]
Ti52Al48 cP20
P4132
Mn
a = 690 metastable phase precipitating in early
stage from amorphous thin film after
anneal 1 h, 525°C [1999Abe]
Ti2Cu
< 1012
tI6
I4/mmm
MoSi2
a = 295.3
c = 1073.4
[Mas2, V-C2, 1994Ali]
dissolves -8 at.% Al
(Ti,Al)2Cu [1971Vir]
TiCu
< 982
tP4
P4/nmm
TiCu
a = 310.8 to 311.8
c = 588.7 to 592.1
48 to 52 at.% Cu [Mas2, V-C2]
Ti3Cu4
< 925
tI14
I4/mmm
Ti3Cu4
a = 313.0
c = 1994
[Mas2, V-C2]
Ti2Cu3
< 875
tP10
P4/nmm
Ti2Cu3
a = 313
c = 1395
[Mas2, V-C2]
TiCu2
890-870
oC12
Amm2
VAu2
a = 436.3
b = 797.7
c = 447.8
[Mas2, V-C2]
TiCu4
885 - 400
oP20
Pnma
ZrAu4
a = 452.5
b = 434.1
c = 1295.3
~ 78 to ~ 80.9 at.% Cu [Mas2, V-C2]
TiCu4
500
tI10
I4/m
MoNi4
~ 78 to ~ 80.9 at.% Cu [Mas2]
* 1, TiCu2Al
1125
cF16
Fm3m
MnCu2Al
a = 601
a = 601.9
[1965Ram2]
[1997Dur]
with homogeneity range
[1971Vir, 1973Mar]
L21 ordered phase
* 2, TiCuAl
< 1200
hP12
P63/mmc
MgZn2
a = 502.6
c = 808.4
a = 503
c = 811
a = 506
c = 814
[1964Kry], with homogeneity range
[1971Vir, 1973Mar], stable at 1200°C
[2000Kai]
C14 type phase
Ti33Cu37Al30
[1989Miz]
Ti33Cu20Al47
[1989Miz]
* 3, Ti2CuAl51350
cP4
Pm3m
Cu3Al
a = 392.7 [1965Ram2], linear homogeneity range
with constant Ti [1973Mar]
melting [1971Vir]
L12 ordered phase
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]Comments/References
169
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
Table 2: Invariant Equilibria
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Ti
L “Ti2Al5” + 3 ? max1 L 65 8 27
L + “Ti2Al5” TiAl3 + 3 1280 U1 L 70 8 22
L + “Ti2Al5” TiAl + 3 ? U2 L 61 9 30
L ( Ti) + 2 1155 max2 L 30 27 43
L + ( Ti) TiAl + 2 1150 U3 L 39 15 46
L 2 + 1 1100 max3 L 28 46 26
L (Cu) + 1 1020 max4 L 6 76 18
L + (Cu) + 1 1010 U4 L 25 68 7
L + TiAl 2 + 3 1000 U5 L 41 19 40
L + 0 + 1 1000 U6 L 36.94 57.83 5.23
L + ( Ti) Ti2Cu + ( Ti) 980 U7 L 10 27 63
L + 2 ( Ti) + 1 970 U8 L 18 41 41
L +( Ti) Ti2Cu + 1 965 U9 L 16 42 42
L + Ti2Cu TiCu + 1 940 U10 L 7 52 41
L + 0 1 + 1 920 U11
L + TiCu Ti3Cu4 + 1 910 U12 L 2 63 35
L + Ti3Cu4 TiCu2 + 1 900 U13
L + (Cu) TiCu4 + 1 870 U14 L 2 71 27
L TiCu2 + TiCu4 + 1 860 E1 L 2 66 32
L + 2 1 + 3 860 U15
L + 1 1 + 2 820 U16
L + 1 3 + 2 810 U17
L + 2 1 + 3 610 U18 L 64 34 2
L + 1 + 3 580 U19 L 68 30 2
L + 3 + TiAl3 570 U20 L 74 24 2
L (Al) + + TiAl3 540 E2 L 82 17 1
170
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
20
40
60
80
20 40 60 80
20
40
60
80
Ti Cu
Al Data / Grid: at.%
Axes: at.%
U3
max2
τ3
Ti3Al
τ2
max3
τ1
TiCu
Ti2Cu
(βTi)
"Ti2Al5"
(αTi)
TiAl
(Cu)
max4
e, 1032
p, 1037
p, 958
e, 848
p, 624
p, 591η
1
θ
e, 548.2
(Al)
p, 1393
p, 1416
p, 1463
p, 1490
e, 1005 e, 960p, p, e,p,
TiCu2Ti3Cu4 βTiCu4
E2
U20U1
U2
max1
U5
ε2
ε1U11
γ0U6
U4
β
U12 E1 U14
U10U9
U8
U7
U19
U18
U16
U15
U13
U17
925 890 875885
Fig. 1: Al-Cu-Ti.
Liquidus surface
40
50
60
10 20
40
50
60
Ti 65.00Cu 0.00Al 35.00
Ti 35.00Cu 30.00Al 35.00
Ti 35.00Cu 0.00Al 65.00 Data / Grid: at.%
Axes: at.%
TiAl
(βTi)
(αTi)
Fig. 2: Al-Cu-Ti.
Partial isothermal
section at 1300°C
171
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Ti
40
50
60
10 20
40
50
60
Ti 65.00Cu 0.00Al 35.00
Ti 35.00Cu 30.00Al 35.00
Ti 35.00Cu 0.00Al 65.00 Data / Grid: at.%
Axes: at.%
TiAl
(βTi)
(αTi) τ2
40
50
60
10 20
40
50
60
Ti 65.00Cu 0.00Al 35.00
Ti 35.00Cu 30.00Al 35.00
Ti 35.00Cu 0.00Al 65.00 Data / Grid: at.%
Axes: at.%
Ti3Al
TiAl
τ2
Fig. 3: Al-Cu-Ti.
Partial isothermal
section at 1200°C
Fig. 4: Al-Cu-Ti.
Partial isothermal
section at 1000°C
172
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
20
40
60
80
20 40 60 80
20
40
60
80
Ti Cu
Al Data / Grid: at.%
Axes: at.%
τ2
τ1
TiAl
β,TiCu4
(Cu)
γ1
δ
ζ2
η2
θTiAl2
TiAl3
(Al)
Ti3Al
(αTi)
Ti2CuTiCu
Ti3Cu4
Ti2Cu3
τ3
20
40
60
80
20 40 60 80
20
40
60
80
Ti Cu
Al Data / Grid: at.%
Axes: at.%
τ2
TiAl
TiAl2
TiAl3
L
ε2
γ1
γ0
β
(Cu)
τ3
τ1
"Ti2Al5"
Ti3Al
(αTi)
TiCuTi3Cu4
Ti2Cu3Ti2Cu β,TiCu4(βTi)
Fig. 6: Al-Cu-Ti.
Isothermal section at
500°C
Fig. 5: Al-Cu-Ti.
Isothermal section at
800°C
173
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Ti
500
600
Ti 0.00Cu 4.50Al 95.50
Ti 0.60Cu 4.50Al 94.90Ti, at.%
Tem
pera
ture
, °C
540
L+(Al)L+TiAl3
L
L+(Al)+TiAl3
(Al)+θ+TiAl3
0.40.2
400
500
600
700
800
900
1000
1100
Ti 3.45Cu 76.00Al 20.55
Ti 0.00Cu 79.30Al 20.70Cu, at.%
Tem
pera
ture
, °C
L
β
(Cu)+β
(Cu)+γ1
(Cu)+γ1+TiCu2Al
(Cu)+β+TiCu2Al
β+TiCu2Al
570
7977 78
Fig. 7: Al-Cu-Ti.
Partial vertical
section with constant
10 mass% Cu
Fig. 8: Al-Cu-Ti.
Partial vertical
section with constant
10 mass% Al
174
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Yb
Aluminium – Copper – Ytterbium
Gabriele Cacciamani and Paola Riani
Literature Data
The Al-Cu-Yb system has been previously assessed by [1992Ran] and, recently, by [2003Ria], in the
framework of a general review of the R-Cu-Al (R = rare earth) systems.
At low Yb concentrations (< 33 at.% Yb) several ternary phases are present, which often show line
solubility due to substitution between Al and Cu. Phase equilibria at 600°C have been studied by
[1993Ste1].
Binary Systems
The binary systems Al-Cu, Al-Yb and Cu-Yb assessed by [2003Gro, 2003Ria], [2002Bod] and [2002Rog]
are accepted here as boundary sub-systems.
Solid Phases
Crystal structure data are reported in Table 1. Appreciable ternary extensions of the binary compounds and
seven ternary phases are present in the Al-Cu-Yb system for x(Yb) < 0.33.
YbCu5 (hexagonal, CaCu5 type) dissolves up to 35 at.% Al. A cubic structure, AuBe5 type, was also
obtained at high pressure in the Cu-Yb system [1996He, 2002Rog]. At room conditions substitution of Cu
by Al is reported to stabilize the hexagonal structure [1998He].
At nearly equiatomic composition 1 (ZrNiAl type, related to Fe2P type) [1968Dwi, 1973Oes, 1974Fer,
1993Ste1] shows a small solubility range. At high pressure it transforms to the cubic MgCu2 type structure
[1987Tsv1, 1987Tsv2].
2 (YbCu0.9Al2.1, PuNi3 type), nearly stoichiometric, has been identified by [1992Kuz] and confirmed by
[1993Ste1].
7 (Yb(CuxAl1-x)12, ThMn12 type) has been studied by [1976Bus, 1979Fel, 1993Ste1] at compositions close
to YbCu4Al8. The same structure was identified in a sample at the YbCu6Al6 composition investigated by
[1980Fel] after annealing at 800-1000°C.
An YbCuAl3 phase, tI10 BaAl4 type, has been reported by [1988Kuz] but not confirmed by [1993Ste1].
Isothermal Sections
The 600°C Al-Cu-Yb isothermal section has been studied by [1993Ste1]. It is reported in Fig. 1 according
to the modifications added by [2003Ria] in order to meet the accepted Al-Cu phase equilibria (in particular,
the presence of the liquid phase at this temperature was neglected in the original paper).
Notes on Materials Properties and Applications
Properties related to the Yb mixed valence state in YbCuAl (the 1 phase) have been studied by several
authors: [1977Mat] (low temperature Cp and magnetization), [1979Ent] (symmetry properties, phonon
phenomena and anomalous features in the low temperature T/P phase diagram), [1980Mat] (thermal
expansion and magneto-volume effect), [1981Ble1, 1981Ble2] (low temperature Cp at high pressure up to
10 kbar), [1981Pot] (thermal expansion and Cp), [1982Mar, 1991Ell] (molar volume).
More recently, attention has been attracted by the YbCu5-based solid solution. Low temperature resistivity
and magnetic properties have been investigated in either CaCu5 type and AuBe5 type structures evidencing
Kondo behavior [1992Bau, 1998He, 1999Bon, 2001And, 2001He].
175
Landolt-BörnsteinNew Series IV/11A2
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Al–Cu–Yb
References
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1968Dwi] Dwight, A.E., Mueller, M.H., Conner, R.A. JR., Downey J.W., Knott, H., “Ternary
Compounds with the Fe2P-Type Structure”, Trans. Met. Soc. AIME, 242, 2075-2080 (1968)
(Crys. Structure, Experimental, 14)
[1973Oes] Oesterreicher, H., “Structural and Magnetic Studies on Rare Earth Compounds RNiAl and
RCuAl”, J. Less-Common Met., 30, 225-236 (1973) (Crys. Structure, Magn. Prop.,
Experimental, 21)
[1974Fer] Ferro, R., Marazza, R., Rambaldi, G., “Equiatomic Ternary Phases in the Alloys of the Rare
Earth with In and Ni or Pd”, Z. Metallkd., 65, 37-39 (1974) (Crys. Structure, Experimental,
2)
[1976Bus] Buschow, K.H.J., van Vucht, J.H.N., van den Haagenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth 3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50(1), 145-150 (1976) (Crys. Structure, 2)
[1977Mat] Mattens, W.C.M., Elenbaas, R.A., de Boer, F.R., “Mixed-Valence Behaviour in the
Intermetallic Compound YbCuAl”, Commun. Phys., 2, 147-150 (1977) (Experimental,
Phys. Prop., 7)
[1979Ent] Entel, P., Grewe, N., “Mixed Valencies: Structure of Phase Diagrams, Lattice Properties,
and the Consequences of Electron Hole Symmetry”, Z. Phys. B, 34(3), 229-241 (1979)
(Crys. Structure, Equi. Diagram, Phys. Prop., 20)
[1979Fel] Felner, I., Nowik, I., “Magnetism and Hyperfine Interactions of 57Fe, 151Eu, 155Gd, 161Dy,166Er and 170Yb in RM4Al8 Compounds (R=Rare Earth or Y, M=Cr, Mn, Fe, Cu)”,
J.Phys.Chem. Solids, 40, 1035-1044 (1979) (Crys. Structure, Experimental, 8)
[1980Fel] Felner, I. “Crystal Structure of Ternary Rare Earth - 3d Transition Metal Compounds of the
RT6Al6 Type ”, J. Less-Common Met., 72, 241-249 (1980) (Crys. Structure, Experimental,
10)
[1980Mat] Mattens, W.C.M., Hoelscher, H., Tuin, G.J.M., Moleman, A.C., de Boer, F.R., “Thermal
Expansion and Magneto-Volume Effects in the Mixed-Valent Compound YbCuAl”,
J. Magn. Magn. Mater., 15-18, 982-984 (1980) (Experimental, Magn. Prop., 3)
[1981Ble1] Bleckwedel, A., Eichler, A., “Specific Heat Measurements on Intermediate-Valent YbCuAl
Under High Pressure”, in “Phys. Solids High Pressure”, Proc. Int. Symp., 1981, 323-325
(1981) (Thermodyn., 9)
[1981Ble2] Bleckwedel, A., Eichler, A., Pott, R., “Pressure Dependence of the Specific Heat of
YbCuAl”, Physica B/C, 107B, 93-94 (1981) (Experimental, Phys. Prop., 7)
[1981Pot] Pott, R., Schefzyk, R., Wohlleben, D.,Junod, A., “Thermal Expansion and Specific Heat of
Intermediate Valent YbCuAl”, Z. Phys. B: Condens. Matter, 44B, 17-24 (1981) (Electr.
Prop., Experimental, 20)
[1982Mar] Marazza, R., Rossi, D., Mazzone, D., Ferro, R., “Ternary Alloys of Cerium and Ytterbium:
Some Notes on the Behavior of Their Molar Volumes”, J. Less-Common Met., 84, 33-38
(1982) (Experimental, 26)
[1985Mur] Murray, J.L., “The Aluminum-Copper System”, Internat. Met. Rev., 30(5), 211-233 (1985)
(Equi. Diagram, Crys. Structure, Review, 230)
[1987Adr] Adroja, D.T., Malik, S.K., Padalia, B.D., Vijayaraghavah, R., “The Valence State of Yb in
YbXCu4 (X = Al, Ag and Ga)”, J. Phys. C: Solid State Physics, 20(15), L307-310 (1987)
(Experimental, 8)
[1987Tsv1] Tsvyashchenko, A.V., Fomicheva, L.N., “High-Pressure Synthesis and Structural Studies of
Rare Earth (R) Compounds RCuAl”, J. Less-Common Met., 134, L13-L15 (1987) (Crys.
Structure, Experimental, 10)
176
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Yb
[1987Tsv2] Tsvyashchenko, A.V., Fomicheva, L.N. “New Polymorphic Modifications of the
Compounds RTAl (R = r.e.m., T = Cu, Ni)”, Inorg. Mater., 23, 1024-1027 (1987), translated
from Izv. Akad. Nauk SSSR, Neorg. Mater., 23, 1148-1152 (1987) (Crys. Structure,
Experimental, 15)
[1988Kuz] Kuz'ma, Yu.B., Stel'makhovich, B.M., “New RCuAl3 Compounds (R = Tb, Dy, Ho, Er, Tm,
Yb) and their Crystal Structure” (in Russian), Dop. Akad. Nauk Ukr. SSR, Ser. B: Geol.
Khim. Biol. Nauki, (11), 40-43 (1988) (Crys. Structure, Experimental, 4)
[1989Gsc] Gschneidner, K.A.Jr., Calderwood, F.W., “The Al-Yb (Aluminum-Ytterbium) System”,
Bull. Alloy Phase Diagrams, 10, 47-49 (1989) (Crys. Structure, Equi. Diagram, Review, 16)
[1989Mee] Meetsma, A., de Boer, J.L., van Smaalen, S., “Refinement of the Crystal Structure of
Tetragonal Al2Cu” J. Solid State Chem., 83(2), 370-72 (1989) (Crys. Structure,
Experimental, 17)
[1990Ste] Stelmakhovich, V.M., Kuzma, Yu.B., “New Compounds Ln6(Cu,Al)23 and their Crystal
Structure” (in Russian), Dokl. Akad. Nauk SSSR, (6), 63-65 (1990) (Crys. Structure,
Experimental, 4)
[1991Ell] Ellner, M., Kolatschek, K., Predel, B., “On the Partial Atomic Volume and the Partial Molar
Enthalpy of Aluminium in Some Phases with Cu and Cu3Au Structures”, J. Less-Common
Metals, 170, 171-184 (1991) (Experimental, Crys. Structure, 57)
[1991Ste] Stel'makhovich, B.M., Kuz'ma, Yu.B., “A New Aluminide Yb8Cu17Al49 and its Structure”,
Sov. Phys.-Crystallogr. (Engl. Transl.), 36(6), 808-810 (1991) (Crys. Structure, 4)
[1992Bau] Bauer, E., Hauser, R., Gratz, E., Gignoux, D., Schmitt, D., Sereni, J., “Transport and
Thermodynamical Properties of Ytterbium-Copper-Aluminum (Yb(Cu,Al)5) Compounds”,
J. Phys.: Condens. Matter, 4(38), 7829-7838 (1992) (Experimental, Thermodyn., 19)
[1992Kuz] Kuz'ma, Yu.B., Stel'makhovych, B.M., Babizhec'kyi, V.S., “A New compounds with the
PuNi3 Structure Type in the Rare-Earth-Cu-Al Systems” (in Russian), Izv. Akad. Nauk
SSSR, Met., (2), 227-230 (1992) (Crys. Structure, 6)
[1992Ran] Ran, Q., “Aluminum - Copper - Ytterbium”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.15536.1.20, (1992) (Crys. Structure, Equi. Diagram,
Assessment, 12)
[1993Gra] Gratz, E., Lindbaum, A., Rotter, M., Bauer, E., Kirchmayr, H., “Structural Investigations of
the Intermediate Valence Systems Yb(CuxAl1-x)5 (x=1, 0.8, 0.6)”, Mater. Sci. Forum,
133-136, 519-522 (1993) (Crys. Structure, Experimental, 3)
[1993Ste1] Stel'makhovych, B.M., Kuz'ma, Yu.B., Babizhet'sky, V.S., “The Ytterbium - Copper
- Aluminum System”, J. Alloys Compd., 190, 161-164 (1993) (Crys. Structure, Equi.
Diagram, Experimental, 21)
[1993Ste2] Stel'makhovich, B.M., Kuz'ma, Yu.B., Akselrud, L.G., “New Intermetallic Compounds
with Structures of the YbMo2Al4 and Th2Zn17 Type”, Russ. Metall. (Engl. Transl.), (1),
173-175 (1993) (Crys. Structure, Experimental, 5)
[1994Mur] Murray, J.L., “Al-Cu (Aluminum-Copper)”, in “Phase Diagrams of Binary Copper Alloys”,
Subramanian, P.R., Chakrabati, D.T., Laughlin, D.E., (Eds.), ASM International, Materials
Park, OH, 18-42 (1994) (Equi. Diagram, Review, 226)
[1994Sub] Subramanian, P.R., Laughlin, D.E., “Cu-Yb (Copper-Ytterbium)” in “Phase Diagrams of
Binary Copper Alloys”, Subramanian, P.R., Chakrabarti, D.J., Laughlin, D.E. (Eds.), ASM
International, Materials Park, OH, 482-486 (1994) (Equi. Diagram, Review, 39)
[1996Cer1] Cerny, R., Francois, M., Yvon, K., Jaccard, D., Walker, E., Petricek, V., Cisarova, I.,
Nissen, H.-U., Wessicken, R., “A Single-Crystal X-ray and HRTEM Study of the
Heavy-Fermion Compounds YbCu4.5”, J. Phys.: Condens. Matter, 8, 4485-4493 (1996)
(Crys. Structure, 13)
[1996Cer2] Cerny, R., “YbCu4.5 - A Giant Structure Determined by Single-Crystal X-Ray Diffraction
and HRTEM”, Acta Crystallogr., A52, 323-324 (1996) (Crys. Structure, 1)
177
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Yb
[1996Goe] Gödecke, T., Sommer, F., “Solidification Behaviour of the Al2Cu Phase” Z. Metallkd.,
87(7), 581-6 (1996) (Equi. Diagram, Crys. Structure, 8)
[1996He] He, J., Tsujii, N., Nakanishi, M., Yoshimura, K., Kosuge, K., “A Cubic AuBe5-Type YbCu5
Phase with Trivalent Yb Ion”, J. Alloys Compd., 240, 261-265 (1996) (Crys. Structure, 18)
[1997Bel] Belan, B.D., Bodak, O.I., Cerny, R., Pacheko, J.V., Yvon, K., “Crystal Structure of YbCu”,
Z. Kristallogr. NCS, 212, 508 (1997) (Crys. Structure, 6)
[1998He] He, J., Tsujii, N., Yoshimura, K., Kosuge, K., “Preparation of Cubic AuBe5-type
YbCu5-xAlx (0 < x < 0.5) Under High Pressure and Their Kondo Behavior”, J. Alloys
Compd., 268, 221-225 (1998) (Crys. Structure, Experimental, Magn. Prop., 27)
[1998Liu] Liu, X.J., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria in the Cu-rich Portion of
the Cu-Al Binary System”, J. Alloys Compd., 264(1-2), 201-08 (1998) (Equi. Diagram,
Crys. Structure, 25)
[1999Bon] Bonville, P., Vincent, E., Bauer, E., “Low Temperature Kondo Reduction of Quadrupolar
and Magnetic Moments in the YbCu5-xAlx Series”, Eur. Phys. J. B, 8, 363-369 (1999)
(Experimental, Thermodyn., 13)
[2001And] Andreica, D., Amato, A., Gygax, F.N., Schenck, A., Wiesinger, G., Reichl, C., Bauer, E.,
“ SR Studies of the Nonmagnetic-Magnetic Transition in YbCu5-xAlx”, J. Magn. Magn.
Mater., 226-230, 129-131 (2001) (Experimental, Magn. Prop., 5)
[2001He] He, J., Ling, G., Ye, Z., “Magnetic Properties of Hexagonal YbCu5-xAlx Crossover from
Intermediate Valence to Trivalence of Yb Ion”, J. Alloys Compd., 325, 54-58 (2001) (Crys.
Structure, Experimental, Magn. Prop., 26)
[2002Bod] Bodak, O., “Al-Yb (Aluminum-Ytterbium)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 20.13523.1.20 (2003) (Crys. Structure, Equi. Diagram,
Assessment, 15)
[2002Gul] Gulay, L.D, Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. “Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Rog] Rogl, P., van Rompaey, T., “Cu-Yb (Copper-Ytterbium)”, MSIT Binary Evaluation
Program,in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 20.13889.1.20 (2002) (Crys. Structure, Equi.
Diagram, Assessment, 10)
[2003Gro] Gröbner, J., “Al-Cu (Aluminium - Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 68)
[2003Ria] Riani, P., Arrighi, L., Marazza, R., Mazzone, D., Zanicchi, G., Ferro, R., “Ternary Rare
Earth Aluminum Systems with Copper: a Review and a Contribution to Their Assessment”
submitted to J. Phase Equilib. (Assessment, Review, 267)
178
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Yb
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Al)
< 660.45
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2],
0 to 2.48 at.% Cu [Mas2]
(Cu)
< 1084.62
Cu1-xAlx
cF4
Fm3m
Cu
a = 361.46
a = 361.52
a = 365.36
at 25°C [Mas2],
0 to 19.7 at.% Al [Mas2]
0 to 0.1 at.% Ce at 876°C [1994Sub]
x=0, quenched from 600°C [1991Ell]
x=0.152, quenched from 600°C, linear
da/dx [1991Ell]
( Yb)
819-795
cI2
Im3m
W
a = 444 [Mas2]
( Yb)
795-(-3)
cF4
Fm3m
Cu
a = 548.48 at 25°C [Mas2]
( Yb)
<-3
hP2
P63/mmc
Mg
a = 387.99
c = 638.59
[Mas2]
, Cu3Al(h)
1049-559
cI2
Im3m
W a = 294.6
~70 to 82 at.% Cu [1985Mur],
[1998Liu]
at 672°C
2, Cu1-xAlx< 363
t**
TiAl3long period
super-lattice
a = 366.8
c = 368.0
0.22 x 0.235 [1985Mur]
76.5 to 78.0 at.% Cu
at 76.4 at.% Cu
(subcell only)
0, Cu1-xAlxCu~2Al
1037-800
cI52
I43m
Cu5Zn8
0.37 x 0.315 [Mas2],
63 to 68.5 at.% Cu [1998Liu]
1, Cu9Al4< 890
cP52
P43m
Cu9Al4
a = 870.23
a = 870.68
62 to 68 at.% Cu, [Mas2, 1998Liu];
single crystal [V-C2] at 68 at.% Cu
from single crystal [V-C2]
, AlxCu1-x
< 686
hR*
R3m
a = 1226
a = 1511
0.407 x 0.381 [1985Mur]
59.3 to 61.9 at.% Cu
at x = 38.9 [V-C2]
1, Cu1-xAlx958-848
cubic? 0.406 x 0.379
59.4 to 62.1 at.% Cu [Mas2, 1985Mur]
2, Cu2-xAl
850-560
hP6-x
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.78 x 0.45
55 to 61 at.% Cu
[Mas2, 1985Mur, V-C2],
NiAs in [Mas2, 1994Mur]
179
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Yb
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2Cu47.8Al35.5
a = 812
b = 1419.85c = 999.28
55.2 to 59.8 at.% Cu [Mas2, 1994Mur]structure: [2002Gul]
2, Cu11.5Al9(r)
< 570oI24 - 3.5
Imm2Cu11.5Al9
a = 409.72
b = 703.13c = 997.93
55.2 to 56.3 at.% Cu [Mas2, 1985Mur]structure: [2002Gul]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200c = 863.5
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]Pearson symbol: [1931Pre]
2, CuAl(r)
< 560
mC20
C2/m
CuAl
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.3 at.% Cu [V-C]
, CuAl2< 592
tI12
I4/mcm
CuAl2a = 606.7
c = 487.7
32.05 to 32.6 at.% Cu at 549°C
32.4 to 32.8 at.% Cu at 250°C
[1996Goe]
single crystal [V-C2,1989Mee]
YbAl3< 980
cP4
Pm3m
AuCu3
a = 420.2 [1989Gsc]
Yb(CuxAl1-x)2
YbAl2< 1360
cF24
Fd3m
MgCu2
a = 787.7
0 x 0.25 [1993Ste1]
[1989Gsc]
YbCu
< 628
oP8
Pnma
FeB
a = 756.8
b = 426.7
c = 577.6
a = 756.53
b = 425.53
c = 576.67
[1994Sub]
[1997Bel]
YbCu2
< 757
oI12
Imma
CeCu2
a = 428.6 to 429.1
b = 689.4 to 689.9
c = 738.2 to 738.6
[1994Sub, V-C2]
YbCu2 (HP) hP12
P63/mmc
MgZn2
a = 526.0 ± 0.05
c = 856.7 ± 0.08
[V-C2]
Yb2Cu7
< 825
? ? [1994Sub, 1996Cer2]
Yb2Cu9
< 937
mC7448
-
Yb2Cu9
a = 4896.1
b = 4899.4
c = 4564.3
= 91.24°
monoclinic superstructure deriving
from cubic AuBe5-type via the
introduction of anti-phase boundaries
and copper-deficient shear planes
[1996Cer1, 1996Cer2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
180
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Yb
Yb(CuxAl1-x)5 (I)
YbCu~6.5
< 879
hP6
P6/mmm
CaCu5
a = 510.6 to 500.8
c = 414.6 to 411.7
a = 504.4
c = 414.0
a = 499.2 to 500
c = 412.6 to 413
a = 498.6
c = 412.8
0.58 x 1 [1993Ste1]
at x = 0.6 to 0.9
[1992Bau, 1993Gra]
at x = 0.8 [1987Adr]
[1994Sub], the composition Yb2Cu13
was attributed to a structure described
with same lattice parameter with a
random substitution of 18% of
Yb-sites by Cu-pairs [1994Sub]
[1996He]
Yb(CuxAl1-x)5 (II) cF24
F43m
AuBe5
a = 700.0 to 697.3 0.5 x 1 HP phase
prepared at 1.5 GPa, 1000°C, but also
found in as-cast alloys prepared under
ambient pressure [1996He, 1998He]
Yb6Cu23 (HP) cF116
Fm3m
Th6Mn23
a = 1203 ± 1 [V-C2]
* 1, Yb(CuxAl1-x)2 hP9
P62m
ZrNiAl
a = 692.5 to 691.3
c = 399.0 to 398.3
0.50 x 0.55 [1993Ste1]
* 2, YbCu0.9Al2.1 hR36
R3m
PuNi3
a = 547.1
c = 2535.8
[1992Kuz,1993Ste1]
* 3, Yb6(CuxAl1-x)23 cF116
Fm3m
Th6Mn23
a = 1223.4 x = 0.74 (Yb6Cu16Al7) [1990Ste]
* 4, Yb(CuxAl1-x)6 tI14
I4/mmm
YbMo2Al4
a = 638.6
c = 492.6
x = 0.85 [1993Ste1, 1993Ste2]
* 5, Yb4(CuxAl1-x)33 tI*
I4/mmm
Yb8Cu17Al49
a = 856.5
c = 1625.5
x = 0.26 [1991Ste]
* 6, Yb2(CuxAl1-x)17 hR57
R3m
Th2Zn17
a = 887.7 to 865.3
c = 1273.4 to 1265.9
0.46 x 0.51 [1993Ste1]
* 7, Yb(CuxAl1-x)12 tI26
I4/mmm
ThMn12
a = 872.4 to 862.3
c = 511.8 to 505.7
a = 874.6
c = 512.2
a = 864.3
c = 504.3
0.33 x 0.50 [1993Ste1]
at x = 0.33 [1979Fel]
at x = 0.50 [1980Fel]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
181
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Yb
20
40
60
80
20 40 60 80
20
40
60
80
Yb Cu
Al Data / Grid: at.%
Axes: at.%
τ1
τ3
τ2
τ5
τ7
τ6
τ4
YbCu5YbCu2YbCu
YbAl2
YbAl3
η1
ε2
δγ
1
β
L
(Al)
?
(Cu)(Yb)
Fig. 1: Al-Cu-Yb.
Isothermal section at
600°C
[1993Ste1, 2003Ria]
182
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
Aluminium – Copper – Zinc
Gautam Ghosh and Jan van Humbeeck, updated by Pierre Perrot
Literature Data
This ternary system contains many technologically important alloys, present and future applications.
Accordingly, the phase equilibria of the system have been reviewed [1934Fus, 1943Mon, 1952Han,
1961Phi, 1969Gue, 1973Wil, 1976Mon, 1979Cha] from time to time. Köster [1941Koe3] was the first to
report the entire liquidus surface and it was subsequently modified by [1960Arn2]. Isothermal sections in
the temperature range of 200 to 700°C have been determined by several researchers [1932Bau1, 1932Bau2,
1932Bau3, 1940Geb, 1941Geb1, 1941Koe1, 1941Koe2, 1941Koe3, 1942Geb, 1942Koe, 1960Arn1,
1960Arn2]. After a gap of four decades, [1980Mur] reinvestigated the solid state equilibria, using 31 ternary
alloys containing about 40.8 mass% Cu, in the temperature range of 250 to 350°C by means of
metallography, X-ray diffraction and electron probe microanalysis. Thermodynamic descriptions of the
system were mainly carried out by [1998Lia, 2002Mie]. Except for the sequence of solid state phase
transformations, the basic features of the phase equilibria in all of the above investigations are consistent
with each other. The present evaluation continuous the detailed critical review made by [1992Gho], which
took into account the data published until the year 1988.
Al-Cu-Zn alloys exhibit high damping capacity, shape memory effects and super elasticity which allows a
wide variety of possible use. The physical properties are associated with the reversible thermo-elastic
martensitic transformation [1987Lon, 1987Sca, 1988Mun, 1988Yev, 1990Gui, 1992Gui, 1993Lex,
1994Bou, 1995Pri1, 1995Pri2, 1997Zha, 1998Buj, 1999Ago1, 1999Lon, 2000Pel, 2000Zel]. So, interest in
these materials is grown and a large amount of literature is devoted to their physical properties.
The enthalpy of formation of the ternary phase ’ has been measured by dissolution calorimetry [2000Leg].
Calphad assessment has been carried out by [1998Lia, 2002Che, 2002Mie]. [2000Kra] calculated
solidification maps below the solidus at different cooling rates.
Binary Systems
The edge binary systems were recently critically evaluated, Al-Cu by [2003Gro], Al-Zn by [2003Per] and
Cu-Zn by [2003Leb] in the MSIT Binary Evaluation Program. These works are accepted here.
Solid Phases
The maximum solid solubility of Cu in ( Al) is up to 5.5 mass% in absence of Zn, and that of Zn is up to
83.1 mass% in absence of Cu. In equilibrium with the Cu solubility in (Al) increases with addition of Zn,
whereas in the ( Al)+ two phase field it decreases with increasing Zn content. The solid solubility limits
of Cu and Zn in (Al) are shown in Fig. 1 [1961Phi]. Within the composition range covered in Fig. 1, the
locus of the apex of the ( Al)+ + three-phase field is also shown. The apex of the ( Al)+ +( Zn)
three-phase field was not given by [1961Phi]; it is estimated in Fig. 1 and given by a dashed line. The solid
solubilities of Cu in (Al), given by [1942Geb] at 350, 300 and 240°C agree reasonably well with those of
[1961Phi]. However, the solid solubility of Zn in (Al) given by [1942Geb] are systematically higher than
those of [1961Phi]. [1941Koe1] reported that (Al) contains 1.5 mass% Cu and 33.5 mass% Zn when it is in
equilibrium with and phases at 350°C (annealed for 336 h), whereas [1942Geb] reported the
composition of (Al) to be about 1.5 mass% Cu and 43.0 mass% Zn after annealing at the same temperature
for 1680 h. Hume-Rothery [1948Hum] discussed the solid solubility limits of Al and Zn in (Cu) in terms of
the electron concentration factor. He noticed that, when Al is added to Cu-Zn alloys, the solubility range of
the (Cu) phase against remains at a constant electron concentration over a wide range of composition,
whereas when Zn is added to Al-Cu alloys there is an immediate departure from the simple electron
concentration rule. The solid solubility of Al and Cu in (Zn) were reported by [1936Bur, 1940Geb,
1940Loe, 1941Geb1, 1942Geb, 1949Geb] and [1980Mur]. The maximum solubility are about 1.3 mass%
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Al and 2.8 mass% Cu at 375°C and 0.8 mass% Al and 1.7 mass% Cu at 275°C. The saturation
concentrations of Al and Cu in (Zn) [1940Loe], as a function of temperature, are listed in Table 3. It should
be noted that the solubility found by [1940Geb, 1940Loe, 1941Geb1] and [1942Geb] agree well. Those of
[1980Mur] indicate a higher Cu solubility. The phase shows a continuous series of solid solutions from
Cu3Al to CuZn; it has a disordered cI2, W type structure at high temperatures. The stability of the phase
alloys decreases with decreasing temperature, and centers around an electron concentration of 1.48 for both
the binary and ternary alloys. [1948Ray] predicted the lower temperature limit of the stability of the ternary
phase in terms of an effective size factor. At lower temperatures, the phase undergoes ordering to a CsCl
or Fe3Si type superlattice depending on the alloy composition. Comprehensive reviews of the stability of
the phase and the effect of ordering on the subsequent martensitic transformation can be found elsewhere
[1977Rap, 1978Sin, 1980Ahl, 1986Ahl1, 1986Ahl2, 1995Ahl]. Also the -brass phases form a continuous
series of solid solutions at high temperatures [1941Koe3] which shows a miscibility gap below about
400°C. The behavior of the binary and ternary phases has been investigated by a number of experimental
techniques, such as resistivity and thermo-emf [1972Kan1, 1973Ash], X-ray diffraction [1972Kan2,
1974Ash, 1988Kis], and thermo-graphymetry and dilatometry [1974Umu]. The solid solubilities of Al in
Cu5Zn8 at 20 and 350°C are about 3.5 and 7.0 mass% Al, respectively [1973Ash]. At the same temperatures,
the 1 phases of the Al-Cu binary system dissolve about 30 mass% Zn [1973Ash]. With the addition of Al
in Cu5Zn8, the lattice parameter is reported to decrease continuously [1928Bra]. [1941Koe2] and
[1941Koe3] assumed , and ' to have one common field of homogeneity at higher temperatures. The
same was assumed for the 2 and phases. The phases and were shown to be different phases at any
temperature by [1960Arn2]. The phases 2 and have such different unit cells that it is very improbable to
have one continuous series of solid solutions between them. The 2 phase of the Al-Cu binary system was
assumed to be completely soluble with the phase of the Cu-Zn binary system above about 680°C
[1941Koe3] and [1960Arn2]. Below this temperature, separation occurs through the intrusion of
equilibrium between the and phases. The phase of the Al-Cu binary system can dissolve up to 2 to 3
mass% Zn with little change in lattice parameter and properties [1941Koe3]. The phase of the Cu-Zn
binary system can dissolve up to about 12 mass% Al [1941Koe3] at about 600°C, and this solid solubility
decreases with decreasing temperature. The ternary phase, below 250°C has two separate ranges of
homogeneity and ' [1960Arn1] due to the maximum of the three-phase field + + 1 [1941Koe1] and
[1941Koe2]. The different structures do not exclude a single range of homogeneity at higher temperatures
since the hR9 structure of ' is a superstructure of the CsCl type with ordered vacancies. It may be formed
from a CsCl structure with random distribution of vacancies by a second order transformation. The possible
formulas of and ' phases can be represented as Cu5Zn2Al3 and Cu3ZnAl4, respectively. The phase is
formed by a univariant peritectic reaction between 2 and liquid at about 740°C. The ternary ' phase
appears between 600 and 550°C near the Al-rich end of the homogeneity range of the phase. At 550°C,
the phase has a wide range of homogeneity (Fig. 7). At 200°C, the phase has a relatively narrow range
of homogeneity surrounding 13 mass% Al, 56 mass% Cu and 31 mass% Zn and the ' phase also has a
narrow homogeneity range surrounding 32 mass% Al, 56 mass% Cu and 12 mass% Zn (Fig. 13). A
metastable X phase has been reported [1988DeG] in both Al-Cu and ternary phase alloys which were
quenched from 900 to 950°C to room temperature or in ice water, and subsequently annealed at 300 to
348°C. This X phase has a long period superlattice structure and can be described in terms of 18R or
monoclinic unit cell. The details of the crystal structures and the lattice parameters of all stable solid phases
are listed in Table 1.
Invariant Equilibria
Figures 2a and 2b show the reaction scheme based on the investigations of [1940Geb, 1941Geb1,
1941Geb2, 1941Koe3, 1942Geb, 1949Geb, 1960Arn1, 1960Arn2] and [1980Mur]. The univariant reaction,
p8, occurs at about 740°C and feeds both the invariant reactions U4 and U6. Some of the four-phase
equilibria involving the compositions of the phases are listed in Table 2 after [1940Geb, 1941Geb1,
1941Geb2, 1941Koe3, 1942Geb, 1942Wei, 1949Geb, 1960Arn1, 1960Arn2, 1967Coo] and [1980Mur]. For
most of the invariant reactions, both the temperatures and the compositions of the invariant points as
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reported by [1925Han] and [1927Nis] differ substantially from the above authors. The sequence of the solid
state reactions in the temperature range of 275 to 350°C is adopted from [1980Mur]. The solid state
reactions in the temperature range of 268 to 288°C proposed by [1941Geb1] and [1941Geb2] have been
experimentally verified by [1980Mur]. This involves three U type reactions instead of one U type and one
E type reaction proposed by [1960Arn2]. To comply with the accepted Al-Zn binary phase diagram, the
temperature of the four-phase reaction U12 is taken as 278°C instead of 276°C as proposed by [1980Mur].
In contrast to the results of [1941Koe3] and [1980Mur], [1969Cia] reported that the four-phase reaction
U14, (Al)+ '+(Zn), can take place at as low as 50°C. In the original papers the reaction scheme was
simplified, as the phases 0 and 1, 1, 2 and , 1 and 2, 1 and 2 were not distinguished and the
invariant equilibria evolving from solid state three-phase reactions containing 2 and phases of the Al-Cu
system were neglected. In Figs. 2a and 2b the phases 0 and 1, 1, 2 and are tentatively distinguished.
It must be emphasized that the reaction scheme in Figs. 2a and 2b is still incomplete as the participation of
some binary solid state invariant reactions has not been considered; 1 and 2 as well as 1 and 2, are not
distinguished and are called 1 and 1, respectively. Nevertheless, the assessed reaction scheme is
consistent with the experimental phase diagrams.
Liquidus Surface
Figure 3 shows the liquidus surface after [1941Koe2] and [1960Arn2] and the monovariant curves
separating different areas of primary crystallization. The valley projection not yet determined are given
tentatively by dashed lines. [1911Lev] and [1912Lev] reported the primary crystallization temperature of a
number of ternary alloys, but their results differ significantly from [1941Koe2] and [1960Arn2]. The partial
liquidus surface determined by the earlier workers [1912Car, 1919Jar, 1920Ros, 1921Hau, 1925Han,
1927Nis] agree only qualitatively with the results of [1941Koe2] and [1960Arn2]. Even though [1926Nis]
and [1927Nis] performed a thorough investigation of the Al-Cu-Zn phase equilibria, some of their results
concerning the liquidus surface could not be reproduced later by [1928Ham]. The liquidus surface of the
Zn-corner reported by [1957Wat] does not agree with those of [1941Koe1] and [1960Arn2]. Approximate
isotherms at 50 K intervals are also shown in Fig. 3. The Cu-rich part of the system was optimized by
[2002Mie]. The calculated liquidus surface (xZn < 0.5, xAl < 0.35) agrees well with the experimental one
represented in Fig. 1.
Isothermal Sections
The isothermal sections at 700°C [1941Koe2, 1960Arn2], 650°C [1960Arn2], 600°C [1941Koe2,
1960Arn2], 550°C [1941Koe2, 1960Arn2], 500°C [1941Koe2], 400°C [1941Koe2], 350°C [1941Koe1,
1941Koe2, 1942Geb, 1960Arn1], 300°C [1942Geb], 240°C [1942Geb] and 200°C [1942Koe, 1960Arn1]
are shown in Figs, 4, 5, 6, 7, 8, 9, 10, 11,12 and 13, respectively. The Cu-rich regions are particularly derived
from [1932Bau1, 1932Bau2, 1932Bau3, 1970Fle] and the Al- and Zn-rich regions are derived from
[1940Geb, 1941Geb1, 1942Geb, 1949Geb] and [1980Mur]. The partial isotherms at the Zn-corner reported
by [1920Ros] and [1921Hau] in the temperature range of 200 to 400°C and those for other alloys by
[1925Han] at 370 and 385°C agree only qualitatively with the results of the above authors. The isothermal
section at 700°C (Fig. 4) shows the continuous solid solutions (between of Al-Cu binary system and
of Cu-Zn binary system) and (between of Al-Cu binary system and of Cu-Zn binary system). In Fig. 4,
the phases 2 and are tentatively distinguished by dashed lines. Figure 7 shows the isothermal section at
550°C. Here, the ternary phase ' appears in the Al-rich region of the phase field. Even though two
different superstructures, for and ' phases, have been reported, no two-phase field has been detected
[1941Koe1, 1941Koe2]. The isothermal sections shown above are also consistent with the results of phase
decomposition studies by several authors [1934Ful, 1970Fle, 1984Man, 1986Myk, 1986Yan]. Below
350°C, the Cu-rich portion of the isothermal sections are still in doubt. In the isothermal sections, minor
adjustments have been made to comply with the accepted binary phase diagrams. The liquidus isotherms in
Figs. 4, 5, 6, 7, 8 and 9 are adjusted to those given in Fig. 3. (Al)’ and (Al)’’ correspond to the de-mixing
of ( Al) below 352°C.
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Temperature – Composition Sections
A large number of temperature-concentration diagrams, cutting vertically through the ternary phase
diagram are reported as isopleths or polythermal sections, e.g. by [1919Jar], and by [1919Sch] at constant
Cu contents of 2, 4, 6, 8 and 10 mass% Cu. [1921Hau] determined the isopleths at 1, 2, 3, 4, 5, 7, and 9
mass% Cu and also at 2, 4, 6, 8, 10, 12 and 15 mass% Al. [1925Han] determined the isopleths at 5, 10, 15,
20 and 25 mass% Cu. [1926Nis] reported the polythermal sections at 1, 2, 3, 5, 7.5 and 10 mass% Cu.
[1949Geb] reported three isopleths at 1, 2 and 3 mass% Cu. [1960Arn2] determined two isopleths at 10 and
20 at.% Zn. [1957Wat] determined three polythermal sections at 2.5, 5.0 and 10.0 mass% Cu. The earlier
results [1919Jar, 1919Sch, 1921Hau, 1925Han, 1926Nis] agree only qualitatively with each other. In
general, there is substantial disagreement between the earlier results [1919Jar, 1919Sch, 1921Hau,
1925Han, 1926Nis] and later investigations by [1949Geb, 1957Wat] and [1960Arn2] which are considered
to be accurate and reliable. However all data have been considered in the course of this critical evaluation.
Thermodynamics
Heat capacities of the 1 and ’1 phases has been measured on the Cu-13.9Zn-17.3Al (at.%) [1988Tsu].
[1993Ahl] evaluates the phase stabilities of martensitic and equilibrium phases and discusses the
contribution which controls the Gibbs energy of the different phases. The first expressions of the chemical
potentials changes were proposed by [1988Kuz] for the transition liquid and by [1994Hsu] for the
martensitic transformations of the phase. The thermodynamic properties of the ternary alloys containing
25 to 62 at.% Al have been determined in [1994Van] by emf measurements between 420 and 920°C by an
aluminum concentration cell. [1998Lia] presents a thermodynamic description of the Al-Cu-Zn system with
an emphasis on the Al-Zn binary. The descriptions of the binary systems accepted by [1998Lia] are those
of [1993Che] for Al-Zn and [1993Kow] for Cu-Zn. The liquid, fcc-(Cu), fcc-(Al), cph-(Zn), and
disordered solutions are modeled by a disordered solution with the introduction of a ternary interaction
parameter. The two binary phases: Al4Cu9 and Cu5Zn8, isomorphous and forming a continuous solid
solution are of a rather complex structure. Cu5Zn8 has a superlattice in which one unit cell corresponds to
27 unit cells of the W type; Al4Cu9 is an ordered variant of that structure in which every Zn position of
Cu5Zn8 splits into two positions, one occupied by Al, the other by Cu. Models with 4 to 6 sublattices have
been proposed for the solid solution [2000Ans, 2000Sat]. The model used by [1998Lia] is a simple
Redlich-Kister description with hypothetical lattice stabilities used for the phases and does not take into
account the ordering; it describes reasonably well the solubility range. The 0 phase was modeled as
Cu8(Cu,Zn,Al)1(Zn,Al)4 and the ternary Cu5Zn2Al3 as (Al,Cu)1Cu4ZnAl4 that is as formed by two
hypothetical stoichiometric compounds Cu4ZnAl5 and Cu5ZnAl4 Using the Pandat software, [2001Che,
2002Che] propose an isothermal section of the diagram at 277°C (550 K) showing a miscibility gap in the
fcc-(Cu) solid solution which does not appear in the experimental diagrams drawn between 200 and 300°C
(Figs. 11, 12 and 13).
Notes on Materials Properties and Applications
Al-Cu-Zn based alloys are important materials with shape-memory effect, more economic than Ni-Ti alloys
[1997Zha]. In addition to the martensitic transformation ensuring shape-memory effect [1995Gue,
1999Lov], these alloys are characterized by ordering occurring in the phase after annealing at 450°C and
below. Before turning into martensite, the parent phase (austenite) undergoes an ordering reaction which
transforms the unit cell (A2) into ordered 1 (L21) or 2CsCl. During the direct martensitic
transformation, the above parent phases change respectively into ’1 (monoclinic) and ’2 (orthorhombic)
martensites [1995Cha, 1998Buj]. Between 300 and 600°C, the phase can decompose by the following
reaction: ( Cu)+ Cu5Zn8 [2000Zel]. The heat exchange associated with the martensitic transformation
has been recorded for three alloy compositions, Cu-24.8Zn-9.2Al at.% [1995Cha], Cu-16.49Zn-15.75Al
at.% (alloy R) [2000Pel] and Cu-8.83Zn-22.09Al at.% (alloy H) [2000Pel]. On cooling, the martensitic
transformation starts at MS and is completed at MF; on heating, the reverse transformation (austenitization),
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starts at AS and terminates at AF. The temperature intervals (MS - MF) and (AF - AS) for the phase
transformations depend on the martensitic structure, but not on the grain size. A similar dependence applies
for the width of the hysteresis (AF - MS).
The martensitic transformations has been investigated by various methods, recording the nuclear magnetic
resonance [1991Dim], measuring the associated caloric effects [1988Mun, 1995Cha, 1998Wei, 2000Pel]
and observing the response of the material’s structure in X-ray diffraction and electron microscopy
[1989Tol, 1998Buj, 2000Dor, 2000Zel]. One of the resulting conclusions is that the relative stabilities of
different martensitic phases are related to the lattice distortion [1992Ahl, 1992Pel, 1992Sau, 1995Sau,
1995Ahl].
Other important features such as the influence of quenching and aging on the transformation temperatures
were investigated by [1988Ara, 1989Cha, 1994Wu, 1998Man]. [1990Gui] and [1996Gar] studied the
influence of compositional changes on the transformation temperatures. Effects on the transformations
attributed to the stress-state of the material were studied by [1992Ame, 1995Isa, 1998Gal]. The work of
[2001Bek] investigates the influence of pressure, up to 1.5 GPa.
The Gibbs energy of the martensitic transformation of both thermal and mechanical origin has been
evaluated by [1988Ort, 1991Gui1, 1991Gui2]. [1999Ago2] developed a thermo-mechanical model
allowing the simulation of the shape-memory effect on Cu-14.1Zn-17.0Al (at.%). Point defects in
Cu-Zn-Al single crystals alloys have been investigated by means of positron lifetime spectroscopy
[1997Som, 1999Rom]. The formation and growth of 1 plates from a ’ matrix by a bainitic transformation
has been studied by [1992Tak, 1994Men]. The shape memory effect has also been observed in alloys with
dual phase - ’ structure, obtained by quenching from the equilibrium - [1999Lon]. Martensites in
shape-memory alloys often exhibit unusual pseudo-elasticity referred to as the rubber-like behavior which
has been investigated by [1987Sak, 1995Pri1, 1995Pri2, 1995Tsu, 2000Yaw] and thermodynamic models
[1993Lex, 1994Bou] as well as thermo-mechanical models [1999Ago2] has been proposed.
Small Cu-additions to as-cast Al-Zn alloys close to the eutectoid composition show a relatively low ductility
but also instabilities [1992Cia], which can be reduced by relatively simple heat treatments [1992Bob].
Miscellaneous
[1986Sug] reported the chemical activity of Zn in liquid Al-Cu-Zn alloys at 1150 and 1100°C in the
composition range xZn < 0.09 and xAl 0.08. [1964Day] determined the solid/liquid distribution
coefficients by centrifugal method in Al-rich and Zn-rich alloys. The partition coefficients are reported to
be consistent with the phase diagram features.
As early as in the beginning 20th century [1905Gui] and [1906Gui] performed systematic studies of
replacing Zn by Al, Fe, Mg, Mn, P, Pb, Sb, Si and Sn in a number of Cu-Zn brasses. They determined the
volume fraction of the and phases in Cu-Zn alloys and their mechanical properties with the addition of
these alloying elements. Comparable systematic studies were made by [1925Sma] replacing Zn by Al, Fe,
Ni and Sn in Cu-Zn brasses. Similar alloy development studies, regarding the effect of Si and Sb on the
microstructure of Al-Cu-Zn bronzes, were also performed by [1930Sev]. All these laborious alloy
development studies were performed by carefully examining the microstructure and determining the
mechanical properties.
[2001Liu] investigated the influence of zinc and other elements on the (fcc), (bcc) and (Cu) Cu9Al4equilibrium in the Al-Cu system and develop a quantitative method to determine the effect of the alloying
elements on the two-phase microstructure. [2001Zhu1] analyses by electron back-scatter diffraction the
microstructure of an alloy Zn85-Cu11-Al4 (mass%) in which both hexagonal phases ( Zn) and are
present. The microstructure evolution in Zn76-Al22-Cu2 and Zn86-Al11-Cu3 (mass%) alloys during
ageing between 100 and 200°C were followed respectively by [2000Dor] and [2001Zhu2]. The evidence of
a spinodal decomposition of the ( Zn) phase and the occurrence of a four phase reaction + + is shown.
Prolonged ageing causes the disordered phase to transform into an ordered ’, which confirms previous
observations made by [1999Zhu]. The measured composition of the ’ phase 57.7Al-34.9Cu-7.4Zn (at.%)
agrees with the composition given by [1975Mur] and is incorporated in the Figs. 7 to 13.
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Mechanical alloying of Al-Cu-Zn alloys [1998Lop] allows to form metastable phases such as ternary
compounds, supersaturated solutions and also amorphous alloys; this opens another large spectrum of
possible applications for this ternary system.
References
[1905Gui] Guillet, L., “Researches on Cu Alloys: Special Brasses and Bronzes” (in French), Rev.
Metall., 2, 97-120 (1905) (Experimental, 1)
[1906Gui] Guillet, L., “A General Study of Special Brasses” (in French), Rev. Métall., 3, 159-204
(1906) (Experimental, 1)
[1911Lev] Levi-Malvano, M., Marantonio, M., “Researches on the Constitution of Al” (in Italian),
Gazz. Chim. Ital., 41, 282-297 (1911) (Experimental, 5)
[1912Car] Carpenter, H.C.H., Edwards, C.A., “The Liquidus Curves and Constitutional Diagram of
the Ternary System Aluminium-Copper-Zinc (Copper Rich Alloys)” (in German), Int.
Z. Metallographie, 2, 209-242 (1912) (Equi. Diagram, Experimental, 13)
[1912Lev] Levi-Malvano, M., Marantonio, M., “On Light Alloys of Al, Zn and Cu” (in Italian), Gazz.
Chim. Ital., 42, 353-360 (1912) (Experimental, 3)
[1919Jar] Jares, V., “The Ternary System Al-Cu-Zn with Special Attention to the Zn Corner”
(in German), Z. Metallkd., 10, 1-44 (1919) (Equi. Diagram, Experimental, 12)
[1919Sch] Schulz, E.H., Waehlert, M., “Studies on High Zn Copper-Aluminium-Zinc Alloys”
(in German), Metall und Erz, 16, 170-175 (1919) (Equi. Diagram, Experimental, 19)
[1920Ros] Rosenhain, W., Haughton, J.L., Bingham, K.E., “Zinc Alloys with Aluminium and
Copper”, J. Inst. Met., 23, 261-324 (1920) (Equi. Diagram, Experimental, 4)
[1921Hau] Haughton, J.L., Bingham, K.E., “The Constitution of the Alloys of Aluminium, Copper and
Zinc Containing High Percentages of Zinc”, Proc. Roy. Soc., 99A, 47-68 (1921) (Equi.
Diagram, Experimental, 15)
[1925Han] Hanson, D., Gaylor, M.L.V., “On the Constitution of Alloys of Aluminium, Copper and
Zinc”, J. Inst. Met., 34, 125-170 (1925) (Equi. Diagram, Experimental, 7)
[1925Sma] Smalley, O., “Special Nickel Brasses”, Trans. AIME, 73, 799-833 (1925) (Experimental)
[1926Nis] Nishimura, H., “Al-Rich Al-Cu-Zn Alloys” (in Japanese), Suiyokwai-Shi, 5, 291-304 (1926)
(Equi. Diagram, Experimental, 6)
[1927Nis] Nishimura, H., “An Investigation of the Alloy System of Aluminium, Copper and Zinc”,
Mem. Coll. Eng., Kyoto Imp. Univ., 5, 61-132 (1927) (Equi. Diagram, Experimental, 30)
[1928Bra] Bradley, A.J., Gregory, C.H., “The Structure of Some Ternary Alloys of Copper, Zinc and
Aluminium”, Mem. Proc. Manchester Lit. Phil. Soc., 72, 91-100 (1928) (Crys. Structure,
Experimental, 7)
[1928Ham] Hamasumi, H., Matoba, S., “A Solution of the Ternary Equilibrium Diagram and a
Contribution on the Al-Cu-Zn System”, Tech. Rep. Tohoku Imp. Univ., 8, 71-98 (1928)
(Experimental, Theory, 2)
[1930Sev] Sevault, A., “Study of Special Al Bronzes with Zn, Si and Sb” (in French), Rev. Métall., 27,
64-82 (1930) (Experimental, 3)
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1932Bau1] Bauer, O., Hansen, M., “The Effect of Third Metal on the Constitution of Brass Alloy. IV.
The Effect of Al/A Constitution on the Ternary System Cu-Zn” (in German), Z. Metallkd.,
24, 1-6 (1932) (Equi. Diagram, Experimental, #, *, 24)
[1932Bau2] Bauer, O., Hansen, M., “The Effect of Third Metal on the Constitution of Brass Alloy. IV.
The Effect of Al/A Constitution on the Ternary System Cu-Zn” (in German), Z. Metallkd.,
24, 73-78 (1932) (Equi. Diagram, Experimental, *, 1)
[1932Bau3] Bauer, O., Hansen, M., “The Effect of Third Metal on the Constitution of Brass Alloy. IV.
The Effect of Al/A Constitution on the Ternary System Cu-Zn” (in German), Z. Metallkd.,
24, 104-106 (1932) (Equi. Diagram, Experimental, *, 0)
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[1934Fus] Fuss, V., “Al-Cu-Zn” in “Metallography of Al and its Alloys” (in German), Berlin, 149-151
(1934) (Equi. Diagram, Review, 4)
[1934Ful] Fuller, M.L., Wilcox, R.L., “Studies of Phase Changes During Ageing of Zinc-Alloy
Die-Casting. I. Eutectoidal Decomposition of Beta Aluminium-Zinc Phase and its Relation
to Dimensional Changes in Castings”, Metals Technol. (Sept.), AIME, Tech. Publ. No. 572,
1-17 (1934) (Experimental, 17)
[1936Bur] Burkhardt, A., “Zinc Alloys as Substitute Metals” (in German), Z. Metallkd., 28, 299-308
(1936) (Equi. Diagram, Experimental, *, 15)
[1940Geb] Gebhardt, E., “The Zn-Corner of the Zn-Al-Cu Ternary System” (in German), Z. Metallkd.,
32, 78-85 (1940) (Equi. Diagram, Experimental, *, 12)
[1940Loe] Löhberg, K., “X-Ray Determination of the Solubility of Al and Cu in Zn” (in German),
Z. Metallkd., 32, 86-90 (1940) (Experimental, *, 11)
[1941Geb1] Gebhardt, E., “The Constitution and the Volume Changes of Zn-Cu-Al Alloys. IV. Reasons
for the Volume Changes and a Technique of Achieving Dimensional Stability” (in German),
Z. Metallkd., 33, 297-305 (1941) (Equi. Diagram, Experimental, #, *, 13)
[1941Geb2] Gebhardt, E., “The Decomposition of in Al-Containing Zn Alloys and the Effect of Small
Additions on the Rate of Decomposition” (in German), Z. Metallkd., 33, 328-332 (1941)
(Equi. Diagram, Experimental, #, *, 24)
[1941Koe1] Köster, W., Moeller, K., “The Constitution and the Volume Changes of Zn-Cu-Al Alloys.
I. The Partitioning of the Concentration Plane at 350°C” (in German), Z. Metallkd., 33,
278-283 (1941) (Equi. Diagram, Experimental, #, *, 18)
[1941Koe2] Köster, W., Moeller, K., “The Constitution and the Volume Changes of Zn-Cu-Al Alloys.
II. The Relation of CuAl with the Ternary Phase” (in German), Z. Metallkd., 33, 284-288
(1941) (Equi. Diagram, Experimental, #, 3)
[1941Koe3] Köster, W., “The Constitution and the Volume Changes of Zn-Cu-Al Alloys. III. Summary
of the Equilibrium Relationships in the System Cu-Al-Zn” (in German), Z. Metallkd., 33,
289-296 (1941) (Equi. Diagram, Experimental, #, *, 12)
[1942Geb] Gebhardt, E., “The Constitution and the Volume Changes of Zn-Cu-Al Alloys. VI. Survey
of the Equilibrium Relationships on the Zn-Al Side under 350°C” (in German), Z. Metallkd.,
34, 208-215 (1942) (Equi. Diagram, Experimental, #, *, 13)
[1942Koe] Köster, W., Moeller, K., “The Constitution and Volume Changes of Zn-Cu-Al Alloys. V.
The Division of the Ternary Phases at Low Temperatures” (in German), Z. Metallkd., 34,
206-207 (1942) (Equi. Diagram, Experimental, #, *, 4)
[1942Wei] Weisse, E., Blumenthal, A., Hanemann, H., “Results of a Study of Eutectic Zn Alloys”
(in German), Z. Metallkd., 34, 221 (1942) (Experimental, 9)
[1943Mon] Mondolfo, L.F., “Al-Cu-Zn” in “Metallography of Aluminium Alloys”, Wiley, J., Inc, S.
(Eds.), New York, 89-90 (1943) (Equi. Diagram, Review, #, 2)
[1948Hum] Hume-Rothery, W., “The Effect of Manganese, Iron and Nickel on the / Brass”, Philos.
Mag., 39, 89-97 (1948) (Equi. Diagram, Experimental, *, 13)
[1948Ray] Raynor, G.V., “A Note on the Forms of the -Brass Regions in Certain Ternary Alloys of
Copper”, Philos. Mag., 39, 212-218 (1948) (Theory, 8)
[1949Geb] Gebhardt, E., “Study of Equilibria in the Zn-Al-Cu System” (in German), Z. Metallkd., 40,
136-140 (1949) (Equi. Diagram, Experimental, #, *, 9)
[1952Han] Hanemann, H., Schrader, A., “Al-Cu-Zn” in “Ternary Al Alloys” (in German), Stahleisen
m.b.h., Düsseldorf, 94-100 (1952) (Equi. Diagram, Review, #, *, 6)
[1957Wat] Watanabe, H., “Fundamental Studies 75S. I. Investigations on the Phase Diagram of the
Al-Zn-Cu System” (in Japanese), Nippon Kinzoku Gakkai Shi, 21, 333-337 (1957) (Equi.
Diagram, Experimental, #, *, 13)
[1960Arn1] Arndt, H.H., Moeller, K., “The Ternary Phase of the Cu-Al-Zn System. I. The
Decomposition of the T-Phase at 200-300°C” (in German), Z. Metallkd., 51, 596-600 (1960)
(Equi. Diagram, Experimental, #, 9)
189
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
[1960Arn2] Arndt, H.H., Moeller, K., “The Ternary Phase of the Cu-Al-Zn System. II. The T-Phase
Field above 500°C” (in German), Z. Metallkd., 51, 656-662 (1960) (Equi. Diagram,
Experimental, #, 13)
[1961Phi] Philips, H.W.L., “Al-Cu-Zn” in “Equilibrium Diagrams of Aluminium Alloy Systems”,
Aluminium Development Association, 74-77 (1961) (Equi. Diagram, Review, #, *, 1)
[1964Day] Day, M.G., Hellawell, A., “The Determination of Solid/Liquid Distribution Coefficient by
Centrifugal Methods”, J. Inst. Met., 93, 276-277 (1964-1965) (Experimental, 7)
[1967Coo] Cooksey, D.J.S., Hellawell, A., “The Microstructure of Ternary Eutectic Alloys in the
Systems Cd-Sn-(Pd, In, Tl), Al-Cu-(Mg, Zn, Ag) and Zn-Sn-Pb”, J. Inst. Met., 95(6),
183-187 (1967) (Experimental, 17)
[1969Cia] Ciach, R., Krol, J., Wegrzyn-Tasior, K., “Studies of a Four-Phase Transformation
(i.e. A+B C+D) in Al-Zn 78 % Alloys Containing 1-3% of Cu”, Bull. Acad. Pol. Sci., Ser.
Sci. Chim., 17, 371-378 (1969) (Experimental, 13)
[1969Gue] Guertler, W., Guertler, M., Anastasiadias, E., “Aluminium - Copper - Zinc” in
“A Compendium of Constitutional Ternary Diagrams of Metallic Systems”, Israel Program
Scientific Translations, Jerusalem, 543-548 (1969) (Equi. Diagram, Review, #, *, 21)
[1970Fle] Fletcher, A.J., Thomas, D.L., “Solid State Transformation in Certain Cu-Al-Zn Alloys”,
J. Inst. Met., 98, 188-192 (1970) (Equi. Diagram, Experimental, #, 7)
[1972Kan1] Kandaurov, N.E., Melikhov, V.D., “Determination of the Specific Resistance and
Thermo-EMF of Alloys in the -Region of the Cu-Al-Zn System” (in Russian), Tr. Sem.
Kef. Teor. Mekh. Vy. Dzh. Tekh. Inst., 2, 281-288 (1972) (Experimental, 10)
[1972Kan2] Kandaurov, N.E., Beginov, T.B., Presnyakov, A.A., Melikhov, V.D., Ashirimbetov, Zh. A.,
“Structure of Alloys in the -Region of the Cu-Al-Zn System at Room Temperature”
(in Russian), Prikl. Teor. Fiz., 3, 269-275 (1972) (Experimental, 6)
[1973Ash] Ashirimbetov, Zh. A., Kandaurov, N.E., Kalina, M.M., Melikhov, V.D., Presnyakov, A.A.,
“Structure and Properties of Solid Solutions of the -Region of the Cu-Al-Zn System”
(in Russian), Prikl. Teor. Fiz., 5, 210-213 (1973) (Experimental)
[1973Wil] Willey, L.A., “Al-Cu-Zn (Aluminum-Copper-Zinc)” in “Metals Handbook”, 8, 390-391
(1973) (Equi. Diagram, Review, #, *, 11)
[1974Ash] Ashirimbetov, Zh. A., Kalina, M.M., Presnyakov, A.A., Melikhov, V.D., “Crystal
Structures of Ternary Solid Solutions Based on the Intermetallic Compounds Cu5Zn8 and
Cu9Al4” (in Russian), Prikl. Teor. Fiz., 6, 67-71 (1974) (Experimental, 7)
[1974Umu] Umurzakov, T.M., Kalina, M.M., Melekhov, V.D., Presnyakov, A.A., Antonyuk, V.I.,
“Thermographic and Dilatometric Study of Alloys of the -Region of the Cu-Al-Zn
System” (in Russian), Obshch. i Prikl. Fizika, (7), 181-188 (1974) (Experimental, 6)
[1975Mur] Murphy, S., “The Structure of the T'-Phase in the System Al-Cu-Zn”, Met. Sci., 9, 163-168
(1975) (Crys. Structure, Experimental, *, 8)
[1976Mon] Mondolfo, L.F., “Aluminium-Copper-Zinc” in “Metallography of Aluminum Alloys”, Wiley
& Sons, Inc., New York, 518-520 (1976) (Equi. Diagram, Review, *, 21)
[1977Rap] Rapacioli, R., Ahlers, M., “Ordering in Ternary -Phase Cu-Zn-Al Alloys”, Scr. Metall., 11,
1147-1150 (1977) (Experimental, Theory, 9)
[1978Sin] Singh, S.C., Murakami, Y., Delaey, L., “Remarks on Ordering in Ternary -Cu-Zn-Al
Alloys”, Scr. Metall., 12, 435-438 (1978) (Theory, 5)
[1979Cha] Chang, Y.A., Neumann, J.P., Mikula, A., Goldberg, D., “Aluminum-Copper-Zinc” in “The
Metallurgy of Copper, Phase Diagrams and Thermodynamic Properites of Ternary
Copper-Metal Systems”, INCRA Monograph VI, 253-263 (1979) (Equi. Diagram, Review,
#, *, 25)
[1980Ahl] Ahlers, M., “The Influence of DO3 Order on the Martensitic Transformation in CuZnAu and
CuZnAl Alloys”, Z. Metallkd., 71, 704-707 (1980) (Theory, 21)
[1980Mur] Murphy, S., “Solid State Reactions in the Low-Copper Part of the Aluminium-Copper-Zinc
System”, Z. Metallkd., 71, 96-102 (1980) (Equi. Diagram, Experimental, #, *, 12)
190
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Al–Cu–Zn
[1984Man] Mannan, S.K., Ganesan, V., Vijayalakshmi, M., Seetharaman, V., “Isothermal
Decomposition of the '-Phase in a Cu-Zn-Al Alloy”, J. Mater. Sci., 19, 2465-2472 (1984)
(Experimental, 24)
[1985Mur] Murray, J.L., “The Aluminium-Copper System”, Int. Met. Rev., 30, 211-233 (1985) (Equi.
Diagram, Review, #, *, 230)
[1986Ahl1] Ahlers, M., “Phase Relationship and Stabilities of the , and Various Martensite Phases
in Brasses” in “Noble Metals Alloys: Phase Diagrams, Alloy Phase Stability,
Thermodynamic Aspects, Properties and Special Features”, Conf. Proc. TMS-AIME,
Massalski, T.B., Pearson, W.B., Bennett, L.H., Chang, Y.A., (Eds.), Warrendale, PA,
87-108 (1986) (Review, *, 42)
[1986Ahl2] Ahlers, M., “Martensite and Equilibrium Phases in Cu-Zn and Cu-Zn-Al Alloys”, Prog.
Mater. Sci., 30(3), 135-186 (1986) (Equi. Diagram, Review, *, 145)
[1986Myk] Mykura, N., Zhu, Y.H., Murphy, S., “Solid State Reactions in Zn-Al Based Alloys”, Canad.
Metall. Quart., 25(2), 151-159 (1986) (Equi. Diagram, Experimental, #, *, 14)
[1986Sug] Sugino, S., Hagiwara, H., “Effects of Aluminium and Nickel on the Activity of Zinc in
Molten Copper” (in Japanese), J. Jpn. Inst. Metals, 50, 1068-1074 (1986) (Experimental,
Thermodyn. *, 19)
[1986Yan] Yang, D., Zhu, M., “Analysis of Phases Formed in a CuZnAl Shape Memory Alloy under
Equilibrium Conditions” (in Chinese), J. Dalian Inst. Tech., 25(2), 81-85 (1986)
(Experimental, 8)
[1987Lon] Longauer, S., Billy, J., Janak, G., Karel, V., “Breakdown of the Phase in CuZnAl Shape
Memory Alloys”, Kovove Mater., 25(3), 150-154 (1987) (Experimental, 5)
[1987Sak] Sakamoto, H., Shimizu, K., ”Pseudoelasticity Due to Consecutive 1 - ’1 - ’1
Transformations and Thermodynamics of the Transformation in a Cu-14.4Al-3.6Ni Alloy”,
Trans. Jpn. Inst. Met., 28 (9), 715-722 (1987) (Experimental, 16)
[1987Sca] Scarsbrook, G., Stobbs, W.M., “The Martensitic Transformation Behaviour and
Stabilisation of Rapidly Quenched CuZnAl Ribbons”, Acta Metall., 35(1), 47-56 (1987)
(Crys. Structure, Experimental, 18)
[1988Ara] Arab, A.A., Ahlers, M., “The Stabilization of Martensite in Cu-Zn-Al Alloys”, Acta Metall.,
36 (9), 2627-2638 (1988) (Mechan. Prop., Experimental, 21)
[1988DeG] de Graef, M., Delaey, L., Broddin, D., “High Resolution Electron Microscopic Study of the
X-Phase in Cu-Al and Cu-Al-Zn Alloys”, Phys. Status Solidi A, 107, 597-609 (1988)
(Experimental, 25)
[1988Kis] Kisi, E.A., “Problems in Determining the Structure of Brass Alloy Cu64.8Al23.8Zn6.9 by
Powder and Single-Crystal Neutron Diffraction”, Mater. Sci. Forum, 27-28, 89-94 (1988)
(Crys. Structure, Experimental, 13)
[1988Kuz] Kuznetsov, G.M., Krivosheeva, G.B., Shaina, M.V., “Study of Alloys of the Al-Mg-Zn-Cu
System” (in russian) Izv. Vyssh. Uchebn. Zaved., Tsvetn. Metall., (5), 88-91 (1988) (Equi.
Diagram, 8)
[1988Mun] Muntasell, J., Tamarit, J.H., Guilemany, J.M., Gil, J., Cesari, E., “Martensitic
Transformation Differences on Poly and Single CuZnAl Crystals”, Mater. Res. Bull.,
23(11), 1585-1590 (1988) (Crys. Structure, Experimental, 11)
[1988Ort] Ortin, J., Planes, A., “Thermodynamic Analysis of Thermal Measurements in
Thermoelastic Martensitic Transformations”, Acta Metall., 26(8), 1875-1889 (1988)
(Thermodyn., 36)
[1988Tsu] Tsumura, R., Rios-Jara, D., Chavez, M., Rodriguez, L., Akachi, T., Escudero, R., “Specific
Heat Measurements of the 1 and ’1 Phases in a Copper-Zinc-Aluminium Alloy”, Phys.
Status Solidi A, A105 (2), 411-418 (1988) (Thermodyn., Experimental, 10)
[1988Yev] Yevsyukov, V.A., Garshina, M.N., Agapitova, N.V., “Amplitudinal Dependence of Internal
Friction of Alloys Cu-Zn-Al in the Presence of Strain-Induced Martensite”, Phys. Met.
Metallogr., 65 (2), 172-174 (1988), translated from Fiz. Metal. Metalloved., 65(2), 395-396
(1988) (Experimental, Mechan. Prop., 3)
191
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Al–Cu–Zn
[1989Cha] Chandrasekaran, M., Cooreman, L., Van Humbeeck, J., Delaey, L., “Martensitic
Transformation in AlCuZn : Changes in Transformation Entropy Due to Post-Quench
Aging in the or Martensitic Condition”, Scr. Metall., 23(2), 237-239 (1989)
(Experimental, 14)
[1989Tol] Tolley, A., Jara, R.D., Lovey, F.C., “18R to 2H Transformations in Cu-Zn-Al Alloys”, Acta
Metall., 37 (4), 1099-1108 (1989) (Crys. Structure, Experimental, 12)
[1990Gui] Guilemany, J.M., Gil, F.J., “The Relationship Between Chemical Composition and
Transformation Temperatures, Ms and As, in Polycrystals and Single Crystals of Cu-Zn-Al
Shape-Memory Alloys”, Thermochim. Acta, 167, 129-138 (1990) (Experimental, 6)
[1991Dim] Dimitropoulos, C., Borsa, F., Rubini, S., Gotthardt, R., “NMR Techniques Applied to
Martensitic Transformation”, J. Phys. Colloque C4, 1, 307-315 (1991) (Crys. Structure,
Experimental, Phys. Prop., 4)
[1991Gui1] Guilemany, J.M., Gil, F.J., “The Gibbs Free Energies of Thermal and Stress-Induced
Martensite Formation in Cu-Zn-Al Single Crystal Shape Memory Alloys”, Thermochim.
Acta, 182, 193-199 (1991) (Experimental, Thermodyn., 14)
[1991Gui2] Guilemany, J.M., Gil, F.J., “The Martensitic Transformation Entropy Values of Thermal
and Mechanical Origin in Shape Memory Cu-Zn-Al Single Crystals”, Thermochim. Acta,
190, 185-189 (1991) (Experimental, Thermodyn., 7)
[1992Ahl] Ahlers, M., Pelegrina, L.J., “The Martensitic Phases and Their Stability in Cu-Zn and
Cu-Zn-Al Alloys-II. The Transformation Between the Close Packed Martensitic Phases”,
Acta Metall. Mater., 40(12), 3213-3220 (1992) (Crys. Structure, Experimental,
Thermodyn., 16)
[1992Ame] Amengual, A., “Partial Cycling Effects on the Martensitic Transformation of CuZnAl
SMA”, Scr. Metall. Mater., 26, 1795-1798 (1992) (Crys. Structure, Experimental, Phys.
Prop., 16)
[1992Bob] Bobic, I., Djuric, B., Jovanovich, M.T., Zec, S., “Improvement of Ductility of a Cast
Zn-25Al-3Cu Alloy”, Mater. Charact., 29, 277-283 (1992) (Equi. Diagram, Mechan.
Prop., 5)
[1992Cia] Ciach, R., Podosek, M., “Phase Transformations in Aluminum-Zinc alloys Solidifying at
Various Rates”, J. Therm. Anal., 38(9), 2077-2085 (1992) (Thermodyn., 13)
[1992Gui] Guilemany, J.M., Peregrin, F., “Comprehensive Calorimetric, Thermodynamic and
Metallographic Study of Copper-Aluminum-Manganese Shape Memory Alloys”, J. Mater.
Sci., 27(4), 863-868 (1992) (Crys. Structure, Equi. Diagram, Thermodyn., 12)
[1992Pel] Pelegrina, J.L., Ahlers, M., “The Martensitic Phases and Their Stability in Cu-Zn and
Cu-Zn-Al Alloys- III. The Transformation Between the High Temperature Phase and the 2H
Martensite”, Acta Metall. Mat.,40(12), 3221-3227 (1992) (Crys. Structure, Experimental,
Thermodyn., 10)
[1992Sau] Saule, F., Ahlers, M., Kropff, F., Rivero, E.B., “The Martensitic Phases and their Stability
in Copper-Zinc and Copper-Zinc-Aluminum Alloys - IV. The Influence of Lattice
Parameter Changes and Evaluation of Phase Stabilities”, Acta Metall. Mat., 40(12),
3229-3238 (1992) (Crys. Structure, 29)
[1992Tak] Takezawa, K., Sato, S., “Composition Dependence of Bainite Morphology in Cu-Zn-Al
Alloys”, Mater. Trans., JIM, 33(2), 102-109 (1992) (Crys. Structure, Equi. Diagram,
Experimental, 30)
[1992Gho] Ghosh, G.., van Humbeeck, J., ”Aluminium - Copper - Zinc”, MSIT Ternary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 10.10277.1.20, (1992) (Crys. Structure, Equi.
Diagram, Assessment, 71)
[1993Ahl] Ahlers, M., “Martensite and Equilibrium Phases in Hume-Rothery Noble-Metal Alloys”,
J. Phys.: Condens. Matter, 5, 8129-8148 (1993) (Calculation, Review, Theory,
Thermodyn., 78)
192
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Al–Cu–Zn
[1993Che] Chen, S.L., Chang, Y.A., “A Thermodynamic Analysis of the Al-Zn System and Phase
Diagram Calculation”, Calphad, 17(2), 113-124 (1993) (Equi. Diagram, Thermodyn.,
Calculation, #, 55)
[1993Kow] Kowalski, M., Spencer, P.J., “Thermodynamic Reevaluation of the Cu-Zn System”,
J. Phase Equilib., 14(4), 432-438 (1993) (Equi. Diagram, Thermodyn., Calculations, #, 36)
[1993Lex] Lexcellent, C., Torra, V., Raniecki, B., “Hysteresis Behaviour of Thermoelastic Alloys -
Some Shape-Memory Alloys Models” (in French), J. Phys. III, 3, 1463-1477 (1993) (Crys.
Structure, Experimental, Thermodyn., 23)
[1994Bou] Bourbon, G., Lexcellent, C., “Thermodynamic Modeling of the Cyclic Behaviour of the
Shape-Memory Alloys Ti-Ni and Cu-Zn-Al in Nonlinear Profiles” (in French), J. Phys. IV,
Colloque C3, 4, 145-150 (1994) (Experimental, Phys. Prop., Thermodyn., 6)
[1994Hsu] Hsu, T.Y., Zhou, X.W., “Thermodynamic Consideration of Formation Mechanism of 1
Plate in Cu-Base Alloys”, Metall. Mater. Trans. A, 25A, 2555-2563 (1994) (Calculation,
Thermodyn. 39)
[1994Men] Meng, X.K., Kang, M.K., Yang, Y.Q., Liu, D.H., “The Formation Mechanism of Plate in
Cu-Zn and Cu-Zn-Al Alloys”, Metall. Mater. Trans. A, 25A, 2601-2608 (1994) (Crys.
Structure, Mechan. Prop., Experimental, 20)
[1994Mur] Murray, J.L., “Al-Cu (Aluminium-Copper)” in “Phase Diagrams of Binary Copper Alloys”,
Subramanian, P.R., Chakrabarti D.J., Laughlin, D.E., (Eds.), ASM International, Materials
Park, OH, 18-42 (1994) (Equi. Diagram, Cryst. Struct., Thermodyn., Review, 226)
[1994Van] Van, T.D., Segers, L., Winand, R., “Determination of Thermodynamic Properties of
Ternary Al-Cu-Zn Alloys by Electromotive Force Method”, J. Electrochem. Soc., 141(4),
927-933 (1994) (Equi. Diagram, Experimental, Thermodyn., #, 34)
[1994Wu] Wu, M.H., Hamada, Y., Wayman, C.M., “Transformation Characteristics of 1 Plates in
Cu-Zn-Al Aloys”, Metall. Mater. Trans. A, 25A, 2581-2599 (1994) (Crys. Structure,
Experimental, Kinetics, 39)
[1995Ahl] Ahlers, M., “Phase Stability of Martensinic Structures”, J. Phys. IV, Colloque C8, 5, 71-80
(1995) (Crys. Structure, Experimental, Thermodyn., 17)
[1995Cha] Charbonnier, P., Buffard, L., Macqueron, J.L., Morin, M., Weynant, E., “Atomic Ordering
and Martensitic Transformation in Cu-Zn-Al and Cu-Al-Ni Industrial Alloys”, J. Phys. IV,
Colloque C2, 5, 159-163 (1995) (Experimental, Thermodyn., 13)
[1995Gue] Guenin, G., “Martensitic Transformation and Thermomechanical Properties”, Key Eng.
Mater., 101-102, 339-392 (1995) (Crys. Structure, Phys. Prop., Thermodyn., Review, 73)
[1995Isa] Isalgue, A., Lovey, F.C., Pelegrina, J.L., Torra, V., “Time Evolution in Static Phase and
Dynamic Martensite Coexistence (Cu-Zn-Al Shape Memory Alloys)”, J. Phys. IV,
Colloque C8, 5, 853-858 (1995) (Crys. Structure, Experimental, 17)
[1995Pri1] Prieb, V., Steckmann, H., “Pseudo-Plastic Behaviour of Single-Crystals of Cu-Base
Memory Alloys”, J. Phys. IV, Colloque C8, 5, 907-912 (1995) (Crys. Structure,
Experimental, Thermodyn., 5)
[1995Pri2] Prieb, V., Link, T., Feller-Kniepmeier, M., Steckmann, H., Poljakova, N.A., Udovenko,
V.A., “Influence of the Structure and Orientation of the Parent Phase on the Hysteresis of
Single-Crystal Shape Memory Alloys”, J. Phys. IV, Colloque C8, 5, 913-918 (1995) (Crys.
Structure, Phys. Prop., Thermodyn., 6)
[1995Sau] Saule, F., Ahlers, M., “Stability, Stabilization and Lattice Parameters in Cu-Zn-Al
Martensites”, Acta Metall. Mater., 43 (6), 2373-2384 (1995) (Crys. Structure,
Experimental, Thermodyn., 25)
[1995Tsu] Tsuchiya, K., Marukawa, K., “The Mechanism of Rubber-like Behavior in Cu-Zn-Al
Martensite”, J. Phys. IV, Colloque C8, 5, 853-858 (1995) (Crys. Structure, Mechan.
Prop., 17)
[1996Gar] Garcia, J., Pons, J., Cesari, E., “Effect of Precipitates on the Stabilization of Martensite in
Cu-Zn-Al Alloys”, Mater. Res. Bull., 31(6), 709-715 (1996) (Experimental, Phys. Prop.,
Mechan. Prop., 21)
193
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[1997Som] Somoza, A., Macchi, C., Romero, R., “Thermal Generation of Point Defects in Cu-Zn-Al
Alloys”, Mater. Sci. Forum, 255-257, 587-589 (1997) (Experimental, Thermodyn., 10)
[1997Zha] Zhang, M.R., Yang, D.Z., Tadaki, T., Hirotsu, Y, “Effects of Addition of Small Amounts of
Fourth Elements on Structure, Crystal Structure and Shape Recovery of Cu-Zn-Al Shape
Memory alloys”, Scr. Mater., 36(2), 247-252 (1997) (Crys. Structure, Experimental, 19)
[1998Buj] Bujoreanu, L.G., Craus, M.L., Stanciu, S., Sutiman D., “On the 2 to Phase
Transformation in a Cu-Zn-Al Based Shape Memory Alloy”, J. Alloys Compd., 278,
190-193 (1998) (Experimental, 12)
[1998Gal] Gall, K., Sehitoglu, H., Maier, H.J., Jacobus, K., “Stress-Induced Martensitic Phase
Transformation in Polycrystalline Cu-Zn-Al Shape Memory Alloys under Different Stress
States”, Metall. Mater. Trans. A, 29A (3), 765-773 (1998) (Mechan. Prop.,
Experimental, 58)
[1998Lia] Liang, H., Chang, Y.A., “A Thermodynamic Description for the Al-Cu-Zn System”,
J. Phase Equilib., 19 (1), 25-37 (1998) (Equi. Diagram, Thermodyn., Calculation, *, #, 72)
[1998Lop] Lopez-Hirata, V.M., Zhu, Y.H., Saucedo-Munoz, M.L., Hernandez, F., “Mechanical
Alloying of Zn-Rich Zn-Al-Cu Alloys”, Z. Metallkd., 89(3), 230-232 (1998) (Crys.
Structure, Mechan. Prop., 8)
[1998Man] Manosa L., Jurado M., Gonzalez-Comas A., Obrado E., Planes A., Zaretsky J., Stassis C.,
Romero R., Somoza A., Morin M., “A Comparative Study of the Post-Quench Behavior of
Cu-Al-Be and Cu-Zn-Al Shape Memory Alloys”, Acta Mater., 46(3), 1045-1053 (1998)
(Phys. Prop., Experimental, 46)
[1998Wei] Wei, Z.G., “Transformation Relaxation and Aging in a CuZnAl Shape-Memory Alloy
Studied by Modulated Differential Scanning Calorimetry”, Metall. Mater. Trans. A,
29A(11), 2697-2705 (1998) (Experimental, Kinetics, Thermodyn., 36)
[1999Lov] Lovey, F.C., Torra, V., “Shape Memory in Cu-Based Alloys: Phenomenological Behavior
at the Mesoscale Level and Interaction of Martensitic Transformation with Structural
Defects in Cu-Zn-Al”, Prog. Mater. Sci., 44, 189-289 (1999) (Review, Thermodyn., Crys.
Structure, Theory, 163)
[1999Ago1] Agouram, S., Bensalah, M.O., Ghazali, A., “A Micromechanical Modelling of the
Hysteretic Behavior in Thermally Induced Martensitic Phase Transitions: Application to
Cu-Zn-Al Shape Memory Alloys”, Acta Mater., 47(1), 13-21 (1999) (Crys. Structure,
Experimental, Thermodyn. 27)
[1999Ago2] Agouram, S., Bensalah, M., Ghazali, A., “Thermomechanical Modelling of the One-Way
Memory Effect of a Cu-Zn-Al Shape Memory Alloys”, Compt. Rend. Acad. Sci. Paris, Ser.
II-B, 327, 573-579 (1999) (Experimental, Thermodyn., 13)
[1999Lon] Longauer, S., Makroczy, P., Janak, G., Longauerova, M., “Shape Memory in Cu-Zn-Al
Alloy with a Dual Phase Microstructure”, Met. Mater., 37(3), 120-126 (1999) translated
from Kovove Mater., 37(3), 173-183 (1999) (Crys. Structure, Magn. Prop., Mechan.
Prop., 18)
[1999Rom] Romero, R., Somoza, A., “Point Defects Behavior in Cu-Based Shape Memory Alloys”,
Mater. Sci. Eng. A, A273-275, 572-576 (1999) (Crys. Structure, Experimental, 25)
[1999Zhu] Zhu, Y.H., Hernandez, R.M., Banos, L., “Phase Decomposition in Extruded Zn-Al Based
Alloy”, J. Mater. Sci., 34, 3653-3658 (1999) (Equi. Diagram, Experimental, 11)
[2000Ans] Ansara, I., Burton, B., Chen, Q., Hillert, M., Fernandez-Guillermet, A., Fries, S.G., Lukas,
H.L., Seifert, H.-J., Oates, W.A., “Model for Composition Dependence”, Calphad, 24(1),
20-40 (2000) (Calculation, Equi. Diagram, Review, Thermodyn., 26)
[2000Dor] Dorantes-Rosales, H.J., Lopez-Hirata, V.M., Mendez-Velazquez, J.L., Saucedo-Munoz,
M.L., Hernandez-Silva, D., “Microstructure Characterization of Phase Transformations in
a Zn-22 wt%Al-2 wt%Cu alloy by XRD, SEM, TEM and FIM”, J. Alloys Compd., 313,
154-160 (2000) (Crys. Structure, Equi. Diagram, Experimental, 15)
194
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[2000Kra] Kraft, T., “The Influence of Kinetic Effects on the Equilibrium Phase Diagram During
Solidification in the Aluminium-rich Corner of the Quaternary System Al-Cu-Mg-Zn”,
Z. Metallkd., 91(3), 221-226 (2000) (Calculation, Equi. Diagram, Kinetics, 19)
[2000Leg] Legendre, B., Feutelais, Y., San Juan, J.M., Hurtado, I., “Enthalpy of Formation of the
Ternary ’ Phase in the Al-Cu-Zn System”, J. Alloys Compd., 308, 216-220 (200)
(Experimental, Thermodyn., 11)
[2000Pel] Pelegrina, J.L., Romero, R., “Calorimetry in Cu-Zn-Al Alloys Under Different Structural
and Microstructural Conditions”, Mater. Sci. Eng. A, A282, 16-22 (2000) (Crys. Structure,
Experimental, Thermodyn., 33)
[2000Sat] Satto, C., Jansen, J., Lexcellent, C., Schryvers, D., “Structure Refinement of L21 Cu-Zn-Al
Austenite, Using Dynamical Electron Diffraction Data”, Solid State Commun., 116,
273-277 (2000) (Crys. Structure, Experimental, 8)
[2000Yaw] Yawny, A., Lovey, F.C., Sade, M., “Pseudoelastic Fatigue of Cu-Zn-Al Single Crystals: the
Effect of Concominant Diffusional Processes”, Mater. Sci. Eng. A, A290, 108-121 (2000)
(Crys. Structure, Experimental, Thermodyn., 29)
[2000Zel] Zel’dovich, V.I., Khmoskaya, I.V., Frolova, N.Yu., “Structural Mechanism of the -Phase
Formation and Martensitic Transformation in Cu-Zn-Al Alloys”, Phys. Met. Metallogr.,
89(3), 292-299 (2000) translated from Fiz. Met. Metalloved. 89(3), 85-92 (2000) (Phys.
Prop., Experimental, 21)
[2001Bek] Beke, D.L., Daroczi, L., Lexcellent, C., Mertinger, V., “Effect of Hydrostatic Pressures on
Thermoelastic Martensitic Transformations”, J. Phys. IV (France), Pr8, 11, 119-124 (2001)
(Crys. Structure, Phys. Prop., 14)
[2001Che] Chen, S.-L., Daniel, S., Zhang, F., Chang, Y.A., Oates, W.A., Schmid-Fetzer, R., “On the
Calculation of Multicomponent Stable Phase Diagrams”, J. Phase Equilib., 22, 373-378
(2001) (Calculation, Equi. Diagram, #, 26)
[2001Liu] Liu, X.J., Wang, C.P., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Stability Among the
(A1), (A2), and (D83) Phases in the Cu-Al-X System”, J. Phase Equilib., 22, 431-438
(2001) (Equi. Diagram, Experimental, 14)
[2001Zhu1] Zhu, Y.H., Lee, W.B., Yeung, C.F., Yue, T.M., “EBSD of Zn-Rich Phases in Zn-Al-Based
Alloys” Mater. Charact., 46(1), 19-23 (2001) (Crys. Structure, Experimental, 9)
[2001Zhu2] Zhu, Y.H., Yeung, C.F., Lee, W.B., “Phase Decomposition of Cast Alloy ZnAl11Cu3”,
Z. Metallkd., 92, 1327-1330 (2001) (Equi. Diagram, Experimental, 14)
[2002Che] Chen, S.-L., Daniel, S., Zhang, F., Chang, Y.A., Yan, X.-Y., Xie, F.-Y., Schmid-Fetzer, R.,
Oates, W.A., “The PANDAT Software Package and its Applications”, Calphad, 26(2),
175-188 (2002) (Calculation, Equi. Diagram, 24)
[2002Gul] Gulay, L.D., Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. “Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Mie] Miettinen, J., “Thermodynamic Description of the Cu-Al-Zn and Cu-Sn-Zn Systems in the
Copper-Rich Corner”, Calphad, 26(1), 119-139 (2002) (Calculation, Equi. Diagram,
Thermodyn., #, 20)
[2003Gro] Gröbner, J., “Al-Cu (Aluminium - Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 68)
[2003Leb] Lebrun, N., “Cu-Zn (Copper-Zinc)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 18)
[2003Per] Perrot, P., “Al-Zn (Aluminium-Zinc)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 41)
195
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Al)
660.452
cF4
Fm3m
Cu
a = 404.96 pure Al at 25°C, [Mas2]
dissolves up to 2.48 at.% Cu at 548.2°C
[2003Gro]
( Cu)
1084.87
cF4
Fm3m
Cu
a = 361.48 pure Cu at 25°C, [V-C]
dissolves up to 19.7 at.% Al at 559°C
[2003Gro]; disolves up to 35.84 at.% Zn
at 300°C [2003Leb]
( Zn)
419
hP2
P63/mmc
Mg
a = 266.46
c = 494.61
pure Zn at 22°C, [V-C]
dissolves up to 1.5 at.% Cu at 424°C
[2003Leb]
, CuAl2 591
tI12
I4/mcm
CuAl2
a = 605.0
c = 487.0
from 31.9 to 33.0 at.% Cu
at 33.3 at.% Cu, [1985Mur]
1, CuAl(h)
624-560
o*32 a = 408.7
b = 1200
c = 863.5
49.8 to 52.4 at.% Cu
[V-C2, Mas2, 1985Mur]
Pearson symbol: [1931Pre]
2, CuAl(r)
561
mC20
C 2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
[1985Mur],
from 49.8 to 52.3 at.% Cu
1, Cu47.8Al35.5(h)
590-530
oF88 - 4.7
Fmm2
Cu47.8Al35.5
a = 812
b = 1419.85
c = 999.28
55.2 to 59.8 at.% Cu, [Mas2, 1994Mur]
structure: [2002Gul]
2, Cu11.5Al9(r)
< 570
oI24 - 3.5
Imm2
Cu11.5Al9
a = 409.72
b = 703.13
c = 997.93
55.2 to 56.3 at.% Cu, [Mas2, 1985Mur]
structure: [2002Gul]
1, Cu100-xAlx958-848
cubic ?
-
- 37.9 x 40.6 [1985Mur]
2, Cu1+xAl
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
0.22 x 0.57
[1985Mur]
1, Cu100-xAlx hR*
-
a = 869.0
= 89.78°
38.1 x 40.7 [1985Mur]
0, Cu100-xAlx1037-800
cI52
I43m
Cu5Zn8-
- 31 x 40.2 [1985Mur]
, Cu5(CuxZn2-2xAlx)7
, Cu9Al4 < 890
, Cu5Zn8
< 835
cP52
P43m
Cu9Al4
cI52
I43m
Cu5Zn8
a = 870.68
a = 886.9
Zn free 69.23 at.% Cu, [V-C2]
Al free [V-C2]
Cu9Al4 is ordered with Cu and Al on
2nd sites,
cP52-Cu9Al4 type
196
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
Table 2: Invariant Equilibria
2, Cu100-xAlx363°C
TiAl3-type
long period
super- lattice
a = 366.6
c = 367.5
22 x 23.5
at 77.9 at.% Cu, [1985Mur]
', CuZn(r)
468
cP2
Pm3m
CsCl
a = 295.9 at 49.5 at % Zn [V-C2],
from 44.8 to 50.0 at.% Zn
, CuZn3
700-560
hP3
P6
CuZn3
a = 427.5
c = 259.0
[V-C2],
from 72.4 to 76.0 at.% Zn [1985Mur]
, CuZn4
598
hP2
P63/mmc
Mg
a = 274.18
c = 429.39
[V-C2],
from 78 to 88.0 at.% Zn
, (Cu,Zn,Al)
, CuZn(h)
903-454
, CuAl
1049-559
cI2
Im3m
W
a = 299.67
a = 285.64
a = 294.6
[V-C2],
from 36.1 to 55.8 at.% Zn
at 672°C in two-phase field, [1985Mur]
at 75.7 at.% Cu, 580°C [1985Mur] solid
solubility range: 70.6 to 82.0 at.%Cu
* , Cu5Zn2Al3< 740
* ’, Cu3Zn
cP2
CsCl
hR9
a = 290.4
a = 293.2
a = 867.6
= 27.41°
Cu40Zn7Al53 [1942Koe]
at Cu46Zn20Al34 [1942Koe]
rhombohedral superstructure of 5 CsCl
lattice [1942Koe], [1975Mur, 2000Dor]
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Zn
L + + 625 P2 L 29.7
26.3
33.5
27.9
26.9
45.4
46.7
44.1
43.4
28.3
19.8
28.0
L + 2 1 + 620 U6 L
2
62.6
22.0
25.5
24.0
35.2
53.0
51.4
51.0
2.2
25.0
23.1
25.0
L + 1 + 580 U8 L 65.9
29.4
47.0
30.0
31.6
48.1
32.5
46.0
2.5
22.5
20.5
24.0
1 + + 480 E2 19.1
15.2
26.2
17.2
43.2
44.4
48.0
40.2
37.7
40.4
25.8
42.6
L + (Al) + 422 U9 L
(Al)
44.5
66.8
54.4
52.1
11.3
32.0
1.4
39.0
44.2
1.2
44.2
8.9
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
197
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
Table 3: Saturation Concentrations of Al and Cu in (Zn) at Different Temperatures
L+ (Al) + 396 U10 L
(Al)
28.2
50.4
42.0
11.2
9.4
39.2
1.5
22.0
62.4
10.4
56.5
66.8
L (Al) + + (Zn) 377 E3 L
(Al)
(Zn)
15.4
37.0
3.3
3.1
3.7
1.4
15.3
2.9
80.9
61.6
81.4
94.0
+ (Al)" (Al)' + 288 U11
(Al)"
(Al)'
59.2
50.3
80.5
2.8
35.7
1.8
1.4
16.6
5.1
47.9
18.1
80.6
(Al)" + (Al)' + (Zn) 278 U12 (Al)"
(Al)'
(Zn)
49.1
2.4
83.4
2.4
1.5
18.7
0.8
3.0
49.4
78.9
15.8
94.6
(Al)' + + (Zn) 268 U13 (Al)'
(Zn)
43.3
0.7
52.7
1.9
0.8
17.5
39.2
1.7
55.9
81.8
8.1
96.4
Temperature [°C] Al (at.%) Al (mass%) Cu (at.%) Cu (mass%)
375
350
300
275
250
3.0
2.7
2.2
1.9
1.5 (0.9)
1.25
1.1
0.9
0.8
0.6 (0.4)
2.8
2.5
2.1
1.7
1.2 (0.9)
2.8
2.5
2.1
1.7
1.2 (0.9)
Reaction T [°C] Type Phase Composition (at.%)
Al Cu Zn
Cu,at.%
Zn, at.%
220
240
260
280
300
320
220
240
260
280
300
�´
�
Al
99.01.0
Al
Cu
90.010.0
Al
Zn
Fig. 1: Al-Cu-Zn.
Solvus of the (Al)
phase and three phase
equilibrium (Al)+ +
at different
temperatures [°C]
198
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
Fig
. 2a:
Al-
Cu
-Zn
. R
eact
ion s
chem
e, p
art
1
Cu
-Zn
Al-
Cu
A-B
-C
l +
(αC
u)
β9
03
p3
l +
β
γ 0
10
37
p1
Lτ
+ ε 2
74
0e 4
Al-
Cu
-Zn
ε 1+
γ 0
L
+ γ1
U2
Al-
Zn
l +
γ1
δ6
65
p7
l+
βγ 1
83
5p6
l +
ε2
ε 1
62
4p9
l +
γ1
δ 1
68
6p7
γ 0β
+ γ1
78
0e 3
ε 1
ε 2 +
l
84
8e 2
ε 1 +
γ1
ε 2
85
0p5
γ 0 +
ε1
γ 1
87
3p4
l +
γ0
ε 1
95
8p2
l (
αCu)
+ β
10
32
e 1
ε 1L
+ ε 2
+ γ1
E1
L +
γ0
β +
γ 1U3
L +
ε2
+γ 1
δ
P1
L +
δ +
τε
62
5P2
ε 2 +
δγ 1
+ τ
680
U5L +
ε2
δ +
τU4
L +
ε2
η 1 +
τ6
20
U6
L+
β +
γ0
L +
ε 2 +
γ1
L+
γ 1+
γ 0L
+ ε1
+ γ 1
ε 2+
γ 1+
δL
+ ε 2
+ δ
L+
δ +
τ?
δ +
γ 1 +
τε 2+
γ 1+
τ
δ +
τ +
ε L+
ε +
τ
ε 2+
η 1+
τ
L+
η 1 +
τ
199
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
Fig
. 2b
:
Al-
Cu
-Zn
. R
eact
ion s
chem
e, p
art
2
Cu
-Zn
Al-
Cu
A-B
-C
l +
η1
θ5
91
p10
Al-
Cu
-Zn
ε 2 +
τγ 1
+ η2
U7
Al-
Zn
l +
ε (
ηZn)
42
4p13
δε
+ γ 1
54
8e 8
l (
αAl)
+ θ
548.2
e 7
β (
αCu)
+ γ1
55
9e 6
ε 2ζ 1
+ δ
56
0e 5
ε 2 +
η1
ζ 1
59
0p11
L +
θ (
αAl)
+ τ
42
2U9
L +
η1
θ +
τ5
80
U8
δε
+ γ1 +
τ4
80
E2
(αA
l)´´
+ τ
(αA
l)´
+ ε
28
8U11
L (
αAl)
+ (
ηZn
) +
ε3
77
E3
L +
τ (
αAl)
+ ε
39
6U10
(αA
l)´´
+ε
(αA
l)´+
(ηZ
n)
27
8U12
(αA
l)´´
+ ε
(ηZ
n)
+ τ
26
8U13
(αA
l)´´
(αA
l)´+
(ηZ
n)
27
7e 10
l (
αAl)
+ (
ηZn)
38
1e 9
δ+γ 1
+τ
ε 2+γ1+τ
ε 2+η
1+τ
δ+τ+
ε
L+η
1+τ
ε +
γ 1+
τ
η 1+θ
+τL
+θ+τ
(αC
u)+
β+γ 1
L+
(αA
l)+
τ(α
Al)
+θ+τ
L+
(αA
l)+
ε
(αA
l)+
ε+τ
(αA
l)´´
+(α
Al)
´+τ
(αA
l)´+
ε+τ
(αA
l)´´
+(α
Al)
´+ε
(αA
l)´+
ε+(η
Zn)
(αA
l)´+
(ηZ
n)+
τ(η
Zn
)+ε+
τ
(αA
l)´´
+(η
Zn
)+ε
ca.
351.5
L+
ε+τ
τ+γ 1
+η1
?
l +
δε
57
4p12
200
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
(αCu)
(αCu)+ββ
β+γ
γ
ε2 τL+τ L
δL+δ
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
e1
p1
p2
e2
p9
p10
e7
e9
p13p12p8p6p3
1050(αCu)
β
(αAl)
1000
γ0
950
900
850
ε1
U2P1
U3
γ
800
750
700
650600
550
550
600
650
500
U10
U9
P2
δ
U4
θ
ε
ε2
η1
U8
U6
τ
E1
400
450
E3
(ηZn)
e4
Fig. 4: Al-Cu-Zn.
Isothermal section at
700°C
Fig. 3: Al-Cu-Zn.
Liquidus surface
201
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%(αAl)+L(αAl)
L+τ
γ
τ
ε2δ1
(αCu)
(αCu)+β
β+γδ
β
L
L+δ
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
L+δδ
L+εε
γ
τ+γ
L
(αAl)
(αAl)+L
L+τ
β(αCu)
(αCu)+ββ+γ
δ1
ε2
η1
τ
Fig. 6: Al-Cu-Zn.
Isothermal section at
600°C
Fig. 5: Al-Cu-Zn.
Isothermal section at
650°C
202
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%(αAl)
(αAl)+L
L
ε+L
εδ+ε
δγ
β+γ
β
(αCu)
(αCu)+β
θ+Lθ
η2
L+τ
L+τ+ετ+ε
τ
τ'(ζ1,ζ2)
δ1
τ+γ
γ+ε
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
(αAl)
θ+(α
Al)
L+(αAl)
L+θ+(
αAl)
L+θ
θ+τ'+L
L+τ'
L+τ+ετ
ζ2+τ
τ'
η2
ζ2
δ1
τ+γ
L
L+ε
εγ+εγ
γ+β
β(αCu)
β+(αCu)
τ+ε
δ
(αCu)+γ
θ
Fig. 8: Al-Cu-Zn.
Isothermal section at
500°C
Fig. 7: Al-Cu-Zn.
Isothermal section at
550°C
203
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
(αAl)+θ(αAl)
θ+τ´+(αAl)
L+ε+τ
L+τ
L+ε
(αAl)+τ'
L+(αAl)+τ'
τ+ε
ε
(ηZn)(αCu)
(αCu)+β
β
(αCu)+γ
δ1+γ+τ
τ+γ
τ
τ'
θ
η2
ζ2
δ1
γ
γ+εγ+β
L
L+(αAl)
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
(αCu)
α2
δ1
ζ2
η2
θ
(αAl)
(αAl)'+(αAl)´´
(ηZn)+(αAl)
(ηZn)ε
γ
γ+β
β
τ
τ'
τ'+θ+(αAl)
τ'+(αAl)
ε+τ'+(αAl)
ε+(α
Al)
(ηZn)+εε+γ
ε+τ+γ
ε+τγ+δ1+τ
η2+τor τ´
or τ'
θ+(αAl)
(αCu)+γ
Fig. 10: Al-Cu-Zn.
Isothermal section at
350°C
Fig. 9: Al-Cu-Zn.
Isothermal section at
400°C
204
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
(αCu)
?
τ
θ
(αA
l)'+θ
(αA
l)'+θ
+τ
(αAl)'+τ
(αAl)'+(αAl)´´+τ
(αAl)"+τ
(αAl)"+τ+ε
(αA
l)"+ε+(ηZn)
(ηZn)εγ (αAl)"+(ηZn)
(αAl)"
β
(αAl)'+(αAl)´´
(αAl)´
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
(αCu)
τ'
(αAl)+θ
(αAl)+τ'+θ
(αA
l)+τ'
(αAl)+(ηZn)+τ'
(αAl)+(ηZn)
(αAl)
(ηZn)ε
τ'+(ηZn)
ε+(ηZn)+τ'γ
β
?
θ
Fig. 12: Al-Cu-Zn.
Isothermal section at
240°C
Fig. 11: Al-Cu-Zn.
Isothermal section at
300°C
205
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zn
20
40
60
80
20 40 60 80
20
40
60
80
Cu Zn
Al Data / Grid: at.%
Axes: at.%
(αCu) ? γ ε+γε (ηZn)
(αAl)+(ηZn)
(αAl)
θ
η2
ζ2 η2+τ'
τ'
τ
τ´+ε+(ηZn)
τ+γ+ε
(αAl)+τ´+(ηZn)
η2 +τ´+ε
τ´+θ
+(αA
l)
τ´+(
αAl)
Fig. 13: Al-Cu-Zn.
Isothermal section at
200°C
206
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
Aluminium – Copper – Zirconium
Ludmila Tretyachenko
Literature Data
This evaluation is part of the MSIT Ternary Evaluation Program and incorporates and continues the critical
evaluation made by [1992Tre]. Since then the number of publications on Al-Co-Zr has almost doubled. The
isothermal sections at 800°C across the whole range of compositions and at 500°C for the Al rich part of
the diagram are mainly based on data given by [1970Mar]. The isothermal section at 400°C for Al rich part
was given by [1967Zar]. A tentative reaction scheme for the Cu rich part of ternary system close to the
Al-Cu system was proposed from data of [1964Pan] and [1969Hor]. Eight ternary compounds were reported
to exist at 800°C, one more compound was detected at 500°C by [1970Mar] but this compound was not
observed at 400°C by [1967Zar]. The crystal structures were established for only four of the ternary
compounds. So far most of the data have been considered in the reviews of [1979Dri, 1986Riv, 1990Kum].
[1990Mey1] further studied alloys in the vicinity of the Heusler type phase ZrCu2Al. Samples were melted
of pure elements (Al 99.99%, Cu 99.99% and Zr 99.9%) in argon, annealed at 800°C for 72 h in sealed
quartz ampoules under argon and quenched in ice water. The samples were crushed and powders were
annealed at 600°C for 48 h in quartz ampoules under argon quenched and studied by Debye - Scherrer
method. A new ternary compound Zr6Cu16Al7 was found and the crystal structure of this compound and
those of Zr15Cu71Al14 and Cu4ZrAl3 earlier reported by [1970Mar] were established. The compounds
ZrCu2Al and Zr6Cu16Al7 were not obtained as a single phase; but the alloys of the corresponding
compositions contained some amounts of other phases [1989Mey, 1990Mey1, 1990Mey2]. It is well
possible that those samples did not reach the equilibrium states because of far shorter heat treatments than
those applied by [1970Mar]. Interaction of ZrCu2Al with hydrogen has been studied [1989Mey, 1990Mey1,
1990Mey2].
Phase equilibria in the Al rich part of the Al-Cu-Zr system have been studied by [1997Soa, 1998Soa]. Six
alloys containing up to 14 at.% Zr and 25 at.% Cu were melted in an arc furnace by [1997Soa] and three Al
rich Al-Cu alloys with 0.4 and 1.1 at.% Zr were prepared in a resistance furnace by [1998Soa]. Both used
high purity elements and argon atmosphere. To determine by differential thermal analysis the temperatures
of the phase transformations the alloys were annealed at temperatures chosen after the results of DTA and
quenched in salty ice water. The alloys were analyzed by scanning electron microscopy (SEM) and energy
dispersive spectroscopy (EDS). Two earlier identified compounds were confirmed to exist. However
instead of the compound with the composition of 64Al-24Cu-12Zr (at.%) reported by [1970Mar], another
phase was found and its crystal structure established. The stability of the L12 (Cu3Au type) phase in
mechanically alloyed Al6-xCuxZr2 over the range 0 x 1 has been studied by [1991Des1, 1991Des2]. The
alloy powders were prepared ball-milling elemental powders of 99.99%, Al 99.999% Cu and 99.99% Zr
with significant amount of ZrH2 in the initial zirconium powder. The powders were studied using X-ray
diffraction (XRD) and differential scanning calorimetry (DSC).
[2002Moo] used elemental powders of Al 99.5%, Cu 99.5% and Zr 99.9% as starting materials to prepared
by planetary ball milling (PBM) powders of (Al+12.5 at.% Cu)3Zr with a nanocrystalline microstructure.
Subsequently the powder was sintered by spark plasma sintering (SPS) at 500, 600, 700 and 800°C with
subsequent holding times of 0, 180 and 300 seconds. XRD, SEM, TEM results were recorded, particle size
and density measured and optical microscopy was used to investigate and document the samples.
Magnetic susceptibility and lattice parameters of ZrCu1.2Al0.8 alloy have been measured by [1992Sle] in
the range between 5 K and room temperature. The alloy was arc melted from spectrally pure components
and annealed at 727°C for 7 days. The susceptibility was investigated by Faraday method at temperatures
between 80 and 600 K and a magnetic field of 6 kOe.
Amorphous alloys of the Al-Cu-Zr system have been studied by [1991Ino] using X-ray absorption
spectroscopy at room temperature and elevated temperatures, below and above the glass transition
temperature. [1997Sch] examined structural changes at the glass transition and in the undercooled liquid
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region of the metallic glass Zr65Cu27.5Al7.5, prepared by ultra rapid quenching in argon atmosphere.
[1997Kan] measured the specific heat of Zr65Cu7.5Al27.5 metallic glass - in the temperature range 77-800 K
by calorimeter at a heating rate of 5 K·min-1. The crystallization process was examined using differential
scanning calorimetry. [1998Tur] measured the enthalpies of formation of amorphous Al-Cu-Zr alloys in the
Zr0.65Cu0.35-Zr0.65Al0.35 section using the alloys prepared by melt spinning technique of iodine zirconium
(99.98 mass%), electrolytic copper (99.99 mass%) and high purity aluminium (99.995 mass%). The
enthalpies of formation of the amorphous alloys were determined by means of the solution calorimetry in a
high temperature isoperibolic Calvet type solution calorimeter.
Thermodynamic properties of liquid Al-Cu-Zr alloys were measured by high temperature calorimetry at
1177 to 1212 and at 1737 to 1807°C [1998Wit]. The samples were prepared from Cu (99.98%), Al
(>99.99%) and Zr (99.8%). The measurements were performed under pure argon at atmospheric pressure
for the alloys located in 10 vertical sections with various xCu/xZr, xCu/xAl and xAl/xZr ratios. [2001Aki]
developed a phenomenological model of ternary mixtures based on the Flory approximation and derived
expressions were solved numerically for liquid Al-Cu-Zr alloys.
A study of behavior of the superplastic Al-4.1Cu-0.5Zr (mass%) alloy during creep at a constant flow stress
was made by [1990Poy] using an investigation of structure at various stages of creep by means of optical
microscopy.
[1974Bus] studied the ageing of Al-Cu-Zr alloys with Al contents up to 7 mass% Al and 0.525 mass% Zr.
The alloys have been prepared by induction melting, annealed at 950°C for 40 h, hot forged, heated at 950°C
for 15 min in vacuum and quenched. The aging has been carried out at 800°C and 10-2 Torr.
[1984Kai] studied an influence of grain boundaries on superplastic behavior of the Al-2Cu-0.16Zr (at.%)
using an electron microscopy analysis.
Heterogeneous precipitation behavior of partially coherent intermediate phases on ZrAl3 dispersoids has
been studied by [1991Kan] in Al-4Cu-0.18Zr (mass%) alloys. The melted alloys have been homogenized
at 470°C for 86.4 ks, hot and cold rolled and subjected to the following heat treatment: solution treated at
470°C for 3.6 ks, quenched in bath held at 200°C and aged for times up to 60 ks. Subsequently they were
examined by TEM.
Binary Systems
The Al-Cu phase diagram assessed by [2003Gro] is accepted. The Al-Zr system is taken from [1993Oka].
The accepted Cu-Zr phase diagram is based on the assessment [2003Sem]. However, the eutectoid
decomposition of Zr3Cu8, which was established at 612°C by [1986Kne] and supposed to take place at a
temperature below 600°C according to [1998Bra], is taken into account.
Solid Phases
Three phases of nine reported by [1970Mar] were known earlier. These are the Heusler phase ZrCu2Al ( 4),
the Laves phase ZrCuxAl2-x ( 5) and Zr2CuAl5 ( 8). The crystal structure of one more phase, 7, was
established by [1970Mar]. The crystal structure of remaining five phases reported by [1970Mar] was not
determined. The existence of the Heusler phase ZrCu2Al also was confirmed by [1989Mey, 1990Mey1,
1990Mey2], but a single-phase region of this phase was not found. The existence of the 6 phase (ZrCu4Al3)
was confirmed too and its crystal structure was proposed to be bcc. Moreover, a new ternary phase
Zr6Cu16Al7 designated in the present assessment as 10 not identified before was found, and its crystal
structure was described. The Zr6Cu16Al7 was predominant in the 20.7Zr-55.2Cu-24.1Al alloy annealed at
800°C for 98 h and was present in ZrCu2Al alloy annealed at 600°C for 48 h as a minor constituent. It should
be noted that a hydride compound of similar structure was observed to form at an interaction of ZrCu2Al
with hydrogen [1989Mey, 1990Mey1, 1990Mey2].
In the Al rich part of the ternary system [1997Soa, 1998Soa] observed the 7 and 8 phases detected earlier
but the 9 phase, which was reported to exist at 500°C by [1970Mar], was never observed by [1997Soa,
1998Soa]. Instead of 9 phase shown by [1970Mar] at the composition of 64Al-24Cu-12Zr (at.%) another
phase was found. The composition of this phase was determined to be 67.2Al-15.7Cu-17.1Zr [1998Soa].
Its crystal structure was found to be bcc. In the present assessment the preference is given to this new phase,
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which is designated as 9', because its composition was established by [1997Soa, 1998Soa] more exactly.
It was not observed in the alloys annealed at 800°C but was present in the alloys annealed at 700°C and
below.
A compound Zr3Cu2Al with cubic Ti2Ni type structure reported by [1964Rie] was not taken into account
in the present assessment because it is most likely stabilized by impurity elements.
The homogeneity ranges were found for the Laves phase 5 with a linear variation of lattice parameters and
for the 7 phase [1970Mar]. [1991Des2] reported that alloys on the base of Zr2CuAl5 were single phase for
the compositions Zr2CuAl5-x at 0.7 x 1 in the powders produced by mechanical alloying and heated to
750°C. The content of 9 at.% Cu in the 8 phase detected by [1997Soa] is within the composition range
indicated by [1991Des2].
An appreciable solubility of the third component with a linear variation of the lattice parameters up to 10.5
at.% Cu has been established for Zr4Al3 [1970Mar]. The Cu solubility in ZrAl3 was determined using SEM/
EDS technique to be 0.5 at.% at 800°C [1997Soa, 1998Soa] but [1991Des2] observed single ZrAl3 based
phase up to 2.5 at.% Cu. According to the results of SEM/EDS the presence of zirconium was not found in
the phase (CuAl2) [1998Soa]. The maximum solubility about 0.1 mass% Zr was found in the phase
(Cu3Al) at temperatures below 950°C in the section at 10 mass% Al using microscopic examination
[1964Pan].
A metastable phase of the Cu3Au type (L12) was obtained in mechanically alloyed Zr2CuxAl6-x (0 x 1)
powders for all concentrations x [1991Des2].
Data on the crystal structure of the solid phases relevant to the considered ranges of temperatures and
compositions are listed in Table 1.
Invariant Equilibria
The invariant reactions in the Al rich part of the ternary system were established by [1997Soa, 1998Soa]
from the results of DTA and microstructure analysis using SEM/EDS. They are: the U-type reaction
L+ 8 7+ZrAl3 at 820 ± 10°C; the P-type peritectic reaction of 9' formation L+ZrAl3+ 7 9' at
740 ± 10°C; the U-type reaction L+ZrAl3 (Al)+ 9'. The temperature of last reaction was not
experimentally determined but it can be suggested to be lower than 600°C, because the three alloys with the
Cu:Al ratio ~5 and 3.1, 6.0, 9.3 at.% Zr, which are located in a region of supposed invariant equilibrium,
were found to consist of ZrAl3+L. From the data of [1997Soa, 1998Soa] two more invariant reactions can
be supposed: L+ 7 9'+ at a possible temperature of 560 ± 10°C and L+ 9' (Al)+ at a temperature very
close to the temperature of the eutectic reaction L (Al)+ in the binary Al-Cu system (548.2°C). A tentative
reaction scheme for Al rich part of the phase diagram is shown in Fig. 1.
The results of the microscopic investigation of alloys in the sections at 5 and 10 mass% Al with 0 to
5 mass% Zr [1964Pan] suggest the possibility of an invariant equilibrium of eutectic type E, L +(Cu)+ 1
(with the ternary eutectic E, localized close to the binary Al-Cu eutectic e1), or type D, L +(Cu), 1 at the
temperature T1 (900°C < T1 < 965°C) (alloys were homogenized at 900°C, initial melting was observed at
965°C). Data by [1969Hor] and [1964Pan] suggest the occurrence of a U type transition reaction,
+ 1 (Cu)+ 1 at 568°C. Zr was found to increase the temperature of the eutectoid transformation
(Cu)+ 1, when compared with the binary Al-Cu alloys [1969Hor]. A tentative reaction scheme for this
part of the ternary system is proposed in Fig. 2.
The presence of four phases ( 4+ 5+ 6+ 10) in the 26.5Al-49Cu-24.5Zr alloy annealed at 600°C and
three-phase alloys ( 4+ 10+ 5, 4+ 10+ 6 and 4+ 5+ 6) in an area around the above alloy allows to
postulate the existence of appropriate four-phase invariant equilibrium. However, neither temperature nor
the type of this equilibrium are known.
Solidus Surface
Figure 3 shows a tentative projection of the solidus surface in the Al rich part of the ternary phase diagram
composed mainly from data by [1997Soa] and [1998Soa]. The primary feature of the phase equilibria in this
region is the existence of the phase fields ZrAl3+ + 9' and (Al)+ + 9' and the phase fields of ZrAl3+(Al)+
and ZrAl3+ + 9 by [1970Mar] and ZrAl3+(Al)+ and ZrAl3+ + 8 by [1967Zar]. The present version was
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preferred because [1998Soa] has given results of a microscopic investigation and a phase composition of
alloys in the (Al)+ + 9', which give evidence of the existence of 9' in alloys of this concentration. On the
contrary, [1967Zar] and [1970Mar] did not give any firm data on the alloys studied. However, it should be
noticed that the alloys studied by [1998Soa] were not in equilibrium and contained also some amount of
ZrAl3, which was not fully consumed in the transformation reaction L+ZrAl3 9'+(Al).
Isothermal Sections
The phase equilibria in the Al rich part region at 860°C are shown in Fig. 4 according to the data by
[1997Soa]. The composition of the 8 phase, with 9 at.% Zr instead of 12.5 accepted in literature (Table 1),
must be regarded as tentative.
Figure 5 shows the isothermal section at 800°C taking into account the appropriate section by [1970Mar]
adjusted to the binary phase diagrams accepted in this assessment, the data presented by [1997Soa] and
[1998Soa] for the Al rich corner and the existence of the 10 (Zr6Cu16Al7) phase reported by [1990Mey1].
The phase equilibria in a vicinity of 10 and 4 phases do require further additional studies. [1990Mey1]
reported that in the 24.1Al-55.2Cu-20.7Zr alloy, which was annealed at 800°C for 98 h, more than 98 % of
10 coexist with a minor amount of ZrCu2Al.
Figure 6 shows the L+ 7+ 9' phase field in the isothermal section at 700°C according to the data by
[1997Soa]. The L+ZrAl3+ 9' region shown is tentative.
The partial isothermal section at 600°C is presented in Fig. 7 and takes into account the data reported by
[1997Soa, 1998Soa], [1990Mey1] as well as [1970Mar] and [1964Pan]. [1990Mey1] reported the existence
of three-phase alloys 4+ 10+ 6, 4+ 6+ 5 and 4+ 10+ 5 in a vicinity of the 26.5Al-49Cu-24.5Zr
composition, which was found to be four-phase when annealed at 600°C for 48 h. This gives clear evidences
that the studied alloys were not reduced to equilibrium state. Moreover, a simultaneous existence of the
phase fields 4+ 10+ 5, 4+ 10+ 6 and 4+ 6+ 5 at 600°C is possible only if these fields are parts of the
plane of the invariant equilibrium 4+ 5+ 6+ 10 or if the 5 in the 4+ 5+ 10 field contains more than 40
at.% Cu, that never has been observed.
The partial isothermal section at 500°C (Fig. 8) is constructed from the data by [1970Mar], [1997Soa],
[1998Soa] and [1990Mey1]. The data by [1997Soa] agree with the phase equilibria constructed by
[1970Mar], except for the phase equilibria in the ZrAl3-Al- - 9' region. Here the findings of [1970Mar] and
[1998Soa] are contradicting.
The isothermal section at 400°C presented by [1967Zar] agrees with [1970Mar] as to the existence of the
(Al)+ +ZrAl3 equilibrium but [1967Zar] did not find the 9 phase reported by [1970Mar] nor did he find
the 9' phase reported by [1997Soa, 1998Soa].
The partial isothermal sections of the Cu corner of the ternary Al-Cu-Zr diagram (up to 10 mass% Al and 5
mass% Zr) at 850°C and 500°C proposed by [1964Pan] show satisfactory agreement with the results of
[1970Mar].
Temperature – Composition Sections
The vertical sections at 5 and 10 mass% Al up to 5 mass% Zr were constructed by [1964Pan]. The isopleth
at 5 mass% Al intersects the two-phase region (Cu)+intermetallic compound (probably 1). After the
primary crystallization of the (Cu) phase the eutectic (Cu)+ 1 solidifies at 965°C. The isopleth at constant
10 mass% Al demonstrates an increasing +(Cu)+ 1 region with a temperature decrease and eutectoid
decomposition of the phase. [1964Pan] could not determine a change of eutectoid temperature by
additions of Zr. However the results of [1969Hor] indicate a slight temperature increase and are preferred.
Figure 9 shows the partial vertical section at 10 mass% Al up to 5 mass% Zr (3.1 at.% Zr) constructed from
results of [1964Pan] but corrected according to the phase rule and assuming the existence of the univariant
equilibrium L+ 1 , which is concluded from the microstructures of the alloys given in [1964Pan].
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Thermodynamics
The partial and integral enthalpies of mixing of ternary Al-Cu-Zr alloys have been measured by [1998Wit].
The experimental data points of the enthalpy of mixing were treated by means of a least squares procedure
and the developed relationships were used to calculate the isolines of the integral enthalpy of mixing. The
minimal value was estimated to be -51.7 kJ·mol-1 close to the binary Al53Zr47 composition. The estimation
of the excess entropy of mixing of liquid ternary alloys on the basis of composition dependencies of the
measured enthalpies of mixing and the melting and boiling temperatures of pure components was applied
to the Al-Cu-Zr system. The liquid alloys near the binary composition Al53Zr47 were found to have large
negative values of the enthalpy of mixing and a large negative excess entropy. Therefore, the liquid alloys
in the vicinity of this composition were recognized to have the strongest chemical order.
[2001Aki] have derived analytical expressions for the free energy of mixing, enthalpy of mixing,
concentration fluctuations in the long wavelength limit and for the activity using the Flory approximation.
The derived expressions were used to obtain numerical results for the concentration dependence of these
thermodynamic values for the ternary liquid Cu0.33Zr0.67-Al alloys at 1772°C. The obtained results have
indicated that the chemical short range order exists for these liquid Al-Cu-Zr alloys, in quite good agreement
with available experimental data.
Enthalpies of formation of amorphous alloys (Zr0.65Cu0.35)1-x(Zr0.65Al0.35)x in the concentration range 0
x 0.8 from pure crystalline elements at 298 K measured by [1998Tur] can be represented by:
( fH298((Zr0.65Cu0.35)1-x(Zr0.65Al0.35)xam) = - 2964 - 31.915x (kJ·mol-1).
The absolute values of ( fH298((Zr0.65Cu0.35)1-x(Zr0.65Al0.35)xam) indicates strong chemical interaction
between Zr, Cu and Al atoms, which is rising with the increase of concentration of Al atom.
Notes on Materials Properties and Applications
The influence of the state of grain boundaries on superplastic flow has been established experimentally by
[1984Kai] for the Al-2Cu-0.16Zr (at.%) alloys. Different factors, which can have an influence on
superplastic flow have been studied, including the presence of disperse precipitates in the grain boundaries.
It was shown that Al solid solution supersaturated with Zr has been formed through quick crystallization of
the alloy. Precipitation of dispersed ZrAl3 particles occurred during annealing at 380°C. The anneal at
300°C for 48 h after preliminary cold deformation of 3 % resulted in a formation of CuAl2 particles, which
disappeared at superplastic deformation.
Relationships of pore formation and failure of a superplastic Al-4.1Cu-0.5Zr (mass%) alloy have been
studied by [1990Poy] during creep at a constant flow stress. The most pronounced superplastic properties
were shown at 500°C. The optimum conditions of superplasticity development were obtained to be = 5.0
MPa, = 1.5·10-4s-1 in the studied interval of the stress = 3.0 to 6.0 MPa. In this case the maximum
elongation of the samples before the failure was 830 %.
Magnetic susceptibility measurements carried out for the Laves phase ZrCu1.2Al0.8 showed a Curie-Weiss
behavior of this alloy with the effective moment of 1.5 B.
A bulk intermetallic L12 compound was produced by means of the spark plasma sintering (SPS)
nanocrystalline powders of (Al+12.5 at.% Cu)3Zr and 65.6Al-9.4Cu-25Zr (at.%), which were prepared be
planetary ball milling. The highest density, the smallest grain size (20-300 nm) and the highest micro
hardness (989.5 Hv) was achieved with those samples prepared by SPS at 600°C [2002Moo].
Miscellaneous
The temperature of L12 D03 transformation of metastable phases in the mechanically alloyed Zr2CuxAl6-x
(0 < x < 1) was found to increase with increasing Cu content from 500 to 550°C in the studied
concentration interval, but the L12 structure of Zr2CuAl5 (x = 1) is stable at least up to 1300°C [1991Des1,
1992Des2]. The lattice parameter of metastable L12 phase decreases linearly with increasing Cu content
from 409.3 pm for ZrAl3(L12) (x = 0) to 405.8 pm at x = 1 is approximately constant after heating to 750°C
and are close to those of ZrAl3 annealed at 440°C, i.e. 407 pm [1991Des1] (a = 407.2 pm for
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Al-12.5Cu-25Zr (at.%) [1991Des2]. It was noted that hexane, was used as a surfactant by mechanical
alloying, gave rise to the formation of very fine dispersed carbides in the alloy [1991Des2].
Amorphous Al-Cu-Zr alloys were produced by melt spinning over wide composition range [1991Ino]. The
Al-Cu-Zr alloys were concluded to have a large glass-forming capacity. The high thermal stability of the
supercooled liquid was observed in the vicinity of the AlCuZr3 composition. Tg/Tm was measured to be
0.61.
The glass transition temperature Tg in the metallic glass Zr65Cu27.5Al7.5 was measured to be 350°C
[1997Sch]. Above Tg in the undercooled liquid region, a shift in the short range order was observed towards
the short range order of crystalline Zr2Cu. This change was found to be irreversible.
[1997Kan] reported a temperature variation of the specific heat of Zr65Cu27.5Al7.5 at temperatures around
Tg, Tg, Tx, (the temperatures of the initial stage of glass transition and crystallization, respectively) and Tm
were found to be 387, 447 and 475°C, respectively.
The lattice parameter variation with temperature determined for ZrCu1.2Al0.8 by [1992Sle] is shown in
Fig. 10.
Precipitation of metastable phases have been observed by [1974Bus] in Cu rich alloys with up to 7 mass%
Al and 0.525 mass% Zr quenched from 970°C and aged at 800°C. These phases were identified as ( Zr)
(a = 372 ± 1 pm) and (Zr) (a = 318 ± 1 pm), what is rather surprising for an alloy of a such composition.
The crystal structure of particles, which have been precipitated during aging at temperatures above 800°C,
has not be determined, yet. It is worth noting that [1974Bus] considered “ZrCu3” to be possibly a stable
phase with unknown crystal structure.
[1991Kan] observed partially coherent ' precipitates on ZrAl3 dispersoids in Al-4Cu-0.18Zr (mass%)
alloy. The precipitation behavior of the ' phase is different in the recrystallized and recovered condition.
References
[1931Pre] Preston, G.D., “An X-ray Investigation of some Copper-Aluminium Alloys”, Philos. Mag.,
12, 980-993 (1931) (Crys. Structure, Experimental, 11)
[1962Poe] Poetschke, M., Schubert, K., “The Structure of some Systems Homologous and
Quasihomologous to T4-B3. II. The Binary Systems of Al with Ti, Hf, Zr and Mo”
(in German), Z. Metallkd., 53, 548-561 (1962) (Crys. Structure, Experimental, 45)
[1964Pan] Panseri, C., Leoni, M., “Studies on Complex Al Bronze. II. Ternary Equilibrium Diagram
Cu-Al-Zr” (in Italian), Allumino, 33, 63-70 (1964) (Equi. Diagram, Experimental, *, 5)
[1964Rie] Rieger, W., Nowotny, H., Benesovsky, F., “Structural Studies in the Systems with
Transition Elements (Cu, Ag) and (Al, Ga)” (in German), Monatsh. Chem., 95, 1573-1576
(1964) (Crys. Structure, Experimental, 7)
[1964Sch] Schubert, K., Raman, A., Rossteutscher, W., “Some Structural Data of Metallic Phases”
(in German), Naturwissenschaften, 51, 506-507 (1964) (Crys. Structure, Experimental, 0)
[1965Ram] Raman, A., Schubert, K., “On the Crystal Structure of Some Alloy Phases Related to TiAl3.
III. Investigations in Several T-Ni-Al and T-Cu-Al Systems” (in German), Z. Metallkd., 56,
99-104 (1965) (Crys. Structure, Experimental, 14)
[1966Mar] Markiv, V.Ya., Kripyakevich, P.I., “Compounds of the Type R(X’X’’)2 in Systems with R
= Ti, Zr, Hf, X’ = Fe, Co, Ni, Cu, and X’’ = Al, Ga and Their Crystal Structures”, Sov. Phys.
Crystallogr., 11, 733-738 (1967), translated from Kristallografiya, 11, 859-865 (1966)
(Crys. Structure, Experimental, 25)
[1967Hof] Hofer, G., Stadelmaier, H.H., “Co, Ni and Cu-Phases of the Ternary MnCu2Al Type”
(in German), Monatsh. Chem., 98, 408-411 (1967) (Crys. Structure, Experimental, 9)
[1967Zar] Zarechnyuk, O.S., Malinkovich, A.N., Lalayan, E.A., Markiv, V.Ya., “X-Ray Diffraction
Study of Al-Rich Alloys of the Ternary Al-Cu-Cr, Al-Cu-Zr and Al-Cr-Zr Systems and the
Quaternary Al-Cu-Cr-Zr System”, Russ. Metall., (6), 105-107 (1967), translated from Izv.
Akad. Nauk SSSR, Met., (6) 201-204 (1967) (Equi. Diagram, Experimental, *, 2)
[1969Hor] Hori, M., “On the Effects of Fe and Zr on the Eutectoid Transformation of Cu-Al Binary
Alloys” (in Japanese), J. Japan Inst. Metals, 33, 1067-1072 (1969) (Experimental, 23)
212
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[1969Tes] Teslyuk, M.Yu., Intermetallic Compounds with Structure of Laves Phases, Nauka,
Moscow, 1-138 (1969) (in Russian) (Crys. Structure, Experimental, Review, 312).
[1970Mar] Markiv, V.Ya., Burnashova, V.V., “Investigation of the Zr-Cr-Al and Zr-Cu-Al Systems”
(in Russian), Poroshk. Metall, (12), 53-58 (1970) (Crys. Structure, Equi. Diagram,
Experimental, *, 14)
[1974Bus] Bushnev, L.S., Payuk, V.A., Korokayev, A.D., “The Ageing of Copper-Zirconium and
Copper-Aluminium-Zirconium Alloys”, Phys. Met. Metallogr., 37, 111-116 (1975),
translated from Fiz. Met. Metalloved., 37, 573-579 (1974) (Experimental, 9)
[1979Dri] Drits, M.E., Bochvar, N.R., Guzei, L.S., Lysova, E.V., Padezhnova, E.M., Rokhlin, L.L.,
Turkina, N.I., “Cu-Al-Zr” (in Russian), Binary and Multicomponent Copper-Base Systems.
Nauka Moskow, 85-86 (1979) (Equi. Diagram, Review, #, 2)
[1981Kin] King, H.W., “Crystal Structures of Elements at 25°C”, Bull. Alloy Phase Diagrams, 2,
401-402 (1981) (Crys. Structure, Review, 5)
[1984Kai] Kaibyshev, O.A., Valiev, R.Z., Tsenev, N.K., “Influence of the State of Grain Boundaries
on Superplastic Flow”, Sov. Phys.- Dokl. (Engl. Transl.), 29, 752-754 (1984), translated
from Dokl. Akad. Nauk SSSR, 278, 93-97 (1984) (Experimental, 12)
[1985Mur] Murray, J.L., “The Aluminium-Copper System”, Int. Met. Rev., 30, 211-233 (1985) (Equi.
Diagram, Crys. Structure, Review, 230)
[1986Kne] Kneller, E., Khan, Y., Gorres, M., “The Alloy System Copper - Zirconium. Part I, Phase
Diagram and Structural Relations”, Z. Metallkd., 77, 43-48 (1986) (Crys. Structure, Equi.
Diagram, Experimental, 26)
[1986Riv] Rivlin, V.G., Miodownik, A.P., “A Provisional Assessment of the Literature Relevant to
AlCuZr Alloys”, Progr. Report 7, University of Surrey, 1-34 (1986) (Crys. Structure, Equi.
Diagram, Review, #, 43)
[1989Mey] Meyer zu Reckendorf, R., Schmidt, P.C., Weiss, A., “Reaction of Hydrogen with the
Heusler-Type Phases Cu2TiAl and Cu2ZrAl”, Z. Physik. Chemie, Neue Folge, 163, 103-108
(1989) (Crys. Structure, Experimental, 13)
[1990Kum] Kumar, K.S., “Ternary Intermetallics in Aluminium - Refractory Metal - X Systems (X=V,
Cr, Mn, Fe, Co, Ni, Cu, Zn)”, Int. Mater. Rev., 35, 293-327 (1990) (Equi. Diagram, Review,
#, 158)
[1990Mey1] Meyer zu Reckendorf, R., Schmidt, P.C., Weiss, A., “The Ternary Systems Cu-Ti-Al and
Cu-Zr-Al Around the Heusler Phase Composition Cu2XAl (X = Ti, Zr): Phase Diagrams
and Hydrogen Solubility”, J. Less-Common Met., 159, 277-289 (1990) (Crys. Structure,
Equi. Diagram, Experimental, *, 41)
[1990Mey2] Meyer zu Reckendorf, R., Schmidt, P.C., Weiss, A., “Hydrogen-Supported Formation of G
Phase Cu16Zr6Al7 in the Ternary System Copper - Zirconium - Aluminum”,
J. Less-Common Met., 159, 291-298 (1990) (Crys. Structure, Experimental, 14)
[1990Poy] Poyda, V.P., Kuznetsova, R.I., Tsenev, H.K., Sukhova, T.F., Pismennaya, A.N., “Evolution
of Porosity and Failure of the Al-4.1 mass% Cu-0.5 mass% Zr in Conditions of Superplastic
Flow” (in Russian), Metallofizika, 12, 44-79 (1990) (Experimental, 21)
[1991Des1] Desch, P.B., Schwarz, R.B., Nash, P., “Formation of Metastable L12 Phases in Al3Zr and
Al-12.5 % X-25 % Zr (X = Li, Cr, Fe, Ni, Cu)”, J. Less-Common Met., 168, 69-80 (1991)
(Crys. Structure, Experimental, 25)
[1991Des2] Desch, P.B., Schwarz, R.B., Nash, P., “Phase Stability in the Al6-xCuxZr2 System for
0<x<1”, Mater. Res. Soc. Symp. Proc., 186, 439-444 (1991) (Crys. Structure, Experimental,
*, 21)
[1991Ino] Inoue, A., Zhang, T., Masumoto T., “New Amorphous Alloys with Significant Supercooled
Liquid Region and Large Reduced Glass Transition Temperature”, Mater. Sci. Eng. A,
A134, 1125-1128 (1991) (Experimental, 8)
[1991Kan] Kanno, M., Ou, B.-L., “Heterogeneous Precipitation of Intermediate Phases on Al3Zr
Particles in Al-Cu-Zr and Al-Li-Cu-Zr Alloys”, Mat. Trans., JIM, 32, 445-450 (1991),
translated from J. Jpn. Inst. Light Met., 40, 672-677 (1990) (Experimental, 13)
213
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
[1992Sle] Slebarski, A., Hafez, M., Zarek, W., “Spin Fluctuations in ZrM1.2Al0.8 with Transition
Metal M of the 3d Type”, Solid State Commun., 82, 59-61 (1992) (Crys. Structure,
Experimental, 12)
[1992Tre] Tretyachenko, L.A., “Aluminium - Copper - Zirconium”, MSIT Ternary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 10.18961.1.20, (1992) (Crys. Structure, Equi.
Diagram, Assessment, #, 15)
[1993Oka] Okamoto, H., “Al-Zr (Aluminium - Zirconium)”, J. Phase Equilib., 14, 259-260 (Equi.
Diagram, Review, *, 2)
[1994Ari] Arias, D., Abriata, J.P., “Cu-Zr (Copper - Zirconium)”, in “Phase Diagrams of Binary
Copper Alloys”, Subramanian, P.R., Chakrabarty, D.J., Laughlin. D.E. (Eds.), ASM
Materials Park, OH, 497-502 (1994) (Crys. Structure, Equi. Diagram, Review,
Themodyn., 50)
[1994Zen] Zeng, K.-J., Haemaelaeinen, M., “A New Thermodynamic Description of the Cu-Zr
System”, J. Phase Equilib., 15, 577-586 (Equi. Diagram, Review, Thermodyn., 55)
[1997Kan] Kanomata, T., Sato, Y., Sugawara, Y., Aburatani, S., Kimura, H., Kaneko, T., Inoue, A.,
Masumoto, T., “Heat Capacity of Pd-Si, Ni-Si-B and Zr-Based Metallic Glasses”, Sci. Rep.
Res. Inst., Tohoku Univ., Ser. A, A43(2), 89-95 (1997) (Experimental, Thermodyn., 13)
[1997Sch] Schumacher, H., Oelgeschlaeger, D., Traverse, A., Samwer, K., “Structural Changes of the
Metallic Glass in the Undercooled Liquid Region”, J. Appl. Phys., 82, 155-162 (1997)
(Experimental, 34)
[1997Soa] Soares, D., Castro, F., “Study of Phase Equilibria in the Al-Cu-Zr System at the Al-Rich
Part”, J. Chim. Phys., 94, 958-963 (1997) (Crys. Structure, Equi. Diagram, Experimental,
*, 5)
[1998Bra] Braha, M.H., Malheiros, L.F., Castro, F., Soares, D., “Experimental Liquidus Points and
Invariant Reactions in the Cu-Zr System”, Z. Metallkd., 89, 341-345 (1998) (Equi. Diagram,
Experimental, #, 31)
[1998Don] Dong, C., Zhang, Q.H., Wang, D.H., Wang, Y.M., “Al-Cu Approximants in the Al3Cu4
Alloy”, Eur. Phys. J. B, B6, 25-32 (1998) (Crys. Structure, Experimental, 16)
[1998Soa] Soares. D.F., de Castro, F.P., “Study of the Effect of Zirconium Addition to the Al-Rich
Alloys of the Al-Cu and Al-Cu-Mg Systems”, Ber. Bunsen-Ges. Phys. Chem., 102,
1181-1184 (1998) (Crys. Structure, Equi. Diagram, Experimental, *, 6)
[1998Tur] Turchanin, A.A., Tomilin, I.A., “Experimental Investigations of the Enthalpies of
Formation of Zr-Based Metallic Amorphous Binary and Ternary Alloys”, Ber. Bunsen-Ges.
Phys. Chem., 102, 1252-1258 (1998) (Experimental, Thermodyn., 29)
[1998Wit] Witusiewicz, V., Stolz, U.K., Arpshofen, I., Sommer, F., “Thermodynamic of Liquid
Al-Cu-Zr Alloys”, Z. Metallkd., 89, 704-713 (1998) (Experimental, Thermodyn., 16)
[2000Don] Dong, C., Zhang, Q.-H., Wang, D.-H., Wang, Y.-M., “Al-Cu Approximants and Associated
B2 Chemical-Twinning Modes”, Micron, 31, 507-514 (2000) (Crys. Structure,
Experimental, 21)
[2001Aki] Akinlade, O., Sommer, F., “Concentration Fluctuations and Thermodynamic Properties of
Ternary Liquid Alloys”, J. Alloys Compd., 316, 226-235 (2001) (Theory, Thermodyn., 27)
[2002Gul] Gulay, L.D, Harbrecht, B., “The Crystal Structures of the 1 and 2 Phases in the Al-Cu
System”, Abstr. VIII Int. Conf. ”Crystal Chemistry of Intermetallic Compounds”,
September 2002, Lviv, P139, 73 (2002) (Crys. Structure, Experimental, 5)
[2002Moo] Moon, K.I., Kim, S.Ch., Lee, K.S., “A Study on the Microstructure of D023 Al3Zr and L12
(Al+12.5at.%Cu)3Zr Intermetallic Compounds Synthesized by PBM and SPS”,
Intermetallics, 10, 185-194 (2002) (Crys. Structure, Experimental, 20)
[2003Gro] Gröbner, J., “Al-Cu (Aluminium-Copper)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 68)
214
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
[2003Sem] Semenova, E., Sidorko., V., “Cu-Zr (Copper-Zirconium)”, MSIT Binary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys.
Structure, 31)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
(Al)
< 660.42
cF4
Fm3m
Cu
a = 404.96 at 25°C [1981Kin]
Cu solubility 0 to 2.48 at.% [Mas2]
Zr solubility 0 to 0.08 at.% [1993Oka]
(Cu)
< 1084.87
cF4
Fm3m
Cu
a = 361.49 at 25°C [1981Kin]
Al solubility 0 to 19.7 at.% [2003Gro]
Zr solubility 0 to 0.12 at.% [1994Ari,
2003Sem]
( Zr)(h)
1855-863
cI2
Im3m
W
a = 360.90 [Mas2]
Cu solubility 0 to 5.7 at.% [1994Ari,
2003Sem]
Al solubility 0 to 25.9 at.% [1993Oka]
( Zr)(r)
< 863
hP2
P63/mmc
Mg
a = 329.17
c = 514.76
at 25°C [1981Kin]
Cu solubility 0 to 0.2 at.% [1994Ari,
2003Sem]
Al solubility 0 to 8.3 at.% [1993Oka]
, CuAl2< 591
tI12
14/mcm
CuAl2
a = 606.7
c = 487.7
31.9 to 33 at.% Cu [2003Gro]
[V-C2, 2003Gro]
1, CuAl(h)
624-560
o*32
a = 408.7
b = 1200c = 863.5
49.8 o 52.4 at.% Cu [2003Gro]
[V-C, 2003Gro]
2, CuAl(r)
< 563
mC20
C2/m
CuAl(r)
a = 1206.6
b = 410.5
c = 691.3
= 55.04°
49.8 to 52.4 at.% Cu
[V-C2, 1985Mur]Pearson symbol: [1931Pre]
1(h1)
958-848
cubic ? 59.4 to 62.1 at.% Cu [2003Gro]
2(h2)
850-560
hP6
P63/mmc
Ni2In
a = 414.6
c = 506.3
55.0 to 61.1 at.% Cu [2003Gro]
[V-C2, 2003Gro]
215
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
1(h), Cu47.8Al35.5(h)
590-530
hP42
oF*
oF88-4.7
Fmm2
Cu47.8Al35.5
a = 810
c = 1000 (or 1237)
a = 816
b = 1414
c = 999
a = 812.67 ± 0.03
b = 1419.85 ± 0.05
c = 999.28 ± 0.03
55.2 to 56.9 at.% Cu [Mas2]
Cu56.8Al43.2 in the Al43Cu57 sample
annealed at 500°C for 10 h [1998Don,
2000Don]
for Cu47.8Al35.5 (57.5Cu-42.5Al)
annealed at 550°C for 240 h
(single-phase sample) [2002Gul]
2(r) Cu11.5Al9(r)
< 570
m*21
oI*
oI24-3.5
Imm2
Cu11.5Al9.0
a = 707
b = 408
c = 1002
= 90.63°
a = 408
b = 707
c = 999
a = 409.72
b = 703.13
c = 997.93
55.2 to 56.3 at.% Cu [Mas2]
[V-C]
Cu58.7Al41.3 in the Al43Cu57 sample
annealed at 500°C for 10 h [1998Don,
2000Don]
for Cu11.5Al9.0 (56.8Cu-43.2Al)
annealed at 550°C for 240 h (single
phase sample) [2002Gul]
Cu1-xAlx< 686
hR*
R3m
a = 1226
c = 1511
[V-C2, 2003Gro] for Cu61.1Al38.9
59.3 to 61.1 at.% Cu [Mas2, 2003Gro]
0Cu~2Al
1037-800
cI52
I43m
Cu5Zn8
59.8 to 69 at.% Cu [2003Gro]
1
890
cP52
P43m
Cu9Al4
a = 870.23
62.5 to 69 at.% Cu [2003Gro]
[V-C2]
CuAl(h)
1049-559
cI12
Im3m
W
a = 295.64
70.9 to 82.0 at.% Cu [2003Gro]
at 672°C in +(Cu) alloy [V-C2,
2003Gro]
ZrAl3< 1580
tI16
I4mmm
ZrAl3
a = 401.4
c = 1732
[1993Oka, V-C2]
Cu solubility < 0.5 at.% in homogeneity
range at 750°C [1997Soa, 1998Soa];
Zr2CuxM6-x at 0 x 0.9 [1991Des2]
ZrAl2< 1660
hP12
P63/mmc
MgZn2
a = 528.24
c = 874.82
[1993Oka, V-C2]
Zr2Al3< 1590
oF40
Fdd2
Zr2Al3
a = 960.1
b = 1390.6
c = 557.4
[1993Oka, V-C2]
ZrAl
< 1275
oC8
Cmcm
CrB
a = 335.9
b = 1088.7
c = 427.4
[1993Oka, 1962Poe]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
216
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
Zr4Al3-xCux
Zr4Al3 1030
hP7
P6
Zr4Al3
a = 543 to 537a
c = 539a
a = 543.4
c = 539.0
0 x 0.735 [1970Mar]
[1993Oka, V-C2]
Zr3Al2< 1480
tP20
P42/mnm
Zr3Al2
a = 763
c = 699.8
[1993Oka, V-C2]
Zr2Al
< 1215
hP6
P63/mmc
Ni2In
a = 489.39
c = 592.83
[1993Oka, Mas2, V-C2]
Zr3Al
< 1019
cP4
Pm3m
Cu3Au
a = 437.2 [1993Oka, V-C2]
Zr2Cu
< 950
tP150 a = 1592.4
c = 1132.8
[2003Sem, 1986Kne, 1998Bra]
ZrCu
960-725
cP2
Pm3m
CsCl
a = 325.87 [1998Bra, 2003Sem]
Zr7Cu10
< 935
oC68
C2ca
Zr7Ni10
a = 1267.29
b = 931.63
c = 934.66
[2003Sem, 1998Bra]
Zr3Cu8(h)
1028- 600
oP44
Pnma
Hf3Cu8
a = 786.93
b = 815.47
c = 998.48
[2003Sem, V-C2]
[1986Kne, 1998Bra]
Zr14Cu51
< 1112
hP68
P6/m
Gd14Ag51
a = 1124.44
b = 828.15
[2003Sem, V-C2]
ZrCu5
< 1032
cF24
F43m
AuBe5
a = 687 [1986Kne, 1994Zen, 1998Bra,
2003Sem]
* 1 unknown 14Al-71Cu-15Zr [1970Mar]
* 2 unknown 13Al-14Cu-73Zr [1970Mar]
* 3 unknown 21Al-28Cu-51Zr [1970Mar]
* 4, ZrCu2Al oF16
MnCu2Al
a = 621.5 ± 0.3
a = 619
a = 622
a = 621.63 ± 0.03
[1970Mar]
[1964Sch, 1965Ram]
[1967Hof]
[1989Mey, 1990Mey1, 1990Mey2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
217
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
a as scaled from diagram
* 5, ZrCuxAl2-x cF24
Fd3m
MgCu2
a = 730.8 to 744.0
a = 740
a = 739.7
a = 738.1
a = 739.1 ± 0.3
a = 738.83
0.95 x 0.36 at 800°C
[1966Mar, 1969Tes, 1970Mar]
for ZrCuAl [1964Sch]
in as cast alloy Zr25Cu25Al50
[1965Ram]
in the ZrCu2Al alloy annealed at 600°C
[1990Mey1, 1990Mey2]
the phase present in ZrCu2Al at 600°C
(2 %) [1989Mey]
for ZrCu1.2Al0.8 (Zr35.3Cu40Al26.7)
annealed at 1000 K for 7 d [1992Sle]
* 6, ZrCu4Al3cI* a = 1730.0
37Al-51Cu-12Zr [1970Mar]
37Al-51Cu-12Zr [1970Mar]
* 7 tI26
I4/mmm
ThMn12
a = 512 to 490
c = 850 to 856
(50-41)Al-(42.3-51.3)Cu-7.7Zr
(ZrCu5.50-6.70Al6.50-5.90) at 800°C
[1970Mar]
* 8, Zr2CuAl5 cP4
Pm3m
Cu3Au
a = 402
a = 404
62.5Al-12.5Cu-25Zr [1970Mar]
[1964Sch, 1965Ram]
(62.5-66.25)Al-(12.5-8.75)Cu-25Zr
at 750°C [1991Des2]
* 9
< 740
tI*. a = 579
c = 396
for 67.2Al-15.7Cu-17.1Zr [1998Soa]
* 10, Zr6Cu16Al7 cF116
Mg6Cu16Si7
a = 1194.1 ± 0.03
a = 1192.5
a = 1193.3
the phase present in ZrCu2Al annealed
at 600°C (3 %) [1989Mey]
in the ZrCu2Al alloy annealed at 600°C
for 48 h [1990Mey1, 1990Mey2]
in the 20.7Zr-55.2Cu-24.1Al alloy
( 10+ 4) annealed at 800°C for 98 h
[1990Mey1]
Zr2CuxAl6-x cP4
Pm3m
Cu3Au
a = 409.5 to
405.5
0 x 1; metastable phase in a
mechanically alloyed powders
[1991Des2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
218
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
Fig. 1: Al-Cu-Zr. Tentative partial reaction scheme in the Al-rich corner
Al-Zr Al-Cu-Zr
L + τ8
ZrAl3 + τ
7820±10 U
1
ZrAl3 + τ
8 + τ
7
Al-Cu
L + ZrAl3
(Al)
660.8 p
L + ZrAl3
+ τ7
τ9'740±10 P
L + ZrAl3
(Al) + τ9'T
1<600 U
2
L + τ7
θ + τ9'560±10? U
3
L + τ9' (Al) + θ560>T
2>T
eU4
L (Al) + θ548.2 e
ZrAl3 + τ
8 + L τ
7+ τ
8 + L
L + ZrAl3 + τ
7
ZrAl3 + τ
9'+ L
τ7
+ τ9' + L
τ9'+ θ + L
(Al) + θ + L
ZrAl3
+ τ7 + τ
9'
ZrAl3
+ τ9' + (Al) τ
7+ θ + L
τ7 + τ
9' +θ
τ9' + (Al) + θ
Fig. 2: Al-Cu-Zr. Tentative partial reaction scheme near the Al-Cu side for the Cu-rich part
l β + (Cu)
1032 e1
L β + (Cu) + τ1
900<T1<965 E
β (Cu) + γ1
559 e2
β + τ1
(Cu) + γ1
568 U
L + τ1 + β L + (Cu) + τ
1
β + (Cu) + τ1 β + τ
1 + γ
1
(Cu) + γ1
+ τ1
Al-Cu Al-Cu-Zr Al-Zr
219
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
10
20
30
40
50
10 20 30 40 50
50
60
70
80
90
Zr 60.00Cu 0.00Al 40.00
Zr 0.00Cu 60.00Al 40.00
Al Data / Grid: at.%
Axes: at.%
Zr2Al3
Zr5Al4
τ8
ZrAl2
ZrAl3
(Al)
ε2
η1
θ
τ7
τ5
τ9´
560820
740
10
20
30
40
50
10 20 30 40 50
50
60
70
80
90
Zr 60.00Cu 0.00Al 40.00
Zr 0.00Cu 60.00Al 40.00
Data / Grid: at.%
Axes: at.%
ZrAl2
ZrAl3
Zr2Al3
Zr4Al3
τ5 τ
7
τ8 L
Al
Fig. 3: Al-Cu-Zr.
Ternatative solidus
projection for the
Al-rich part
Fig. 4: Al-Cu-Zr.
Partial isothermal
section at 860°C for
the Al-rich part
220
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
10
20
30
40
50
10 20 30 40 50
50
60
70
80
90
Zr 60.00Cu 0.00Al 40.00
Zr 0.00Cu 60.00Al 40.00
Data / Grid: at.%
Axes: at.%
Zr2Al3
ZrAl
τ8
ZrAl2
ZrAl3
L
Zr4Al3ε
2
τ7
τ5
τ9´
Al
20
40
60
80
20 40 60 80
20
40
60
80
Zr Cu
Al Data / Grid: at.%
Axes: at.%
(Cu)
γ1
ε2
L
ZrAl3
ZrAl2
Zr2Al3
ZrAl
Zr4Al3
Zr3Al2
Zr2Al
Zr3Al
(αZr)
Zr2CuZrCu
Zr7Cu10
Zr3Cu8 Zr14Cu51
ZrCu5
τ1
τ2
τ3 τ4
τ5
τ6
τ7
τ8
β
γ0τ10
Fig. 6: Al-Cu-Zr.
Partial isothermal
section at 700°C for
the Al-rich part
Fig. 5: Al-Cu-Zr.
Isothermal section at
800°C
221
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
20
40
60
80
20 40 60 80
20
40
60
80
Zr Cu
Al Data / Grid: at.%
Axes: at.%(Al)
ZrAl3
ZrAl2Zr2Al3
(Cu)
τ1
τ4
γ1
δ
ε2
η1τ
5
τ6
τ7
τ9´
τ8
Zr14Cu51 ZrCu5
τ10
L
β
20
40
60
80
20 40 60 80
20
40
60
80
Zr Cu
Al Data / Grid: at.%
Axes: at.%(Al)
ZrAl3
ZrAl2Zr2Al3
(Cu)
τ1
τ4
γ1
δ
ζ2
η2
θ
τ5
τ6
τ7
τ9´
τ8
Zr7Cu10Zr14Cu51 ZrCu5
τ10
Fig. 8: Al-Cu-Zr.
Partial isothermal
section at 500°C
Fig. 7: Al-Cu-Zr.
Partial isothermal
section at 600°C
222
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Cu–Zr
400
500
600
700
800
900
1000
1100
Zr 3.10Cu 75.90Al 21.00
Zr 0.00Cu 79.30Al 20.70Cu, at.%
Tem
pera
ture
, °C
(Cu)+γ1(Cu)+τ1+γ1
β+(Cu)+γ1568
β+(Cu)β+(Cu)+τ1
β+τ1
β
β+LLL+τ1
L+β+τ1
7976 77 78
Fig. 9: Al-Cu-Zr.
Polythermal section
for 10 mass% Al
Temperature, K
Latticeparameter,pm
0735
50 100 150 200 250 300
736
737
738
739Fig. 10: Al-Cu-Zr.
The lattice parameter
a of ZrCu1.2Al0.8 vs
temperature
[1992Sle]
223
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Fe
Aluminum – Dysprosium – Iron
Riccardo Ferro, Paola Riani, Laura Arrighi
Literature Data
This evaluation is part of the MSIT Ternary Evaluation Program and incorporates and continues the critical
evaluation made by [1991Gri] considering a fast amount of new published data. However the Al-Dy-Fe
system has been investigated only up to 33.3 at.% Dy and most experimental work deals with magnetic
properties measurements and crystal structure determination, either by X-ray or neutron diffraction.
At 500°C a partial isothermal section has been determined by [1973Viv] in the above mentioned region, by
means of X-ray diffraction and microscopy, and by [2001Yan] at the Dy2(Fe,Al)17 composition at the same
temperature. In the [1973Viv] section no indication was given about the phase based on Dy6Fe23 and on the
solubility range of DyFe3. The phase 3 moreover was presented as a point phase (DyFe1.2Al0.8). The
section RFe2-RAl2 was studied at 800°C by [1975Dwi] and by [1998Psz]. [1977Oes] studied the solid
solution phases based on DyFe3, Dy6Fe23 and Dy2Fe17. The alloys were prepared either by induction
melting only or by melting and annealing (Dy6Fe23 200 h at 1000°C).
Binary Systems
The binary phase equilibria in the Al-Fe system are accepted in this evaluation as described by [2003Pis],
who based his evaluation on the assessment of [1993Kat] and incorporated in the Fe-rich region the ordering
equilibria between the ( Fe), FeAl and Fe3Al solid solutions which have been recently investigated by
[2001Ike].
The Dy-Fe and Al-Dy systems are accepted as reported by [1993Oka] and [2002Gry], respectively.
Solid Phases
Crystal structure data are reported in Table 1.
The binary Laves phases DyAl2 and DyFe2 are isostructural both to the MgCu2 type; DyAl2 dissolves about
26 at.% Fe at 800°C ([1975Dwi]) or 20 at.% Fe [1998Psz] (after melting and cooling down); DyFe2
dissolves at 800°C about 22.7 at.% Al [1975Dwi]. At intermediate compositions, however, a different
Laves phase ( 3, MgZn2 type) is formed [1962Wer, 1971Oes, 1972Oes, 1973Oes, 1973Viv, 1973Zar,
1974Oes, 1975Dwi, 1976Gro, 1998Psz].
According to [2001Yan], Dy2Fe17 (Th2Ni17 type) too presents large Al solubility and at increasing Al
contents it transforms into the related structures TbCu7 and Th2Zn17 type, respectively. The hexagonal
Th2Ni17 and TbCu7 type structures dominate at, or below, the theoretical molar ratio Dy/(Fe+Al) = 2:17
(10.5±9.5 at.% Dy) while the rhombohedral Th2Zn17 type structure dominates at higher Dy content
( 11.5 at.%). In the same composition range X-ray diffraction investigations have been performed also by
[1977Oes] and [1999Hao] (see Table1). According to [1996Mao] the TbCu7 type structure is also present
as a DyFe7 metastable phase in the Dy-Fe binary system.
At even higher Al content another ternary phase, with a larger Dy/(Fe,Al) ratio, is formed ( 4, ThMn12 type)
studied by [1973Viv, 1974Viv, 1976Bus, 1988Sch, 1988Won, 2000Pai] at the composition DyFe4Al8, and
by [1980Fel, 1981Fel, 1988Che] at DyFe6Al6. The ThMn12 type structure of R(Fe1-xAlx)12 compounds and
the preferential site occupancies of Fe and Al in 8f and 8i position respectively have been studied by
[2001Sch] for several rare earth metals (R). It was observed that higher Fe concentrations obtained by
substitution of Al by Fe (RFe4Al8 → RFe5Al7 → RFe6Al6 → RFe7Al5) lead to a gradual decrease of the
lattice parameters. In the case of Ho and Er the structures of RFe7Al5 were clearly observed, in the case of
Dy (and Tb) their formation is questionable (probably due to limits related to the atomic dimension of R).
Finally, with the same Dy/(Fe,Al) ratio, another ternary phase ( 5, at the composition DyFe2Al10) was
studied by [1973Viv, 1998Thi, 2000Ree].
224
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Al–Dy–Fe
The phase based on the binary DyFe3 dissolves Al, in the PuNi3 type form, up to about 5 at.% (alloys
prepared by induction melting only) [1977Oes]. A higher solubility (see Table 1) was observed in the CeNi3modification (up to -33 at.% Al); however this solution can be considered as a ternary phase stable at higher
temperature.
The binary Dy6Fe23 phase dissolves up to 20 at.% Al at 1000°C [1977Oes].
Isothermal Sections
A “quasi” isothermal section of the system is proposed in Fig. 1. Notice however that it has been built
assembling various parts investigated at different temperatures. The region from 0 to 18 at.% Dy may be
considered determined at 500°C [1973Viv, 2001Yan]. In the region between 20 and 30 at.% Dy only data
probably relevant to higher temperature are available in literature [1977Oes] and have been included.
Finally in the region around 33 at.% Dy the data obtained at 800°C by [1975Dwi] have been included.
Notes on Materials Properties and Applications
Mössbauer measurements on the 3 Dy(Fe1-xAlx)2 phase have been carried out by [1998Psz] and, at the
DyFeAl composition, by [1975Dwi, 1976Gro].
Magnetic properties of 3 Dy(Fe1-xAlx)2 and DyFe2Al10 were investigated by [1991Su, 1996Kor, 1996Mus,
1999Zho] and by [1998Thi, 2000Ree], respectively.
Magnetic properties of Dy2(Fe1-xAlx)17 alloys have been studied by [1984Plu], calculated by [1999Hao],
reviewed by [1994Liu, 2002Ram] and, at the Dy2Fe9Al8 composition, studied by [1996Rid].
Magnetic properties of 4 Dy(Fe1-xAlx)12 have been investigated by low temperature Cp measurements,
neutron diffraction, etc. by [1978Bus, 1988Sch, 1997Pai, 1998Hag, 2000Hag, 2000Pai] at the DyFe4Al8composition, by [1981Fel, 1988Che] at DyFe6Al6 and by [2001Sch] at DyFe7Al5.
Moreover [1998Ima] investigated the crossover from Heisemberg to Ising spin-glass-like magnetic
properties in random anisotropy magnets of amorphous Dy16Fe84-x Alx (0 x 62) and [2002Kon] studied
the magnetic properties and microstructure of melt-spun ribbons of Dy60Fe30Al10 alloys.
References
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-Rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids, 6, 16-37 (1958) (Crys. Structure,
Experimental, 49)
[1961Lih] Lihl, F., Ebel, H., “X-ray Examination of the Constitution of Iron-Rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenwes., 32, 483-487, (1961) (Crys.
Structure, Experimental, 12)
[1962Wer] Wernick, J.H., Haszko, S.E., Dorsi, D., “Pseudobinary Systems Involving Rare Earth Laves
Phases”, J. Phys. Chem. Solids, 23, 567-572 (1962) (Crys. Structure, Experimental, 22)
[1966Bus] Buschow, K.H.J., “The Crystal Structures of the Rare-Earth Compounds of the Form
R2Ni17, R2Co17 and R2Fe17”, J. Less Common Met., 11, 204-208 (1966) (Crys. Structure,
Thermodyn., Experimental, 8)
[1966Kri] Kripyakevich, P.I., Frankevich, D.P., “New Compounds of Rare Earth with Mn and Fe, and
Their Crystal Structures”, Kristallografiya, 10(4), 560 (1966), translated from Sov. Phys.
Crystallogr., 10(4), 468-469 (1966) (Crys. Structure, Experimental, 11)
[1970Bus] Buschow, K.H.J., van Stapele, R.P., “Magnetic Properties of Some Cubic Rare-Earth-Iron
Compounds of the Type RFe2 and RxY1-xFe2”, J. Appl. Phys., 41(10), 4066-4069 (1970)
(Crys. Structure, Experimental, 8)
[1970Goo] Goot van der, A.S., Buschow, K.H.J., “The Dysprosium-Iron System: Structural and
Magnetic Properties of Dysprosium-Iron Compounds”, J. Less Common Met., 21, 151-157
(1970) (Equi. Diagram, Crys. Structure, Experimental, 11)
[1971Oes] Oesterreicher, H., “Structural Studies of Rare-Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Crys. Structure, Experimental, 6)
225
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Al–Dy–Fe
[1972Oes] Oesterreicher, H., Pitts, R., “Structural and Magnetic Studies on DyFe2-DyAl2 and
DyCo2-DyAl2”, J. Appl. Phys., 33, 5174-5179 (1972) (Crys. Structure, Experimental, 11)
[1973Oes] Oesterreicher, H., “X-Ray and Neutron Diffraction Study of Ordering on Crystallographic
Sites in Rare Earth Base Alloys Containing Al and Transition Metals”, J. Less-Common
Met., 33, 25-41 (1973) (Crys. Structure, Experimental, 19)
[1973Viv] Vivchar, O.I., Zarechnyuk, O.S., Ryabov, V.R., “X-Ray Diffraction Study of Dy-Fe-Al
Alloys in the 0-33.3 at.% Dy Range” (in Ukrainian), Dop. Akad. Nauk Ukr. RSR, Ser. A,
Fiz.-Mat. Tekh. Nauki, 1, 159-161 (1973) (Crys. Structure, Equi. Diagram, Experimental,
17)
[1973Zar] Zarechnyuk, O.S., Rikhal, R.M., Vivchar, O.I., “Laves Phases in Ternary Systems of the
Type Rare-Earth Metal-Transition Metal-Al” (in Russian), Akad. Nauk Ukr. SSR,
Metallofizika, 46, 92-94 (1973) (Crys. Structure, Experimental, 22)
[1974Oes] Oesterreicher, H., “Constitution of Al Base Rare Earth Alloys RT2-RAl2 (R = Pr, Gd, Er, T
= Mn, Fe, Co, Ni, Cu)”, Inorg. Chem., 13, 2807-2811 (1974) (Crys. Structure,
Experimental, 30)
[1974Viv] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12-Type Structure in R-Fe-Al
Systems” (in Russian), Tezisy. Dokl.-Vses. Konf. Kristallokhim. Intermet. Soedin., Rykhal,
R.M. (Ed.), Vol. 2, Gos. Univ., Lvov, 41 (1974) (Crys. Structure, Experimental, 0)
[1975Dwi] Dwight, A.E., Kimball, C.W., Preston, R.S., Taneja, S.P., Weber, L., “Crystallographic and
Mössbauer Study of (Sc, Y, Ln) (Fe, Al)2 Intermetallic Compounds”, J. Less-Common Met.,
40, 285-291 (1975) (Crys. Structure, Experimental, Moessbauer, 8)
[1976Bus] Buschow, K.H.J., van der Vucht, J.H.N., van den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth-3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Crys. Structure, Experimental, 2)
[1976Gro] Groessinger, R., Steiner, W., Krec, K., “Magnetic Investigations of Pseudobinary RE(Fe,
Al)2 Systems (RE = Y, Gd, Dy, Ho)” (in German), J. Magn. Magn. Mater., 2, 196-202
(1976) (Experimental, 20)
[1977Oes] Oesterreicher, H, McNeely, D., “Studies on Compounds DyFe3, Dy6Fe23 and Dy2Fe17 with
Al Substitution for Fe. I: Structural Investigations”, J. Less-Common Met., 53, 235-243
(1977) (Crys. Structure, Experimental, 30)
[1978Bus] Buschow, K.H.J., van der Kran, A.M., “Magnetic Ordering in Ternary Rare Earth Iron
Aluminium Compounds (RFe4Al8)”, J. Phys. F: Met. Phys., 8, 921-932 (1978) (Magn.
Prop., Experimental, 8)
[1980Fel] Felner, I., “Crystal Structures of Ternary Rare Earth-3d Transition Metal Compounds of the
RT6Al6 Type“, J. Less-Common Met., 72, 241-249 (1980) (Crys. Structure, Experimental,
10)
[1981And] Andreyev, A.V., Deryagin, A.V., Zadvorkin, S.M., Moskalev, V.N., “Magnetostriction
Distorsions of the Crystal Structure in ErFe2 and DyFe2”, Fiz. Met. Metalloved., 51(5),
975-979 (1981) (in Russian), translated from Phys. Met. Metallogr., 51(5), 64-67 (1981)
(Equi. Diagram, Crys. Structure, Magn. Prop., Experimental)
[1981Fel] Felner, I., Seh, M., Rakavy, M., Nowik, I., “Magnetic Order and Hyperfine Interactions in
RFe6Al6 (R = Rare Earth)”, Phys. Chem. Solids, 42, 369-377 (1981) (Crys. Structure,
Experimental, 6)
[1984Plu] Plusa, D., Pfranger R., Wyslocki, B., “Magnetic Properties of the Dy2(Fe1-xAlx)17
Pseudobinary Compounds”, J. Less-Common Met., 99, 87-97 (1984) (Crys. Structure,
Experimental, 26)
[1986Gri] Griger, A., Syefaniay, V., Turmezey, T., “Crystallographic Data and Chemical
Compositions of Aluminum-Rich Al-Fe Intermetallic Phases”, Z. Metallkd., 77, 30-35
(1986) (Equi. Diagram, Crys. Structure, Experimental, 23)
[1988Che] Chelkowska, G., Chelkowska, A., Winiarska, A., “Magnetic Susceptibility and Structural
Investigations of Rare Earth-Aluminium-Iron (REAl6Fe6) Compounds for RE = Yttrium,
226
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Al–Dy–Fe
Terbium, Dysprosium, Holmium, and Erbium”, J. Less-Common Met., 143, L7-L10 (1988)
(Crys. Structure, Experimental, 12)
[1988Gsc] Gschneidner, K.A. Jr., Calderwood, F.W., “The Al-Dy (Aluminum-Dysprosium) System”,
Bull. Alloy Phase Diagrams, 9, 673-675 (1988) (Equi. Diagram, Review, 29)
[1988Sch] Schaefer, W., Groenefeld, M., Will, G., Gal, J., “Magnetic Helical Ordering in Intermetallic
Rare Earth-Iron-Aluminum Compounds”, Mater. Sci. Forum, 27-28, 243-248 (1988) (Crys.
Structure, Experimental, 9)
[1988Won] Wong-NG, W., McMurdie, H.F., Paretzkin, B., Kuchinski, M., Dragoo, A., “Standard
X-Ray Diffraction Powder Patterns of Fourteen Ceramic Phases”, Powder Diffr., 3, 246-264
(1988) (Crys. Structure, Experimental, 1)
[1991Gri] Grieb B., “Al-Dy-Fe (Aluminium - Dysprosium - Iron),” MSIT Ternary Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart; Document ID: 10.13514.1.20, (1991) (Equi. Diagram, Crys.
Structure, Assessment, 15)
[1991Su] Su, G., Liu, H., Li, F.-S., Ge, M.-L., “Theoretical Interpretation of the Anomalous
Temperature Dependence of Coercivity at Low Temperatures in Some Pseudobinary
Intermetallics”, Phys. Status Solid A, A126, 459-468 (1991) (Experimental, Thermodyn.,
10)
[1993Kat] Kattner, U.R., Burton, B.P., “Al-Fe (Aluminum-Iron)”, in “Phase Diagrams of Binary Iron
Alloys”, Okamoto, H. (Ed.), ASM International, Materials Park, OH, 12-28 (1993) (Equi.
Diagram, Review, 99)
[1993Oka] Okamoto, H., “Fe-Ho (Iron-Holmium)”, in “Phase Diagrams of Binary Iron Alloys”,
Okamoto H.(Ed.), ASM International, Materials Park, OH, 44073-0002, 179-181 (1993)
(Equi Diagram, Review, 20)
[1994Bur] Burkhardt, U., Grin, J., Ellner, M., Peters, K., “Structure Refinement of the Iron-Aluminium
Phase with the Approximate Composition Fe2Al5”, Acta Crystallogr., Sect. B: Struct.
Crystallogr. Crys. Chem., B50, 313-316 (1994) (Crys. Structure, Experimental, 9)
[1994Gri] Grin, J., Burkhardt, U., Ellner, M., Peters, K., “Refinement of the Fe4Al13 Structure and its
Relationship to Quasihomological Homotypical Structures”, Z. Kristallogr., 209, 479-487
(1994) (Crys. Structure, Experimental, 39)
[1994Liu] Liu, J.P., Boer, F.R. de, Chatel, P.F. de, Coehoorn, R., Buschow, K.H.J., “On the 4f-3d
Exchange Interaction in Intermetallic Compounds”, J. Magn. Magn. Mater., 132, 159-179
(1994) (Magn. Prop., Review, 64)
[1996Kor] Korolyov, A.V., Mushnikov, N.V., Zajkov, N.K., “Low Temperature Magnetisation Jumps
in Dy(Fe,M)2 (M=Al, Si, Ga) and Sm(Co,Ni)5”, Czechoslov. J. Phys., 46, 2095-2096 (1996)
(Magn. Prop., Experimental) as quoted in [Curr. Cont.]
[1996Mao] Mao, O., Yang, J., Altounian, Z., Ström-Olsen, J.O., “Metastable RFe7 Compounds
(R=Rare Earths and Their Nitrides with TbCu7 Structure)”, J. Appl. Phys., 79(8), 4605-4607
(1996) (Crys. Structure, Magn. Prop., Experimental, 5)
[1996Mus] Mushnikov, N.V., Zajkov, N.K., Korolyov, A.V., “On the Nature of Magnetization Jumps
in Dy(Fe,M)2 (M= Al, Si)”, J. Magn. Magn. Mater., 163, 322-326 (1996) (Crys. Structure,
Experimental, 15)
[1996Rid] Ridwan, S., Mujamilah, H., Gunawan, M., Marsongkohadi, P.,Yan, Q.W., Zhang, P.L., Sun,
X.D., Cheng, Z.H., Minakawa, N., Hamaguchi, Y., “High Resolution Neutron Powder
Diffraction Study of Dy2Fe9Al8 at 65 K”, J. Phys. Soc. Jpn., 65(2), 348-350 (1996) (Crys.
Structure, Magn. Prop., Experimental) as quoted in [Curr. Cont.]
[1997Kog] Kogachi, M., Haraguchi, T., “Quenched-in Vacansies in B2-Structured Intermetallic
Compound FeAl”, Mater. Sci. Eng. A, A230, 124-131 (1997) (Crys. Structure,
Experimental, 23)
[1997Pai] Paixao, J.A., Langridge, S., Sorensen, S.Aa., Lebech, B., Gonçalves. A.P., Lander, G.H.,
Brown, P.J., Talik, P., Talik, E., “Unusual Magnetic Interactions in Compounds with the
ThMn12 Structure”, Physica B, B234-B236, 614-616 (1997) (Magn. Prop., Experimental, 6)
227
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Al–Dy–Fe
[1998Ali] Aliravci, C.A., Pekgueleryuez, M.O., “Calculation of Phase Diagrams for the Metastable
Al-Fe Phases Forming in Direct-Chill (DC)-Cast Aluminium Alloy Ingots”, Calphad, 22,
147-155 (1998) (Calculation, Equi. Diagram, 20)
[1998Hag] Hagmusa, I.H., Brueck, E., de Boer, F.R., Buschow, K.H.J., “Magnetic Properties of
RFe4Al8 Compounds Studied by Specific Heat Measurements“, J. Alloys Compd., 278,
80-82 (1998) (Magn. Prop., Experimental, 9)
[1998Ima] Imai, K., Masago, E., Saito, T., Shinagawa, K., Tsushima, T., “Crossover from Heisemberg
to Ising Spin-Glass-Like Magnetic Properties in Random Anisotropy Magnets Amorphous
Dy16MxFe84-x (M = Cu, Al, Cu and Al”, J. Magn. Magn. Mater., 177-181, 99-100 (1998)
(Crys. Structure, Experimental, 6)
[1998Psz] Pszczola, J., Gicala, B. and Suwalski, J., “57Fe Slater-Pauling Dependance in the
Dy(Fe1-xAlx)2 Intermetallic System”, J. Alloys Compd., 274, 47-54 (1998) (Crys. Structure,
Magn. Prop., Moessbauer, Experimental, 33)
[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10(Ln = Y, La = Nd,
Sm, Gd = Lu and T=Fe, Ru, Os) with YbFe2Al10 Type Structure and Magnetic Properties
of the Iron-Containing Series“, J. Mater. Chem., 8(1), 125-130 (1998) (Crys. Structure,
Magn. Prop., Experimental, 31)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-Rich Fe-Al
Alloys”, Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 15)
[1999Hao] Hao, Y., Wang, F., Zhang, P., Sun, X., Yan, Q.W., “An X-Ray Diffraction Study and
Calculation of the Exchange Interaction Constant Between the Rare-Earth Sublattice and
the 3d Sublattice of Dy2Fe17-xAlx Compounds”, J. Phys.: Condens. Matter, 11, 6113-6119
(1999) (Crys. Structure, Magn. Prop., Experimental, Calculation, 13)
[1999Zho] Zhong, W.D., Chen, H.Y., Liu, Z.X., Wu, J.H., Li, G.Z., “Macroscopic Quantum Effects in
Single Crystal Dy(Fe0.8Al0.2)2”, Acta Phys. Sin.(Chin. J. Phys.), 48(12), S204-S210 (1999)
(Magn.Prop., Experimental) as quoted in [Curr. Cont.]
[2000Hag] Hagmusa, I.H., Brueck, E., de Boer, F.R., Buschow, K.H.J., “A Specific-Heat Study of
Some RFe4Al8 Compounds (R = Ce, Pr, Nd, Dy, Ho, Tm)”, J. Alloys Compd., 298, 77-81
(2000) (Crys. Structure, Thermodyn., Experimental, 16)
[2000Pai] Paixao, J.A., Silva, M.R., Sorensen, S.A., Lebech, B., Lander, G.H., Brown, P.J., Langridge,
S., Talik, E., Goncalves, A.P., “Neutron-Scattering Study of the Magnetic Structure of
DyFe4Al8 and HoFe4Al8”, Phys. Rev. B, 61B(9), 6176-6188 (2000) (Crys. Structure, Magn.
Prop., Experimental, 17)
[2000Ree] Reehuis, M., Fehrmann, B., Wolff, M.W., Jeitschko, W., Hofmann, M., “Antiferromagnetic
Order in TbFe2Al10 and DyFe2Al10”, Physica B, 276B-278B, 594-595 (2000) (Crys.
Structure, Magn. Prop., Experimental, 4)
[2000Sac] Saccone, A., Cardinale, A.M., Delfino S., Ferro, R., “Gd-Al and Dy-Al Systems: Phase
Equilibria in the 0 to 66.7 at.% Al Composition Range”, Z. Metallkd., 91(1), 17-23 (2000)
(Equi. Diagram, Experimental, 12)
[2001Ike] Ikeda, O., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
BCC Phases in the Fe-Rich Portion of hte Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Equi. Diagram, Thermodyn., Experimental, 18)
[2001Sch] Schaefer, W., Halevy, I., “Neutron Powder Diffraction of Iron-Rich Rare
Earth-Iron-Aluminium Intermetallics RFe7Al5 (R = Tb, Dy, Ho, Er)”, Mater. Sci. Forum,
378-381, 414-419 (2001) (Crys. Structure, Magn. Prop., Experimental, 12)
[2001Yan] Yanson, T., Manyako, M., Bodak, O., Cerny, R., Yvon, K., “Effect of Aluminium
Substitution and Rare-Earth Content on the Structure of R2(Fe1-xAlx)17 (R = Tb, Dy, Ho,
Er) Phases”, J. Alloys Compd., 320(1), 108-113 (2001) (Crys. Structure, Equi. Diagram,
Experimental, 9)
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[2002Kon] Kong, H.Z., Ding J., Dong, Z.L., Wang, L., White, T., Li, Y., “Observation of Clusters in
Re60Fe30Al10 Alloys and the Associated Magnetic Properties“, J. Phys. D: Appl. Phys., 35,
423-429 (2002) (Crys. Structure, Magn. Prop., Experimental, 26)
[2002Ram] Rama Rao, K. V. S., Ehrenberg, H., Markandeyulu, G., Varadaraju, U. V., Venkatesan, M.,
Suresh, K. G., Murthy, V. S., Schidt, P. C., Fuess, H., “On the Structural and Magnetic
Properties of R2Fe(17-x)(A, T)x (R = Rare Earth, A = Al, Si, Ga, T=Transition Metal)
Compounds”, Phys. Status Solidi A, 189A(2), 373-388 (2002) (Crys. Structure, Magn.
Prop., Review, 51)
[2002Gry] Grytsiv, A., “Al-Dy (Aluminium-Dysprosium)”, MSIT Binary Evaluation Program, in
MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; Document ID: 20.20073.1.20 (2002) (Equi. Diagram, Assessment, Crys.
Structure, 8)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)” MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart, to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 58)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
( Fe)
1538-1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)
1394-912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2, 1993Kat]
dissolves up to 1.2 at.% Al
( Fe)
< 912
cI2
Im3m
W
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60.to 290.12
pure Fe at 25°C [Mas2]
dissolves up to 45.0 at.% Al at 1310°C
0-18.8 at.%Al, HT [1958Tay]
0-19.0 at.% Al, HT [1961Lih]
0-18.7 at.% Al, 25°C [1999Dub]
( Dy)
1412-1381
cI2
Im3m
W
a = 398.0 [Mas2]
dissolves up to 3 at.% Al at 1300°C
[1988Gsc]
( Dy)
< 1381
hP2
P63/mmc
Mg
a = 359.15
c = 565.01
[Mas2]
dissolves up to 1 at.% Al at 1300°C
[1988Gsc]
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Fe4Al13
< 1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7 to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
74.16-76.70 at.% Al [1986Gri]
at 76.0 at.% Al [1994Gri]
Fe2Al5< 1169
oC24
Cmcm
Fe2Al5
a = 765.59
b = 641.54
c = 421.84
at 71.5 at.% Al [1994Bur]
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [1993Kat]
1232-1102
cI16?
-
a = 598.0 at 61 at.% Al [1993Kat]
FeAl
< 1310
cP8
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5 - 47.5 at.% Al [1961Lih]
36.2 - 50.0 at.% Al [1958Tay]
39.7 - 50.9 at.% Al [1997Kog] 500°C
quenched in water
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
24 - 37 at.% Al [2001Ike]
23.1 - 35.0 at.% Al [1958Tay]
24.7 - 31.7 at.% Al [1961Lih]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [1993Kat]
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
metastable
85.7 at.% Al [1993Kat]
[1998Ali]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable [1998Ali]
DyAl31090-1005
hR60
R3m
HoAl3
a = 607.0
c = 3590
[1988Gsc]
(preparable also at 800°C
under 15 kbar)
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
230
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Fe
DyAl3< 1005
hP16
P63/mmc
TiNi3
a = 609.1
c = 953.3
[1988Gsc]
DyAl3 (I)
Dy(FexAl1-x)3 (h)
cP4
Pm3m
AuCu3
a = 423.6
a = 425.3
HP [V-C]
x = 0.067 (1000°C) Fe stabilised phase
[1977Oes]
DyAl2< 1500
Dy(FexAl1-x)2
cF24
Fd3m
MgCu2
a = 784
a = 783.5 to 766
x = 0 [1988Gsc], [2000Sac]
0 x 0.39 [1975Dwi]
0 x 0.3 [1998Psz]
DyAl
< 1110
oP16
Pbcm
ErAl
a = 582
b = 1137 to 1134
c = 560 to 559
[1988Gsc, 2000Sac]
Dy3Al2< 1025
tP20
P42/mnm
Zr3Al2
a = 817 to 820
c = 754 to 755
[1988Gsc, 2000Sac]
Dy2Al
< 990
oP12
Pnma
Co2Si
a = 654 to 653
b = 508
c = 940 to 938
[1988Gsc, 2000Sac]
Dy2Fe17
< 1375
Dy2(Fe1-xAlx)17
hP38
P63/mmc
Th2Ni17
a = 844.4
c = 831.0
a = 845.5 to 853.8
c = 830.9 to 836.0
a = 846.5 to 855.5
c = 829.6 to 836.1
a = 849 to 857
c = 833 to 838
[1966Bus]
0 x 0.168 [1977Oes]
0 x 0.18 ( at 1050°C) [1999Hao]
[2001Yan]:
0 x 0.2 (at 10.5 at.% Dy, data taken
from graph)
0 x 0.25 (at 9.5 at.% Dy, data taken
from graph)
DyFe7 hP8
P6/mmm
TbCu7
a = 487
c = 418
metastable phase prepared by annealing
mechanically alloyed powders
[1996Mao] (lattice parameters from
graph)
Dy6Fe23
< 1290
Dy6(Fe1-xAlx)23
cF116
Fm3m
Th6Mn23
a = 1206
a = 1206.2
a = 1205.64
a = 1214.94
[1966Kri]
[1970Goo]
0 x 0.25 at 1000°C [1977Oes]
x = 0 [1977Oes]
x = 0.25 [1977Oes]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
231
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Fe
DyFe3
< 1305
Dy(Fe1-xAlx)3
hR36
R3m
PuNi3
hP24
P63/mmc
CeNi3(related to the
PuNi3-type:
aPuNi3aCeNi3,
cPuNi33/
2cCeNi3)
a = 511.6
c = 2455
a = 511.8 to 513.3
c = 2454 to 2454
a = 517.7 to 522.7
c=1658.4 to 1679.0
[1970Goo]
0 x 0.067 [1977Oes]
0.13 x 0.43 [1977Oes]
Possibly this structure can be considered
as a high temperature ternary phase (not
reported in Fig. 1). Further research
required.
DyFe2
< 1270
Dy(Fe1-xAlx)2
cF24
Fd3m
MgCu2
a = 732.5
a = 732.4 to 747.4
a 731 to 748
[1970Bus]
0 x 0.34 at 800°C [1975Dwi]
0 x 0.3 [1998Psz] (data taken from
graph)
DyFe2 (l)
< 23
t** [1981And]
tetragonal distorsion of the cubic form
* 1, Dy2(Fe1-xAlx)17 hP8-x
P6/mmm
TbCu7
or hP22
P622
Tb2Fe14Al3(related to TbCu7
type: aTbCu7aTb2Fe14Al3/31/2)
a = 495 to 497
c = 419 to 421
a = 857.2
c = 419.3
0.22 x 0.28 (at 10.5 at.% Dy, data
taken from graph)
x 0.28 (at 9.5 at.% Dy) [2001Yan]
at x = 0.22 [1977Oes]
* 2, Dy2(Fe1-xAlx)17 hR57
R3m
Th2Zn17
a = 866.3 to 876.9
c = 1261.1 to 1270.2
a = 859.7 to 877.9
c = 1255.2 to 1271.4
a = 863 to 877
c = 1260 to 1266
0.28 x 0.50 [1977Oes]
0.23 x 0.52 [1999Hao]
[2001Yan]
0.30 x 0.50 (at ~9.5±10.5 at.% Dy,
data from graph)
0.17 x 0.50 (at ~11.5 at.% Dy)
* 3, Dy(Fe1-xAlx)2 hP12
P63/mmc
MgZn2
a = 534.8
c = 869.5
a = 532 to 538
c = 869 to 874
0.375 x 0.56 at 800°C [1975Dwi]
x = 0.48 [1973Oes]
0.4 x 0.52 [1998Psz] (data from
graph)
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
232
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Fe
* 4 , Dy(Fe1-xAlx)12 tI26
I4/mmm
ThMn12 a = 871.5
c = 503.7
a = 865.0
c = 500.1
a = 864.2
c = 502.6
0.54 x 0.71 at 500°C [1973Viv]
at x = 0.67 [1976Bus]
at x = 0.5 at 800°C [1980Fel]
at x = 0.5 [1988Che]
* 5, DyFe2Al10 oC52
Cmcm
YbFe2Al10
(related to the
ThMn12 type:
ao at, bo 2ct,
co at)
a = 895.4
b = 1014.1
c = 900.0
a = 893.3
b = 1010.6
c = 896.9
[1998Thi] (annealed at 800°C and
cooled at 6°C h-1)
neutron diffraction at 1.5 K [2000Ree]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
20
40
60
80
20 40 60 80
20
40
60
80
Dy Fe
Al Data / Grid: at.%
Axes: at.%
τ5
τ3
Dy(Fe1-xAlx)2
Dy(Fe1-xAlx)3
Dy6(Fe1-xAlx)23
Fe3Al
τ4
DyAl3Fe4Al13
FeAl2
Fe2Al5
τ2
τ1
FeAl
(αFe)
Dy(FexAl1-x)2
Dy2(Fe1-xAlx)17
(Al)Fig. 1: Al-Dy-Fe.
Subsolidus phase
equilibria concluded
from studies made at
different
temperatures.
See section
“Isothermal Sections“
233
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
Aluminium – Dysprosium – Nickel
Riccardo Ferro, Gilda Zanicchi, Rinaldo Marazza
Literature Data
Several investigations have been carried out mainly concerning the intermediate phases, their crystal
structures and magnetic properties [1962Wer, 1968Dwi, 1970Leo, 1972Ryk, 1973Oes, 1973Ryk, 1973Zar,
1977Ryk, 1978Ryk, 1980Ryk, 1981Zar, 1982Roml, 1982Rom2, 1987Tsv1, 1987Tsv2, 1993Gla, 1995Sor,
1997Ehl, 1997Kol, 2002Bur, 2002Dan, 2002Lam]. Different alloys were prepared by arc melting or by
levitation melting carried out under He or Ar. The alloys were generally annealed at temperatures between
600 and 900°C. An investigation of the section DyNi2-DyAl2 was carried out by [1970Leo]. Ranges of
stability of the different phases (DyNi2 and DyAl2-based solid solutions and the intermediate DyNiAl
phase) and structural and magnetic properties were studied. A systematic investigation of the 800°C
isothermal section in the 0 to 33.3 at.% Dy composition range was also carried out by [1980Ryk]. This study
was performed by preparing 45 alloys from 99.98 mass% Al, 99.9 % Ni and 99.6 % Dy. Alloys were
prepared by arc melting under purified argon, annealing at 800°C for 700 h and then quenching in ice water.
A high pressure form of DyNiAl (MgZn2 type) prepared by annealing the initial powdered components at
1450 to 1500°C at a pressure of 7.7 GPa has also been reported [1987Tsvl]. The same information is given
in [1987Tsv2]. [1993Gla] determined the structure of the new DyNi3Al9 compound which crystallizes in
the rhombohedral hR78- ErNi3Al9 type.
Binary Systems
The Al-Dy from [2003Gry], Al-Ni from [2003Sal] and Dy-Ni from [2000Oka] systems have been accepted.
Solid Phases
Special attention was dedicated to the 0 to ~ 30 at.% Dy composition range. Several solid phase pertaining
to this composition field have been described. [1993Gla] determined the structure of the new DyNi3Al9compound which crystallizes in the trigonal ErNi3Al9 type structure, with partly disordered arrangement of
Al-atom triangles and rare earth metal atoms. The crystal properties of the unary, binary and ternary phases
are reported in Table 1. [1973Oes] and [1980Ryk] describe 9, DyNiAl, as a point phase. According to
[1970Leo], however, a certain range of homogeneity between 44 and 52 mole% DyAl2 could be assigned
to this phase along the DyAl2-DyNi2 section.
Notice that on the basis of the lattice parameter values, an analogy between the crystal structures of 1 and
5 may be envisaged a( 1) ≅ a( 5), b( 1) ≅ b( 5), c( 1) ≅ 4 c( 5).
[1995Sor] studied structural properties of the DyNi5-xAlx-hydrogen system. It was found that the hexagonal
crystal structure of the prototype compound DyNi5 (CaCu5 type) exists up to DyNi3Al2, beyond this
composition and up to DyNi2Al3 another related hexagonal structure (YCo3Ga2 type) was observed.
The two forms, conventionally indicated as Dy2Ni7 and Dy2Ni7 have a similar stability, even if in
[1970Bus] an indication is given that probably in rare earth - nickel compounds R2Ni7 the hexagonal form
is stable at high temperature and the rhombohedral at low temperature (at variance however with
[1969Vir]). The transformation between the two forms is sluggish and possibly of the martensitic type. No
indication about a transformation temperature may be reported in Table 1 and in Fig. 1, only a generic
indication to Dy2Ni7 is given.
Isothermal Sections
The partial isothermal section at 800°C, given in Fig. 1, is based on the data of [1980Ryk] who used long
homogenizing annealing periods, followed by quenching in ice water. The solubility limits seem to be
established not very precisely in [1980Ryk], therefore some tie-lines are shown in Fig. 1 by dashed lines.
The liquid phase equilibria in the Al corner have not been studied. [1980Ryk] did not report in his section
234
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
the new phase DyNi3Al9 identified more recently by [1993Gla], it has been included in Fig. 1 with an
indication of a possible trend of the tie-lines (dashed lines).
Miscellaneous
Magnetic properties of the Al-Dy-Ni (and more generally of Al-R-Ni) alloys have been studied and
discussed in several papers. [1970Leo] studied AlxNi2-xR alloys: magnetic properties of Al-Ni-Dy, for
x = 0.16 and 1.80, have been measured. Magnetic parameters of DyNiAl have been reported by [1973Oes].
Magnetic properties of DyNiAl2 and of Dy2Ni2Al have been studied by [1982Roml] and [1982Rom2].
Hydrogen adsorption in RNi4Al alloys has been studied [1978Tak].
[1995Sor] studied hydrogen absorption in the DyNi5-xAlx system. All alloys were exposed to hydrogen gas
at pressure up to 15 MPa and temperatures between 77 and 700 K. Under these conditions ternary alloys
having the CaCu5 structure react with hydrogen, the other ternary alloys do not exhibit any significant
hydrogen absorption. The pressure-composition isotherms were measured.
[1997Kol] studied hydrogen absorption - desorption, crystal structure and magnetism in intermetallic
compound of the series RNiAl (R = Y, Gd, Tb, Dy, Er, Lu), by means of neutron diffraction and
susceptibility measurements. These compounds, crystallizing in the ZrNiAl-type of crystal structure, form
hydrides containing up to 1.4 H/f.u. and the hydrogenation leads to a drastic reduction of magnetic ordering
temperatures. The crystallographic characteristics of RNiAl compounds and of their hydrides or deuterides
were reported.
[1997Ehl] investigated magnetic order in rare-earth based intermetallic compounds of the series RNiAl
(R = Pr, Nd, Tb, Dy, Ho), by means of neutron diffraction and susceptibility measurements.
[2002Lam] measured magnetic moments as a function of temperature in a magnetic field of 0.04T for
DyNi5-xAlx alloys (x = 0; 1; 1.5; 2; 2.5; 3). Magnetic parameters, magnetic behavior and cell dimensions
were reported.
[2002Bur] reported magnetic and X-ray photoelectron spectroscopy (XPS) measurements for DyNi5-xAlx.
[2002Dan] investigated the temperature changes of the lattice parameters in DyNiAl, using low temperature
X-ray powder diffraction: these changes were related to magnetic ordering of the compound. The values of
the refined structure parameter (for 300 and 50K) were reported and compared with those obtained from
powder neutron diffraction.
References
[1962Wer] Wernick, J.H., Haszko, S.E., Dorsi, D., “Pseudobinary Systems Involving Rare-Earth Laves
Phases”, J. Phys. Chem. Solids, 23, 567-572 (1962) (Crys. Structure, Experimental, 22)
[1968Dwi] Dwight, A.E., Mueller, M.H., Conner, R.A., Downey, J.W., Knott, H., “Ternary
Compounds with the Fe2P-Type Structure”, Trans. Met. Soc. AIME, 242, 2075-2080 (1968)
(Crys. Structure, Experimental, 14)
[1969Vir] Virkar, A.V., Raman, A.J., “Crystal Structures of AB3 and A2B7 Rare-Earth - Nickel
Phases”, Less-Common Met., 18, 59-66 (1969) (Crys. Structure, Experimental)
[1970Bus] Buschow, K.H.J., van der Goot, A.S., “The Crystal Structure of Rare-Earth - Nickel
Compounds of the type R2Ni7”, J. Less-Common Met., 22, 419-428 (1970) (Crys. Structure,
Experimental, 10)
[1970Leo] Leon, B., Wallace, W.E., “Magnetic and Structural Characteristics of Ternary Intermetallic
Systems Containing Lanthanides”, J. Less-Common Met., 22, 1-10 (1970) (Crys. Structure,
Magn. Prop., Experimental, 13)
[1972Ryk] Rykhal, R.M., Zarechnyuk, O.S., Pyshchick, G.V., “New Ideas on the MgCuAl2-Structure
Type” (in Russian), Visn. L’viv. Derz. Univ., Ser. Khim., 14, 13-15 (1972) (Crys. Structure,
Experimental, 3)
[1973Oes] Oesterreicher, H., “Structural and Magnetic Studies on Rare-Earth Compounds RNiAl and
RCuAl”, J. Less-Common Met., 30, 225-236 (1973) (Crys. Structure, Magn. Prop.,
Experimental, 21)
235
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
[1973Ryk] Rykhal’, R.M., Zarechnyuk, O.S., Pyshchik. G.V., “New Representatives of the MgCuAl2and YNiAl4 Types of Structure” (in Russian), Dop. Akad. Nauk Ukr. RSR, Fiz-Mat. Tekh.,
(6), 568-570 (1973) (Crys. Structure, Experimental, 2)
[1973Zar] Zarechnyuk, O.S., Rykhal, R.M., Vivchar, O.I., “Laves Phases in Ternary Systems
Rare-Earth Metal-Transition Metal of the IV Period-Aluminium”, Sb. Nauch. Rabot Inst.
Metallofiz., Akad. Nauk Ukr. SSR, (42), 92-94 (1973) (Crys. Structure, Experimental,
Review, 22)
[1977Ryk] Rykhal, R.M., “The Crystal Structure of Y3Ni6Al2 and Relative Compounds”, Vestn. L’vov.
Univ. Ser. Khim., 19, 34-36 (1977) (Crys. Structure, Experimental)
[1978Ryk] Rykhal, R.M., “New Representatives of Structural Types Ce3Co8Si and Mo2NiB2 in Rare
Earth-Ni-Al-Systems” (in Russian), Tret’ya Vses. Konf. Kristall. Intermetallicheskikh
Soyedineniy, 17 (1978) (Crys. Structure, Experimental, 0)
[1978Tak] Takeschita, T., Malik, S.K., Wallace, W.E., “Hydrogen Absorption in RNi4Al (R = Rare
Earth) Ternary Compounds”, J. Solid State Chem., 23, 271-274 (1978) (Crys. Structure,
Experimental, 8)
[1980Ryk] Rykhal, R.M., Zarechnyuk, O.S., Mandzin, V.M., “X-Ray Structural Studies of Terbium,
Dysprosium-Nickel-Aluminum Ternary Systems in the Range of 0-33.3 at.% Rare Earth
Metal” (in Ukrainian), Dopov. Akad. Nauk. Ukr. RSR, Ser. A: Fiz.- Mat.Tekh.Nauki, (12)
77-79 (1980) (Equi. Diagram, Crys. Structure, Experimental, 10)
[1981Zar] Zarechnyuk, O.S., Rykhal’, R.M., “The Crystal Structure of the Compound YNi2Al3 and
Related Phases” (in Russian), Vestn. L’vov. Univ. Ser. Khim., 23, 45-47 (1981) (Crys.
Structure, Equi. Diagram, Experimental, 6)
[1982Rom1] Romaka, V.A., Zarechnyuk, O.S., Rykhal, R.M., Yarmolyuk,Ya.P., Skolozdra, R.V.,
“Magnetic Susceptibility and Crystal Structure of RNiAl2 Compounds” Phys. Met. Metall.,
54(2), 191-193 (1982), translated from Fiz. Met. Metalloved., 54(2), 410-412 (1982) (Crys.
Structure, Magn. Prop., Experimental, 6)
[1982Rom2] Romaka, V.A., Grin, Yu.N., Yarmolyuk, Ya.P,. Zarechnyuk, O.S., Skolozdra, R.V.,
“Magnetic and Crystallographic Parameters of R2Ni2Ga and R2Ni2Al Compounds” Phys.
Met. Metall. 54(4) 58-64, (1982), translated from Fiz. Met. Metalloved., 54(4), 691-696
(1982) (Crys. Structure, Magn. Prop., Experimental, 13)
[1987Tsv1] Tsvyashchenko, A.V., Fomicheva, L.N., “New Polymorphic Modifications of the
Compounds RTAl (R = Rare Earth Metal, T = Cu, Ni)”, Inorg. Mater. (Engl. Trans.), 23(7),
1024-1027 (1987) (Crys. Structure, Experimental, 15)
[1987Tsv2] Tsvyashchenko, A.V., Fomicheva, L. N., “Crystallization of the Laves Phases Rare Earth
Nickel Aluminum (RNiAl) (C14 Type) at High Pressure”, J. Less-Common Met., 135(1),
L9-L12 (1987) (Crys. Structure, Experimental, 10)
[1992Mur] Murakami, Y., Otsuka, K., Hanada, S., Watanabe, S., “Crystallography of Stress-Induced
B2 7R Martensitic Transformation in a Ni-37.0 at.% Al Alloy”, Mater. Trans., JIM, 33(3),
282-288 (1992) (Crys. Structure, Experimental, 25)
[1993Gla] Gladyshevskii, R.E., Cenzual, K., Flack, H.D., Parthé, E., “Structure of RNi3Al9 (R=Y, Gd,
Dy, Er) with either Ordered or Partly Disordered Arrangement of Al-Atom Triangles and
Rare Earth Metal Atoms”, Acta Cryst., B49, 468-474 (1993) (Crys. Structure,
Experimental, 9)
[1994Mur] Murthy, A.S., Goo, E., “Triclinic Ni2Al Phase in 63.1 at.% Al”, Met. Mater. Trans., A,
25A(1), 57-61 (1994) (Crys. Structure, Experimental, 10)
[1995Sor] Sorgic, B., Drasner, A., Blazina, Z., “On the Structural and Thermodynamic Properties of
the DyNi5-xAlx -Hydrogen System”, J. Phys. Condens. Matter., 7, 7209-7215 (1995) (Crys.
Structure, Thermodyn., Experimental, 20)
[1997Ehl] Ehlers,G., Maletta, H., “Frustrated Magnetic Moments in RNiAl Intermetallic Compounds”
Physica B, 234-236, 667-669 (1997) (Crys. Structure, Magn. Prop., Experimental, 4)
[1997Kol] Kolomites, A.V., Havela, L., Yarys, V.A., Andreev, A.V., “Hydrogen
Absorption-Desorption, Crystal Structure and Magnetism in RENiAl Intermetallic
236
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
Compounds and their Hydrides”, J. Alloys Compd., 253-254, 343-346 (1997) (Crys.
Structure, Magn. Prop., Experimental, 13)
[2000Oka] Okamoto, H., “Desk Handbook Phase Diagrams for Binary Alloys, ASM International,
Materials Park, O.H. 44073-0002, (2000) (Equi. Diagram, Review)
[2002Bur] Burzo, E., Chiuzbaian, S.G., Neumann, M., Valeanu, M., Chioncel, L., Creanga, I.,
“Magnetic and Electronic Properties of DyNi5-xAlx Compounds”, J. Appl. Phys. 92(12),
7362-7368 (2002) (Electr. Prop., Experimental, 31)
[2002Dan] Danis, S., Javorsky, P., Rafaja, D., “Magneto-Crystalline Anisotropy in TbPdIn, DyNiAl
and GdNiAl Studied by Using X-ray Powder Diffraction at Low Temperatures”, J. Alloys
Compd., 345, 10-15 (2002) (Experimental, 8)
[2003Gry] Grytsiv, A., “Al-Dy (Aluminium-Dysprosium)”, MSIT Binary Evaluation Program, in
MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; Document ID 20.20073.1.20 (2003) (Crys. Structure, Equi. Diagram,
Assessment, 8)
[2002Lam] Lambrick, D.B., Blazina, Z., Hoon, S.R., “On Magnetic Properties of DyNi5-xAlx (x = 0, 1,
1.5, 2, 2.5, 3) Intermetallics”, J. Mat. Sci. Lett., 21, 807-809 (2002) (Crys. Structure, Magn.
Prop., Experimental, 11)
[2003Sal] Saltykov, P., Cornish, L., Cacciamani, G., “Al-Ni (Aluminium-Nickel)”, MSIT Binary
Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science
International Services GmbH, Stuttgart; to be published, (2003) (Crys. Structure, Equi.
Diagram, Assessment, 164)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
dissolves 0.01 at.% Ni at 639.9°C
[Mas2]
(Ni)
< 1455
cF4
Fm3m
Cu
a = 352.40 at 25°C [Mas2]
dissolves 20.2 at.% Al at 1362°C [Mas2]
~14 at.% at 800°C [2000Oka]
( Dy) hR3
R3m
Sm
a = 343.6
c = 2483
at 25°C, 7.5 GPa
[Mas2]
given as CdCl2-type [Mas2]
given as Sm-type [V-C2]
( Dy)
1412-1381
cI2
Im3m
W
a = 398.0 [Mas2]
( Dy)
< 1381-(-187)
hP2
P63/mmc
Mg
a = 359.15
c = 565.01
[Mas2]
( ’Dy)
<-187
oC4
Cmcm
’Dy
a = 359.5
b = 618.4
c = 567.8
[Mas2]
237
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
DyAl3< 1005
hP16
P63/mcm
TiNi3
a = 609.1
c = 953.3
[V-C2]
DyAl31090-1005
hR60
Rm
HoAl3
a = 608.0
c = 3594.0
[V-C2]
Dy(Al1-xNix)2
DyAl2 < 1500
cF24
Fd3m
MgCu2
a = 784 to 773
a = 783.6
a = 784.0
0 x 0.19 [1970Leo]
0 x 0.22 [1980Ryk]
[2003Gry]
[2003Gry]
DyAl
< 1100
oP16
Pbcm
ErAl
a = 582.2
b = 1137
c = 560.4
a = 582.3
b = 1134
c = 559.3
[2003Gry]
[2003Gry]
Dy3Al2< 1025
tP20
P42/mnm
Zr3Al2
a = 816.7
c = 754.1
a = 820.2
c = 755.4
[2003Gry]
[2003Gry]
Dy2Al
< 990
oP12
Pnma
Co2Si
a = 654.3
b = 507.5
c = 939.7
a = 653.0
b = 507.7
c = 937.6
[2003Gry]
[2003Gry]
Dy3Ni
< 762
oP16
Pnma
Fe3C
a = 685
b = 960
c = 626
[V-C2]
Dy3Ni2< 928
mC20
C2/m
Dy3Ni2
a =1332.1
b = 366.2
c = 951.2
= 105.72°
[V-C2]
DyNi
< 1248
oP8
Pnma
FeB
a = 703
b = 417
c = 544
[V-C2]
DyNi2< 1258
cF24
Fd3m
MgCu2
a = 716 [V-C2]
DyNi3< 1283
hR36
R3m
NbBe3
a = 495.9
c = 2437.9
[V-C2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
238
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
Dy2Ni7< 1307
hP36
P63/mmc
Ce2Ni7
a = 493
c = 2405
[V-C2]
Dy2Ni7< ?
hR54
R3m
Er2Co7
a = 492.8
c = 3618
[V-C2]
DyNi4< 1336
[2000Oka]
Dy4Ni17
< 1352
[2000Oka]
Dy(Ni1-xAlx)5
DyNi5 < 1387
hP6
P6/mmm
CaCu5
a = 489.6
c = 396.5
a = 503.5
c = 403.5
a = 487.56
c = 396.73
0 x 0.4 [1980Ryk]
at 0 at.% Al [1980Ryk]
~30 at.% Al [1980Ryk]
[V-C2]
Dy2(Ni1-xAlx)17
Dy2Ni17
< 1321
hP38
P63/mmc
Th2Ni17 a = 829.9
c = 803.7
0 x 0.04 read from a diagram
[1980Ryk]
[V-C2]
NiAl3< 856
oP16
Pnma
Fe3C
a = 661.3 0.01
b = 736.7 0.01
c = 481.1 0.01
[2003Sal]
Ni2Al3< 1138
hP5
P3m1
Ni2Al3
a = 402.8
c = 489.1
36.8 to 40.5 at.% Ni [Mas2]
[2003Sal]
Ni3Al4< 702
cI112
Ia3d
Ni3Ga4
a = 1140.8 0.01 [V-C2]
NiAl
< 1651
cP2
Pm3m
CsCl
a = 286.0
a = 287
a = 288.72 0.02
a = 287.98 0.02
at 42 to 69.2 at.% Ni [Mas2]
~45 to 60 at.% Ni [2000Oka]
[2003Sal]:
at 63 at.% Ni
at 50 at.% Ni
at 54 at.% Ni
Ni5Al3< 723
oC16
Cmmm
Pt5Ga
a = 753
b = 661
c = 376
63 to 68 at.% Ni [Mas2]
at 63 at.% Ni [2003Sal]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
239
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
Ni3Al
< 1372
cP4
Pm3m
AuCu3 a = 356.77
a = 358.9
a = 356.32
a = 357.92
73 to 76 at.% Ni [Mas2]
[2003Sal]:
at 63 at.% Ni
disordered
ordered
Ni2Al9 mP22
P21/a
Co2Al9
a = 868.5 0.06
b = 623.2 0.06
c = 618.5 0.04
= 96.50 0.05°
Metastable
[2003Sal]
NixAl1-x tP4
P4/mmm
AuCu
m**
a = 383.0
c = 320.5
a = 379.5
c = 325.6
a = 379.5
c = 325.6
a = 375.1
c = 330.7
a = 379.9 to 380.4
c = 322.6 to 323.3
a = 371.7 to 376.8
c = 335.3 to 339.9
a = 378.00
c = 328.00
a = 418
b = 271
c = 1448
= 93.4°
Martensite, metastable; 0.60 < x < 0.68
[2003Sal]:
at 62.5 at.% Ni,
at 63.5 at.% Ni,
at 66.0 at.% Ni,
at 64 at.% Ni,
at 65 at.% Ni,
[1992Mur]
Ni2Al hP3
P3m1
CdI2
aP126
P1
a = 407
b = 499
a = 1252
b = 802
c = 1526
= 90°
= 109.7°
= 90°
Metastable
[2003Sal]
[1994Mur]
D1 Decagonal
Metastable, [2003Sal]
D4 Decagonal
Metastable, [2003Sal]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
240
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
* 1, DyNi3Al16 oC*
Cmcm
a = 402.1
b = 1586
c = 2701
[1980Ryk]
* 2, DyNi3Al9 hR78
R32
ErNi3Al9
a = 727.23 ± 0.09
c = 2734.4 ± 0.06
[1993Gla]
with partly disordered arrangement of Al
and Dy atoms
* 3, DyNi2Al3 hP18
P6/mmm
YNi2Al3
or hP18
Ho2Ni5Ga5
a = 892
c = 393.6
a = 903
c = 407
[1973Ryk, 1980Ryk]
[1981Zar]
according to
[2002Bur]
* 4, Dy2Ni3Al7 hP* a =1782
c = 398.8
[1973Ryk, 1980Ryk, 1981Zar]
* 5, DyNiAl4 oC24
Cmcm
YNiAl4
a = 405.6
b = 1513
c = 663
[1973Ryk, 1980Ryk, 1981Zar]
* 6, Dy3Ni8Al hP24
P63/mmc
Ce3Co8Si
a = 503.7
c =1610
[1973Ryk, 1980Ryk, 1982Rom2]
* 7, DyNiAl2 oC16
Cmcm
CuMgAl2(ord. Re3B)
a = 407.7
b = 1008
c = 693
a = 408
b =1015
c = 688
[1973Ryk, 1980Ryk]
[1982Rom1]
* 8, Dy3Ni6Al2 cI44
Im3m
Ce3Ni6Si2(ord. Ca3Ag8)
a = 891 [1980Ryk]
* 9, Dy(Ni1-xAlx)2
DyNiAl (I)
hP9
P62m
ord. Fe2P
or ZrNiAl
a = 699.39
c = 384.70
a = 699.4
c = 382.1
0.44 x 0.52 [1970Leo]
[1973Oes]
[1980Ryk]
* 10, Dy2Ni2Al oI10
Immm
Mo2NiB2
a = 538.8
b = 833.3
c = 417.3
a = 833.8
b = 538.8
c = 417.3
[1980Ryk, 1982Rom2]
[V-C2]
* 11, DyNiAl (II) hP12
P63/mmc
MgZn2
a = 538.3
c = 854.9
[1987Tsv1] and [1987Tsv2]
high pressure phase
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
241
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Dy–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Dy Ni
Al Data / Grid: at.%
Axes: at.%
Ni3Al
NiAl
Ni2Al3
NiAl3
DyAl3
DyAl2
Dy2Ni17
DyNi5Dy2Ni7
DyNi3DyNi2
τ1
τ5
τ3
τ4
τ7
τ9
τ10 τ8
τ6
L
τ2
(Ni)
Fig. 1: Al-Dy-Ni.
Partial isothermal
section up to 33 at.%
Dy at 800°C
242
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Fe
Aluminium – Erbium – Iron
Bernd Grieb, updated by Alexander Pisch
Literature Data
Two ternary phases were observed besides solid solutions based on binary compounds. The ternary phase
ErFeAl [1971Oes1, 1971Oes2, 1973Zar] and the section along ErAl2-ErFe2 [1971Oes2, 1973Zar, 1974Oes,
1975Dwi, 1977Gua] are well investigated regarding structural and magnetic properties. The structural and
magnetic properties of ErFe4+xAl8-x have been studied at x=0 [1973Zar, 1974Viv, 1976Bus, 1988Sch,
1995Cac, 1998Hag], x=2 [1981Fel, 1988Che, 1998Sch] and x=3 [2000Sch, 2001Sch] using X-ray and
neutron diffraction. Magnetic properties were studied as a function of temperature and composition by the
Faraday method and by SQUID/Vibrating Sample magnetometer. Stoichiometric samples have been
prepared by arc melting of the elements in argon atmosphere and subsequent anneal at 850°C for 10-30d
(ErFe7Al5) [2000Sch] or 800°C for 7d (ErFe6Al6) [1998Sch]. [1998Hag] measured the specific heat from
1.5K to 200K on ErFe7Al5 samples prepared in an arc furnace in reduced Ar atmosphere starting from the
elements (purity > 99.9 mass%) followed by a vacuum anneal at 800°C for several weeks. The
Er2(Fe1-xAlx)17 solid solution has been studied using X-ray and neutron diffraction [1992Jac, 1996Cha,
1998Che, 1998Wan, 2001Yan]. Samples were prepared by arc melting from the pure elements (99.9 mass%
purity) and annealed at 1127°C for 120h followed by a water quench [1998Che],1100°C for 24h [1996Cha],
900°C for 10h [1998Wan] or 500°C for 720h [2001Yan]. In order to determine the exact phase limits,
[2001Yan] varied the Er content from 5 to 15 at.% and an isothermal section at 500°C in the Fe-rich corner
has been constructed based on the XRD results. The magnetic intersublattice constant JErFe for
Er2(Fe1-xAlx)17 has been determined as function of the composition by the high field powder method
(HFFO) by [1994Liu]. [1998Thi] studied the structure and magnetic properties of ErFe2Al10 by X-ray
diffraction and SQUID magnetometry. The sample has been prepared slightly Al-rich by melting the
elements (Fe: 99.5 mass%, Er, Al 99.9 mass%) in Al2O3 crucibles which were sealed in quartz tubes and
annealed for 400h at 800°C. The remaining Al has been removed by hydrochloric acid. [1972Zar] presented
an isothermal section up to 33.3 at.% Er which was investigated by means of X-ray and microscopic
analysis.
Binary Systems
The binary Al-Fe system is taken from [2003Pis], Er-Fe and Al-Er are accepted from [Mas]. Er-Fe from
[1972Zar] is not in agreement with [Mas] because the ErFe3 compound has been neglected.
Solid Phases
The ternary Laves phase ErFeAl ( 3) has the MgZn2 structure and is different from the solid solutions of
the two binary compounds ErAl2 and ErFe2 which crystallize in the MgCu2 prototype. The homogeneity
ranges of theses two binary intermetallics have been determined by [1971Oes2, 1974Oes] and are in good
agreement with the results of [1975Dwi]. The second known ternary phase ErFe4+xAl8-x ( 4) has the
ThMn12 structure [1976Bus]. Aluminium can be substituted by Fe at least up to x=2 [1981Fel, 1988Che,
1998Sch]. Lattice parameters for ErFe4Al8 [1974Viv, 1976Bus, 1988Sch, 1995Cac] are in good agreement.
The Er2(Fe17-xAlx) solid solution crystallizes in different crystallographic structures: hexagonal Th2Ni17 for
0 < x < 4 (0 to 21 at.% Al) and rhombohedral Th2Zn17 for 4 < x < 9 (21 to 47.4 at.% Al) assuming a
stoichiometric Er content (10.5 at.%) and after annealing at 1100/1127°C [1996Cha, 1998Che]. Annealing
at 500°C stabilizes a new TbCu7 type structure around 27 at.% Al [2001Yan], the hexagonal variant being
stable from 0 to 25 at.% Al and the rhombohedral from 30 to 37 at.% Al. [2001Yan] investigated also lower
and higher Er contents leading to the hexagonal type from 0 to 27 at.% Al, TbCu7 type from 30 to 32 at.%
Al and rhombohedral from 35 to 40 at.% Al for an Er content of 9.5 at.% and only rhombohedral from 22
243
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Fe
to 35 at.% Al for an Er-content of 11.5 at.%. The lattice parameters from [1992Jac, 1996Cha, 1998Che,
2001Yan] are in good agreement. The ternary phase ErFe2Al10 ( 5) has a YbFe2Al10 prototype structure
[1998Thi]. Details of crystal structure of solid phases are given in Table 1.
Isothermal Sections
An isothermal section up to 33.3 at.% Er based on the work of [1972Zar, 2001Yan] is reproduced in Fig. 1.
The homogeneity ranges of the MgCu2 and MgZn2 types given by [1972Zar] have been corrected to be in
agreement with [1975Dwi] and [1974Oes].
Notes on Materials Properties and Applications
The magnetic coupling constants for Er2Fe10Al7 / Er2Fe9Al8 at 4.2K are nRT=2.27 / 2.54 (Tf.u./ B) and JRT/
k = -8.16/-9.16 K [1992Jac]. Er2Fe15Al2 has a Curie temperature of 383K [1998Wan]. ErFe6Al6 presents a
paramagnetic to ferrimagnetic phase transition at 340K [1998Sch]. ErFe2Al10 ( 5) has probably a
metamagnetic type behavior with a Néel temperature below 15K and an effective magnetic moment of
9.5(1) B [1998Thi].
References
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-Rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids, 6, 16-37 (1958) (Crys. Structure,
Experimental, 49)
[1961Lih] Lihl, F., Ebel, H., “X-Ray Examination of the Constitution of Iron-Rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenwesen, 32, 483-487, (1961)
(Crys. Structure, Experimental, 12)
[1971Oes1] Oesterreicher, H., “Structural Studies of Rare Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Experimental, Crys. Structure, 6)
[1971Oes2] Oesterreicher, H., “Structural and Magnetic Studies on ErFe2-ErAl2”, J. Appl. Phys., 42,
5137-5143 (1971) (Experimental, Crys. Structure, 31)
[1972Zar] Zarechnyuk, O.S., Vivchar, O.I., Ryabov, V.R., “An X-ray Study of the Er-Fe-Al System
for Er Contents up to 33.3 at.%” (in Russian), Vestn. L'vov Univ., Ser. Khim., 14, 16-19
(1972) (Experimental, Crys. Structure, Equi. Diagram, #, 9)
[1973Zar] Zarechnyuk, O.S., Rikhal' R.M., Vivchar, O.I., “Laves Phases in Ternary Systems of the
Type Rare Earth Metal - Transition Metal - Al” (in Russian), Akad. Nauk Ukr. SSR,
Metallofizika., 46, 92-94 (1973) (Experimental, Crys. Structure, 22)
[1974Oes] Oesterreicher, H., “Constitution of Al Base Rare Earth Alloys RT2-RAl2 (R = Pr, Gd, Er; T
= Mn, Fe, Co, Ni, Cu)”, Inorg. Chem., 13, 2807-2811 (1974) (Experimental, Crys.
Structure, 30)
[1974Viv] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12- Type Structure in R-Fe-Al
Systems” (in Russian), Tezisy. Dokl. Vses. Konf. Kristallokhim. Intermet. Soedin., Rykhal,
R.M., (Ed.), L'vov. Gos. Univ.: Lvov, 2nd, 41, (1974) (Experimental, Crys. Structure, 0)
[1975Dwi] Dwight, A.E., Kimball, C.W., Preston, R.S., Taneja S.P., Weber, L., “Crystallographic and
Mössbauer Study of (Sc, Y, Ln) (Fe, Al)2 Intermetallic Compounds”, J. Less-Common Met.,
40, 285-291 (1975) (Experimental, Crys. Structure, 8)
[1976Bus] Buschow, K.H.J., van Vucht J.H.N., van Den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth-3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Experimental, Crys. Structure, 2)
[1977Gua] Gualtieri, D.M., Wallace, W.E., “Hydrogen Capacity and Crystallography of ErFe2-Based
and ErCo2-Based Ternary Systems”, J. Less-Common Met., 55, 53-59 (1977)
(Experimental, Crys. Structure, 4)
244
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Fe
[1981Fel] Felner, I., Seh, M., Rakavy, M., Nowik, I., “Magnetic Order and Hyperfine Interactions in
RFe6Al6 (R = Rare Earth)”, J. Phys. Chem. Solids, 42, 369-377 (1981) (Experimental, Crys.
Structure, 6)
[1988Che] Chelkowska, G., Chelkowska, A., Winiarska, A., “Magnetic Susceptibility and Structural
Investigations of Rare Earth- Aluminium-Iron (REAl6Fe6) Compounds for RE = Yttrium,
Terbium, Dysprosium, Holmium, and Erbium”, J. Less-Common Met., 143, L7-L10 (1988)
(Experimental, Crys. Structure, 12)
[1988Gsc] Gschneidner Jr, K.A., Calderwood, F.W., “The Al-Er (Aluminum-Erbium) System”, Bull.
Alloy Phase Diagrams, 9, 676-678 (1988) (Equi. Diagram, Review, 29)
[1988Sch] Schaefer, W., Groenefeld, M., Will, G., Gal, J., “Magnetic Helical Ordering in Intermetallic
Rare Earth-Iron-Aluminum Compounds”, Mater. Sci. Forum, 27-28, 243-248 (1988)
(Experimental, Crys. Structure, 9)
[1989Kuz] Kuz'ma, Yu.B., Pan'kiv, T.V., “X-Ray Structural Study of the Er-Cu-Al System”, Russ.
Metall., (3), 208-210 (1989), translated from Izv. Akad. Nauk SSSR Met., (3), 218-219
(1989) (Equi. Diagram, Crys. Structure, Experimental, 5)
[1992Jac] Jacobs, T.H., Buschow, K.H.J., Zhou, G.F., de Boer, F.R., “Intersublattice Interactions in
R2Fe17-xAlx Compounds (R = Tb, Dy, Er and Tm)”, Physica B, (Amsterdam), 179(3),
177-183 (1992) (Abstract, Crys. Structure, Magn. Prop., 15)
[1994Liu] Liu, J.P., de Boer, F.R., de Chatel, P.F., Coehoorn, R.,Buschow, K.H.J., “On the 4f-3d
Exchange Interaction in Intermetallic Compounds”, J. Magn. Magn. Mater., 132, 159-179
(1994) (Magn. Prop., Review, 64)
[1995Cac] Caciuffo, R., Amoretti, G., Buschow, K.H.J., Moze, O., Murani, A.P., Paci, B., “Neutron
Spectroscopy Studies of the Crystal-field Interaction in RET4 Al8 Compounds (RE=Tb, Ho
or Er; T=Mn, Fe or Cu)”, J. Phys.: Condensed Matter, 7, 7981-7989 (1995) (Crys. Structure,
Experimental, 23)
[1996Cha] Chang W.C., Lu S.L., Chen S.K., Yao Y.D., “Structural and Magnetic Studies of
Er2Fe17-xMxCy (M=Ga and Al)”, J. Appl. Phys., 79(8), 5533-5535 (1996) (Crys. Structure,
Experimental, 9)
[1997Kog] Kogachi, M., Haraguchi, T., “Quenched-in Vacansies in B2-Structured Intermetallic
Compound FeAl”, Mater. Sci. Eng. A, A230, 124-131 (1997) (Crys. Structure,
Experimental, 23)
[1998Che] Cheng, Z., Shen, B., Yan, Q., Guo, H., Chen, D., Gou, C., Sun, K., de Boer, F.R., Buschow,
K.,H.J., “Structure, Exchange Interactions, and Magnetic Phase Transition of Er2Fe17-xAlxIntermetallic Compounds”, Phys. Rev. B, 57(22), 14299-14309 (1998) (Crys. Structure,
Experimental, 35)
[1998Hag] Hagmusa I.H., Brueck E., de Boer F.R., Buschow K.H.J., “Magnetic Properties of RFe4Al8Compounds Studied by Specific Heat Measurements”, J. Alloys Compd., 278, 80-82 (1998)
(Experimental, Magn. Prop., 9)
[1998Sch] Schaefer, W., Kockelmann, W., Jansen, E., Fredo, S., Gal, J., “Structural Characteristics of
Rare Earth (R = Tb, Ho, Er) Ternary Magnetic Intermetallics RFexAl12-x with Iron
Concentrations x = 6”, Mater. Sci. Forum, 278-281, 542-547 (1998) (Crys. Structure,
Experimental, 14)
[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10
(Ln = Y,La-Nd,Sm,Cd-Lu and T = Fe,Ru,Os) with YbFe2Al10 Type Structure and Magnetic
Properties of the Iron-Containing Series”, J. Mater. Chem., 8(1), 125-130 (1998) (Crys.
Structure, Experimental, Magn. Prop., 31)
[1998Wan] Wang, J., de Boer, F.R., Zhang, C., Brueck, E., Tang, N., Yang, F., “Structural and Magnetic
Properties of Er2Fe15M2 Compounds with M = Mn, Fe, Ni, Al, Ga and SI”, J. Magn. Magn.
Mater., 185, 345-352 (1998) (Crys. Structure, Experimental, Magn. Prop., 20)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-Rich Fe-Al
Alloys”, Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 15)
245
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Fe
[2000Sch] Schaefer, W., Barbier, B., Halevy, I., “ThMn12-Type Magnetic ErFe7Al5 and
Non-Magnetic YFe7Al5 Studied by X-ray and Neutron Diffraction”, J. Alloys Compd.,
303-304, 270-275 (2000) (Crys. Structure, Experimental, Magn. Prop., 7)
[2001Sch] Schaefer, W., Halevy, I., “Neutron Powder Diffraction of Iron-Rich Rare
Earth-Iron-Aluminium Intermetallics RFe7Al5 (R = Tb, Dy, Ho, Er)”, Mater. Sci. Forum,
378-381, 414-419 (2001) (Crys. Structure, Experimental, Magn. Prop., 12)
[2001Ike] Ikeda, O.,Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
BCC Phases in the Fe-Rich Portion of hte Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Equi. Diagram, Experimental, Mechan. Prop., 18)
[2001Yan] Yanson, T., Manyako, M., Bodak, O., Cerny, R., Yvon, K., “Effect of Aluminium
Substitution and Rare-Earth Content on the Structure of R2(Fe1-xAlx)17 (R = Tb,Dy, Ho, Er)
Phases”, J. Alloys Compd., 320(1), 108-113 (2001) (Crys. Structure, Equi. Diagram,
Experimental, 9)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, 58)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
( Fe)
1538-1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)
< 1394-912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2] dissolves up to
1.2 at.% Al
( Fe)
< 912
cI2
Im3m
W
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
at 25°C [Mas2]
dissolves up to 45.0 at.% Al at 1310°C
0-18.8 at.% Al, HT [1958Tay]
0-19.0 at.% Al, HT [1961Lih]
0-18.7 at.% Al, 25°C [1999Dub]
(Er)
< 1529
hP2
P63/mmc
Mg
a = 355.92
c = 558.50
at 25°C [Mas2]
ErAl3< 1070
cP4
Pm3m
AuCu3
a = 421.4 [1988Gsc]
246
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Fe
ErAl2< 1455
ErCuxAl2-x
cF24
Fd3m
Cu2Mg a = 779.3
a = 773.7
0 x 0.38 (~19 at.% ErCu2) at 600°C
[1989Kuz]
at x = 0 [1988Gsc, 1989Kuz]
at x = 0.38 [1989Kuz]
ErAl
< 1140
oP16
Pbcm
ErAl
a = 580.1
b = 1127
c = 557.0
[1988Gsc]
Er3Al2< 1060
tP20
P42/mnm
Gd3Al2
a = 812.3
c = 748.4
[1988Gsc]
Er2Al
< 1040
oP12
Pnma
Co2Si
a = 651.6
b = 501.5
c = 927.9
[1988Gsc]
Fe3Al14
< 1160
mC102
C2/m
Fe3Al14
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7 to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
74.16-76.70 at.% Al [2003Pis]
sometimes called FeAl3 in the literature
at 76.0 at.% Al [2003Pis]
Fe2Al5< 1169
oC24
Cmcm
-
a = 765.59
b = 641.54
c = 421.84
at 71.5 at.% Al [2003Pis]
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [2003Pis]
1102 - 1232
cI16?
-
a = 598.0 at 61 at.% Al [2003Pis]
FeAl
< 1310
cP2
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5 - 47.5 at.% Al [1961Lih]
36.2 - 50.0 at.% Al [1958Tay]
39.7 - 50.9 at.% Al [1997Kog] 500°C
quenched in water
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
~24 - ~37 at.% Al [2001Ike]
23.1 - 35.0 at.% Al [1958Tay]
24.7 - 31.7 at.% Al [1961Lih]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [2003Pis]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
247
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Fe
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
metastable
85.7 at.% Al [2003Pis]
[2003Pis]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[2003Pis]
Er(FexAl1-x)2
ErAlr
cF24
Fd3m
MgCu2 a = 779.2
0 x 0.333 [1971Oes2]
(0 to 22.2 at.% Fe)
[V-C]
Er(Fe1-xAlx)2
ErFer
cF24
Fd3m
MgCu2 a = 728.3
0 x 0.363 [1971Oes2]
(0 to 24.2 at.% Al)
[V-C]
Er6(Fe1-xAlx)23 cF116
Fm3m
Th6Mn23
a = 1203 ± 2
a = 1213 ± 2
0 x 0.37 [1972Zar]
at x = 0, Er6Fe23
at Er6Fe14.5Al8.5
Er2(Fe1-xAlx)17
Er2Fe17
hP38
P63/mmc
Th2Ni17 a = 844 ± 2
c = 827 ± 2
a = 847.7
c = 830.3
a = 851.1
c = 831.9
a = 853.5
c = 833.9
0 x 0.3 at 9.5 at.% Er [2001Yan]
0 x 0.28 at 10.5 at.% Er [2001Yan]
at x = 0,
at Er2Fe16Al1 [1998Che]
at Er2Fe15Al2 [1998Che]
at Er2Fe14Al3 [1998Che]
* 1
Er2(Fe1-xAlx)17
hP*
P6/mmm
TbCu7
0.335 x 0.358 at 9.5 at.% Er;
x = 0.3 at 10.5 at.% Er [2001Yan]
* 2
Er2(Fe1-xAlx)17
hR57
R3m
Th2Zn17
a = 859.0
c = 1253.2
a = 861.8
c = 1257.6
a = 866.7
c = 1260.3
a = 871.0
c = 1262.2
a = 875.5
c = 1265.5
a = 878.2
c = 1273.1
0.39 x 0.45 at 9.5 at.% Er [2001Yan]
0.335 x 0.414 at 10.5 at.% Er;
0.246 x 0.391 at 11.5 at.% Er;
at Er2Fe13Al4 [1998Che]
at Er2Fe12Al5 [1998Che]
at Er2Fe11Al6 [1998Che]
at Er2Fe10Al7 [1998Che]
at Er2Fe9Al8 [1998Che]
at Er2Fe8Al9 [1998Che]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
248
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Fe
* 3,
Er(Fe1-xAlx)2
ErFeAl
hP12
P63/mmc
MgZn2
a = 538.4
c = 870.7
0.382 x 0.645 [1971Oes2]
(41.2 to 23.7 at.% Fe,
25.5 to 43.0 at.% Al)
at x = 0.5 [1971Oes2, 1975Dwi]
* 4,
ErFe4+xAl8-x tI26
I4/mmm
ThMn12
a = 870.4
c = 503.8
a = 861.1
c = 501.1
a = 859.4(1)
c = 598.1(1)
0 x 1.6 [1972Zar]
at x = 0, ErFe4Al8 [1976Bus]
at x = 2, ErFe6Al6 [1988Che]
at x = 3, ErFe7Al5 [2001Sch] and 20°C
* 5, ErFe2Al10 oC36
YbFe2Al10
a = 895.8 ± 0.2
b = 1013.6 ± 0.3
c = 898.8 ± 0.3
[1972Zar]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
20
40
60
80
20 40 60 80
20
40
60
80
Er Fe
Al Data / Grid: at.%
Axes: at.%
τ4
Fe4Al13Fe2Al5
FeAl2
FeAl
ErFe3Er2(Fe1-xAlx)17
Er(FexAl1-x)2
Er(Fe1-xAlx)2
τ5
ErAl3
τ1
τ2τ3
Fe3Al
(αFe)
(Al)
Er6(Fe1-xAlx)23
Fig. 1: Al-Er-Fe.
Isothermal section at
500°C
249
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
Aluminium – Erbium – Nickel
Riccardo Ferro, Gilda Zanicchi, Rinaldo Marazza
Literature Data
Investigations have been carried out on the intermediate phases, their crystal structures [1968Dwi,
1973Ryk, 1974Oes, 1981Zar, 1982Rom2, 1987Tsv2, 1998Jav], magnetic properties [1970Leo, 1972Oes,
1973Oes, 1982Rom1, 1996Jav, 2002Jav], and hydrogen absorption characteristics [1978Tak, 1996Sor].
Most of the samples were annealed at temperatures between 600 and 900°C.
An investigation of the section ErNi2-ErAl2 was carried out by [1970Leo] who investigated structural and
magnetic properties of the ErNiAl intermediate phase together with the mutual solubility of ErNi2 - and
ErAl2. A systematic investigation of phase equilibria at 800°C and in the range of 0 to 33 at.% Er was made
by [1982Zar]. In this study, 49 alloys were prepared from 99.98Al, 99.9Ni and 99.6 mass% Er by arc
melting under purified argon. The alloys were annealed at 800°C for 700 h and then quenched in ice-water.
A high pressure modification of ErNiAl (MgZn2 type) has been prepared from the powder components at
1450 to 1500°C at a pressure of 7.7 GPa [1987Tsv1]. The same information is also given in [1987Tsv2].
Gladyshevskii et al. [1993Gla] determined the structure of the ErNi3Al9 compound which crystallizes in the
rhombohedral hR78 - ErNi3Al9 type. The present evaluation updates and completes the evaluation made
earlier by [1991Fer] in the MSIT Evaluation Program.
Binary Systems
The present evaluation of ternary data is consistent with the description of the edge binary Al-Er by
[2003Ria], the Er-Ni by [2000Oka] and the Al-Ni diagram as published by [2003Sal] except for the fact that
the phases Er5Ni22, Er4Ni17 and ErNi4 listed by [2000Oka] are omitted as they could not been detected by
[1982Zar].
Solid Phases
Special attention was dedicated to the 0 to 33 at.% Er composition range. Several solid phases pertaining to
this composition field have been described. Their structural properties are summarized in Table 1. For the
ErNi2 - based phase, a solubility of 8.5 mole% ErAl2 was proposed by [1970Leo] in the investigation of the
system ErNi2-ErAl2, however, the negligible solubility suggested by [1982Zar] is presented in Fig. 1.
Magnetic properties of the two terminal solid solutions are given for various compositions by [1970Leo].
According to [1973Oes] and [1982Zar] ErNiAl ( 9) is a point phase. However, [1970Leo] found a range of
homogeneity between 50 and 60 mole% ErAl2.
Isothermal Sections
The partial isothermal section at 800°C, given in Fig. 1, is mainly based on the data of [1982Zar] who used
long homogenizing annealing periods, followed by quenching in cold water. However, [1982Zar] did not
report in his work the ErNi3Al9 phase identified later by [1993Gla]. We introduced this phase in Fig. 1 as
2 with possible tie-lines. The equilibria with the melt in the Al corner have not been investigated.
[1996Sor] investigated the substitution of aluminium for nickel. Nickel may be replaced by aluminium up
to the composition ErNi3Al2 without changing the crystal prototype, i.e. the CaCu5 type structure. However
beyond this composition and up to ErNi2Al3 exists a ternary single phase with a structure of the YCo3Ga2
type (possibly a high temperature phase: the alloys were annealed at about 1000°C).
Miscellaneous
Magnetic properties of the Al-Er-Ni alloys, and more generally of Al-Ni-Rare Earth alloys, have been
discussed in several papers. [1970Leo] studied RNi2-xAlx alloys; Er2Ni2Al and ErNiAl2 have been studied
250
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
by [1982Rom1, 1982Rom2]. Hydrogen adsorption in RNi4Al alloys has been studied by [1978Tak].
[1996Jav] studied polycrystalline samples of ErNiAl by powder neutron diffraction and by susceptibility
measurements. [1996Sor] investigated the substitution of aluminium for nickel and its effect on the
structural and hydrogen absorption properties of ErNi5-xAlx system. It was found that all ternary alloys
having the CaCu5 structure absorb between 1.95 and 2.95 hydrogen atoms per formula unit at room
temperature. These authors reported also crystallographic and thermodynamic data for ErNi5-xAlx-
hydrogen system .
[1997Kol] studied hydrogen absorption-desorption, crystal structure and magnetism in intermetallic
compounds of the series RNiAl (R = Y, Gd, Tb, Dy, Er, Lu). These compounds, crystallizing in the ZrNiAl
type of crystal structure, form hydrides containing up to 1.4 H by formula unit and the hydrogenation leads
to a drastic reduction of the magnetic ordering temperatures.
[1998Jav] presented an inelastic neutron scattering study of the crystal field in the ErNiAl intermetallic
compound. The results were compared with the specific heat data and the lower portion of the crystal-field
energy level scheme was determined.
[2002Jav] presented a study of the crystal field and electronic structure in an ErNiAl intermetallic alloy
based on inelastic neutron spectroscopy, magnetic susceptibility, specific heat data and first-principles
density-functional calculations.
References
[1968Dwi] Dwight, A.E., Mueller, M.H., Conner, R.A., J.R., Downey, Knott, H., “Ternary Compounds
with the Fe2P-Type Structure”, Trans. Met. Soc. AIME, 242, 2075-2080 (1968) (Crys.
Structure, Experimental, 14)
[1970Leo] Leon, B., Wallace, W.E., “Magnetic and Structural Characteristics of Intermetallic Systems
Containing Lanthanides”, J. Less-Common Met., 22, 1-10 (1970) (Crys. Structure,
Experimental, 13)
[1972Oes] Oesterreicher, H., “Metamagnetism in ErNiAl and TmNiAl”, Phys. Status Solidi A, 12,
K109-K110 (1972) (Experimental, 2)
[1973Oes] Oesterreicher, H., “Structural and Magnetic Studies on Rare Earth Compounds RNiAl and
RCuAl”, J. Less-Common Met., 30, 225-236 (1973) (Crys. Structure, Experimental, Magn.
Prop., 21)
[1973Ryk] Rykhal, R.M., Zarechnyuk, O.S., Pyshchik, G.V., “New Representatives of MgCuAl2 and
YNiAl2 Structural Types” (in Ukrainian), Dop. Akad. Nauk Ukr. RSR. Ser. A, Fiz.-Mat.
Tekh. Nauki, 35(6), 568-570 (1973) (Crys. Structure, Experimental, 2)
[1974Oes] Oesterreicher, H., “Constitution of Aluminum Base Rare Earth Alloys RT2-RAl2 (R = Pr,
Gd, Er; T = Mn, Fe, Co, Ni, Cu)”, Inorg. Chem., 13, 2807-2811 (1974) (Crys. Structure,
Equi. Diagram, Experimental, 30)
[1978Tak] Takeshita, T., Malik, S.K., Wallace, W.E., “Hydrogen Absorption in RNi4Al (R = Rare
Earth) Ternary Compounds”, J. Solid State Chem., 23, 271-274 (1978) (Crys. Structure,
Experimental, 8)
[1981Zar] Zarechnyuk, O.S., Rykhal, R.M., “The Crystal Structure of the YNi2Al3 Compound and its
Related Phases” (in Russian), Vestn. L'vov. Univ., Ser. Khim., 23, 45-47 (1981) (Crys.
Structure, Experimental, 6)
[1982Rom1] Romaka, V.A., Zarechnyuk, O.S., Rykhal, R.M., Yarmolyuk, Ya.P., Skolozdra, R.V.,
“Magnetic Susceptibility and Crystal Structure of RNiAl2 Compounds”, Phys. Met.
Metallogr., 54(2), 191-193 (1982), translated from Fiz. Met. Metalloved., 54, 410-412
(1982) (Crys. Structure, Experimental, 6)
[1982Rom2] Romaka, V.A., Grin, Yu.A., Yarmolyuk, Ya.P., Zarechnyuk, O.S., Skolozdra, R.V.,
“Magnetic and Crystallographic Parameters of R2Ni2Ga and R2Ni2Al Compounds”, Phys.
Met. Metallogr., 54(4), 58-64 (1982), translated from Fiz. Met. Metalloved., 54, 691-696
(1982) (Crys. Structure, Experimental, 13)
251
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
[1982Zar] Zarechnyuk, O.S., Rykhal, R.M., Romaka, V.A., Kovalska, O.K., Shazabura, G.I.,
“Isothermal Sections of the Holmium, Erbium-Nickel-Aluminium Ternary Systems at
800°C in the 0 to 0.333 Atomic Fraction Range of the Rare-Earth Metal” (in Ukrainian),
Dop. Akad. Nauk Ukr. RSR, Ser. A, Fiz.-Mat. Tekh. Nauki, (1), 81-83 (1982) (Crys.
Structure, Equi. Diagram, Experimental, #, *, 11)
[1986Hua] Huang, S.C., Briant, C.L., Chang, K.-M., Taub, A.I., Hall, E.L., “Carbon Effects in Rapidly
Solidified Ni3Al”, J. Mater. Res., 1(1), 60-67 (1986) (Experimental, Mechan. Prop., 27)
[1987Tsv1] Tsvyashchenko, A.V., Fomicheva, L.N., “Crystallization of the Laves Phases RNiAl (C14
Type) at High Pressure”, J. Less-Common Met., 135, L9-L12 (1987) (Crys. Structure,
Experimental, 10)
[1987Tsv2] Tsvyashchenko, A.V., Fomicheva, L.N., “New Polymorphic Modifications of the
Compounds RTAl (R = Rare Earth Metal, T = Cu, Ni)”, Inorg. Mater., 23, 1024-1027
(1987), translated from Izv. Akad. Nauk SSSR, Neorg. Mater., 23, 1148-1152 (1987) (Crys.
Structure, Experimental, 15)
[1988Li] Li, F., Ardell, A.J., “The Incoherent / ' Solvus in Ni-Al Alloys”, J. Phase Equilib., 19(4),
334-339 (1998) (Equi. Diagram, Theory, Calculation, 25)
[1989Ell] Ellner, M., Kek, S., Predel, B., “Ni3Al4 - A Phase with Ordered Vacancies Isotypic to
Ni3Ga4”, J. Less-Common Met., 154(1), 207-215 (1989) (Experimental, Crys. Structure, 26)
[1991Fer] Ferro R., Zanicchi, G., Marazza, R., ”Al-Er-Ni (Aluminium - Erbium - Nickel),” MSIT
Ternary Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials
Science International Services GmbH, Stuttgart; Document ID: 10.13103.1.20, (1991)
(Crys. Structure, Equi. Diagram, Assessment, 15)
[1991Kim] Kim, Y.D., Wayman, C.M., “Transformation and Deformation Behavior of Thermoelastic
Martensite Ni-Al Alloys Produced by Powder Metallurgy Method” (in Korean), J. Korean
Inst. Met. Mater., 29(9), 960-966 (1991) (Mechan. Prop., Experimental, 15)
[1992Mur] Murakami, Y., Otsuka, K., Hanada, S., Watanabe, S., “Crystallography of Stress-Induced
B2→7R Martensitic Transformation in a Ni-37.0 at.% Al Alloy”, Mater. Trans., JIM, 33(3),
282-288 (1992) (Crys. Structure, Experimental, 25)
[1993Gla] Gladyshevskii, R.E., Cenzual, K., Flack, H.D., Parthé, E., “Structure of RNi3Al9 (R = Y,
Gd, Dy, Er) with Either Ordered or Partly Disordered Arrangement of Al-Atom Triangles
and Rare-Earth-Metal Atoms”, Acta Crystallogr., Sect. B: Struct. Cystallogr. Cyst. Chem.,
B49, 468-474 (1993) (Crys. Structure, Experimental, 9)
[1993Kha] Khadkikar, P.S., Locci, I.E., Vedula, K., Michal, G.M., “Transformation to Ni5Al3 in a
63.0 at.% Ni-Al Alloy”, Metall. Trans. A, 24A, 83-94 (1993) (Equi. Diagram, Crys.
Structure, Experimental, 28)
[1994Mur] Murthy, A.S., Goo, E., “Triclinic Ni2Al Phase in 63.1 at.% NiAl”, Metal. Mater. Trans. A,
25A(1), 57-61 (1994) (Crys. Structure, Experimental, 10)
[1996Jav] Javorsky, P., Burlet, P., Ressouche, E., Sechovsky, V., Michor, H., Lapertot, G., “Magnetic
Structure Study of ErCuAl and ErNiAl”, Physica B, 225 230-236, (1996) (Crys. Structure,
Magn. Prop., Experimental, 16)
[1996Pau] Paufler, P., Faber, J., Zahn, G., “X-Ray Single Crystal Diffraction Investigation on
Ni1+xAl1-x”, Acta Crystallogr., Sect. A: Found. Crystallogr., A52, C319 (1996) (Crys.
Structure, Experimental, Abstract, 3)
[1996Sor] Sorgic, B., Drasner, A., Blazina, Z., “The Effect of Aluminium on the Structural and
Hydrogen Sorption Properties of ErNi5”, J. Alloys Compd., 232, 79-83 (1996) (Crys.
Structure, Experimental, Equi. Diagram, 22)
[1996Vik] Viklund, P., Häußermann, U., Lidin, S., “NiAl3: a Structure Type of its Own?”, Acta
Crystallogr., Sect. A: Found. Crystallogr., A52, C-321 (1996) (Crys. Structure,
Experimental, Abstract, 0)
[1997Bou] Bouche, K., Barbier, F., Coulet, A., “Phase Formation During Dissolution of Nickel in
Liquid Aluminium”, Z. Metallkd., 88(6), 446-451 (1997) (Thermodyn., Experimental, 15)
252
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
[1997Kol] Kolomites, A.V., Havela, L., Yarys, V.A., Andreev, A.V., “Hydrogen Absorption-
Desorption, Crystal Structure and Magnetism in RENiAl Intermetallic Compounds and
their Hydrides”, J. Alloys Compd., 253-254, 343-346 (1997) (Crys. Structure, Experimental,
Magn. Prop., 13)
[1997Poh] Pohla, C., Ryder, P.L., “Crystalline and Quasicrystalline Phases in Rapidly Solidified Al-Ni
Alloys”, Acta Mater., 45, 2155-2166 (1997) (Experimental, Crys. Structure, 48)
[1997Pot] Potapov, P.L., Song, S.Y., Udovenko, V.A., Prokoshkin, S.D., “X-Ray Study of Phase
Transformations in Martensitic Ni-Al Alloys”, Metall. Mater. Trans. A, 28A, 1133-1142
(1997) (Crys. Structure, Experimental, 40)
[1997Vil] Villars, P., Prince, A., Okamoto, H., Handbook of Ternary Alloy Phase Diagrams, ASM
International, Materials Park, OH, 3, 3480 (1997) (Equi. Diagram)
[1998Jav] Javorsky, P., Nakotte, H., Robinson, R.A., Kelley, T.M., “Crystal Field in ErNiAl Studied
by Inelastic Neutron Scattering”, J. Magn. Magn. Mater., 186, 373-376 (1998) (Crys.
Structure, Experimental, 10)
[1998Rav] Ravelo, R., Aguilar, J., Baskes, M., Angelo, J.E., Fultz, B., Holian, B.L., “Free Energy and
Vibrational Entropy Difference between Ordered and Disordered Ni3Al”, Phys. Rev. B,
57(2), 862-869 (1998) (Thermodyn., Theory, Calculation, 43)
[1998Sim] Simonyan, A.V., Ponomarev, V.I., Khomenko, N.Yu., Vishnyakova, G.A., Gorshkov, V.A.,
Yukhvid, V.I., “Combustion Synthesis of Nickel Aluminides”, Inorg. Mater., 34(6), 558-
561 (1998), translated from Neorgan. Mater., 34(6), 684-687 (1998) (Crys. Structure,
Experimental, 12)
[2000Oka] Okamoto, H., Desk Handbook Phase Diagrams for Binary Alloys, ASM International,
Materials Park, OH 44073-0002, (2000) (Equi. Diagram)
[2002Jav] Javorsky, P., Divis, M., Sugawara, H., Sato, H., Mutka, H., “Crystal Field and Magneto-
Crystalline Anisitropy in ErNiAl”, Phys. Rev. B, 65(1), 014404-1 - 014404-8, (2002)
(Experimental, Theory, Magn. Prop., 25)
[2003Ria] Riani, P., Arrighi, L., Marazza, R., Mazzone, D., Zanicchi, G., Ferro, R., “Ternary Rare
Earth Aluminium Systems with Copper: a Review and the Contribution to Their
Assessment”, submitted to J. Phase Equilib., (2003) (Review, Assessment, 267)
[2003Sal] Saltykov, P., Cornish, L., Cacciamani, G., “Al-Ni (Aluminium-Nickel)”, MSIT Evaluation
Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International
Services GmbH, Stuttgart, to be published, (2003) (Assessment, Equi. Diagram, Crys.
Structure, 164)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
dissolves 0.01 at.% Ni at 639.9°C
[Mas2]
(Ni)
< 1455
cF4
Fm3m
Cu
a = 352.40 at 25°C [Mas2]
dissolves 20.2 at.% Al at 1385°C [Mas2]
(Er)
< 1529
hP2
P63/mmc
Mg
a = 355.92
c = 558.50
at 25°C [Mas2]
253
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
NiAl3< 856
oP16
Pnma
NiAl3
oP16
Pnma
Fe3C
a = 661.3 ± 0.1
b = 736.7 ± 0.1
c = 481.1 ± 0.1
a = 659.8
b = 735.1
c = 480.2
[1996Vik]
[1997Bou, V-C]
Ni2Al3< 1138
hP5
P3m1
Ni2Al3
a = 402.8
c = 489.1
36.8 to 40.5 at.% Ni [Mas2]
[1997Bou, V-C]
Ni3Al4< 702
cI112
Ia3d
Ni3Ga4
a = 1140.8 ± 0.1 [1989Ell, V-C]
NiAl
< 1651
cP2
Pm3m
CsCl
a = 287
a = 288.72 ± 0.02
a = 287.98 ± 0.02
42 to 69.2 at.% Ni [Mas2]
at 63 at.% Ni [1993Kha]
at 50 at.% Ni [1996Pau]
at 54 at.% Ni [1996Pau]
Ni5Al3< 723
oC16
Cmmm
Pt5Ga3
a = 753
b = 661
c = 376
63 to 68 at.% Ni [1993Kha, Mas2]
at 63 at.% Ni [1993Kha]
Ni3Al
< 1372
cP4
Pm3m
AuCu3
a = 356.77
a = 358.9
a = 356.32
a = 357.92
73 to 76 at.% Ni [Mas2]
[1986Hua]
at 63 at.% Ni [1993Kha]
disordered [1998Rav]
ordered [1998Rav]
Ni2Al9 mP22
P21/c
Ni2Al9
a = 868.5 ± 0.6
b = 623.2 ± 0.4
c = 618.5 ± 0.4
= 96.50 ± 0.01°
Metastable
[1988Li, 1997Poh]
NixAl1-x
0.60 < x < 0.68
tP4
P4/mmm
AuCu
m**
a = 383.0
c = 320.5
a = 379.5
c = 325.6
a = 379.5
c = 325.6
a = 375.1
c = 330.7
a = 379.9 to 380.4
c = 322.6 to 323.3
a = 371.7 to 376.8
c = 335.3 to 339.9
a = 378.00
c = 328.00
a = 418
b = 271
c = 1448
= 93.4°
Martensite, metastable
[1993Kha]
at 62.5 at.% Ni [1991Kim]
at 63.5 at.% Ni [1991Kim]
at 66.0 at.% Ni [1991Kim]
at 64 at.% Ni [1997Pot]
at 65 at.% Ni [1997Pot]
[1998Sim]
[1992Mur]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
254
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
Ni2Al hP3
P3m1
CdI2
a*126
P1
a = 407
b = 499
a = 1252
b = 802
c = 1526
= 90°
= 109.7°
= 90°
Metastable
[1993Kha]
[1994Mur]
D1(Ni,Al) Decagonal Metastable [1988Li]
D4(Ni,Al) Decagonal Metastable [1988Li]
ErAl3< 1070
cP4
Pm3m
AuCu3
hR60
R3m
HoAl3
a = 421.4
a = 602.5
c = 3567.5
[V-C2]
[V-C2]
ErNixAl2-x
ErAl2< 1455
cF24
Fd3m
MgCu2
a = 770.2
a = 780.1
a = 779.3
0 < x < 0.44 (~15at.% Ni) [1982Zar]
~15 at.% Ni [1982Zar]
0 at.% Ni [1982Zar]
0 at.% Ni [V-C2]
ErAl
< 1140
oP16
Pbcm
ErAl
a = 580.1
b = 1127
c = 557.0
[V-C2]
Er3Al2< 1060
tP20
P42/mnm
Gd3Al2
a = 812.3
c = 748.4
[V-C2]
Er2Al
< 1040
oP12
Pnma
Co2Si
a = 651.6
b = 501.5
c = 927.9
[V-C2]
Er2Ni17
< 1315
hP38
P63/mmc
Ni17Th2
a = 828
c = 801
[V-C2]
Er5Ni22 hP108 a = 486.2
c = 717.7
[V-C2], not reported in [1982Zar]
ErNi5-xAlx
ErNi5< 1380
hP6
P63/mmm
CaCu5
a = 497.5
c = 402.6
a = 485.4
c = 396.6
a = 485.4
c = 396.4
0 < x <~ 2 (~30 at.% Al) [1982Zar]
~30 at.% Al [1982Zar]
0 at.% Al [1982Zar]
0 at.% Al [V-C2]
Er4Ni17 hP16 a = 486.9
c = 840.7
[V-C2], not reported in [1982Zar]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
255
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
ErNi4hP90
mC30
C2/m
Ni4Pu
a = 487.4
c = 601.3
a = 485.5
b = 844.4
c =1023.1
= 99.54°
not reported in [1982Zar]
[V-C2]
[V-C2]
Er2Ni7< 1275
hR54
R3m
Er2Co7
a = 490.9
c = 3606.7
[V-C2]
ErNi3< 1320
hR36
R3m
Ni3Pu
a = 494.8
c = 2427
[V-C2]
ErNi2< 1255
cF24
Fd3m
MgCu2
a = 712.46 [V-C2]
solubility: see text
Er3Ni2 hR45
R3
Er3Ni2
a = 847.2
c = 1568.0
[V-C], not reported in [1982Zar]
ErNi
< 1100
oC8
CrB
or
oP8
Pmna
BFe
a = 369.2
b = 1008.8
c = 418.4
a = 699
b = 412
c = 541
[V-C2]
[V-C2]
Er5Ni3< 800
o*24 a = 845
b = 597.5
c = 1065
[V-C2]
Er3Ni
< 845
oP16
Pnma
Fe3C
a = 680.4
b = 943
c = 624.5
[V-C2]
* 1, ErNi3Al16 oC*
Cmcm
a = 396.0
b = 1563
c = 2681
[1982Zar], possibly oC24 - YNiAl4 -
type with c’ = 670 (=c/4) [V-C2]
* 2 ErNi3Al9 hR78
R32
ErNi3Al9
a = 727.16 ± 0.05
c = 2734.6 ± 0.3
[1993Gla]
* 3, ErNi2+xAl3-x hP*
P6/mmm
a = 901
c = 404.9
small solubility ~ 33 to 40 at.% Ni
[1973Ryk, 1981Zar, 1982Zar]
probably hP18 - YNi2Al3 or hP18 -
Ho2Ni5Ga5 -type
* 4, Er2Ni3Al7 hP* a = 1777
c = 397.1
[1973Ryk, 1981Zar, 1982Zar]
* 5, ErNiAl4 oC24
Cmcm
YNiAl4
a = 404.4
b = 1508
c = 663.1
[1973Ryk, 1981Zar, 1982Zar]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
256
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Er–Ni
* 6, Er3Ni8Al hP24
P63/mmc
CeNi3
a = 500.2
c = 1599
[1982Zar]
* 7, ErNiAl2 oC16
Cmcm
ordered Re3B
a = 406.4
b = 1006
c = 689.8
[1973Ryk, 1982Zar]
* 8, Er3Ni6Al2 cI44
Im3m
Ce3Ni6Si2
a = 888 [1982Zar]
* 9, ErNiAl hP9
P62m
ZrNiAl
a = 697.4
c = 380.1
a = 697.44
c = 379.78
a = 697.8
c = 379.9
[1982Zar]
solubility: see text
[1968Dwi]
[1973Oes]
* 10, Er2Ni2Al oI10
Immm
Mo2NiB2
a = 534.7
b = 837.4
c = 415.7
a = 837.4
b = 534.7
c = 415.7
[1982Rom2, 1982Zar]
[1997Vil]
* 11, ErNiAl(I) hP12
P63/mmc
MgZn2
a = 531.2
c = 854.8
[1987Tsv1] high pressure phase
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
20
40
60
80
20 40 60 80
20
40
60
80
Er Ni
Al Data / Grid: at.%
Axes: at.%
NiAl3
Ni2Al3
ErAl2
ErAl3
τ3
τ4
τ5
τ7
τ1
NiAl
Ni3Al
τ6
τ8
τ10
τ9
Er2Ni17ErNi5Er2Ni7ErNi3ErNi2
τ2
(Ni)
Fig. 1: Al-Er-Ni.
Partial isothermal
section up to 33 at.%
Er at 800°C
257
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
Aluminium – Iron – Gadolinium
Gabriele Cacciamani and Laura Arrighi
Literature Data
The Al-Fe-Gd phase diagram has been investigated only for x(Gd) < 0.33 and most experimental works
concerned crystal structure determinations and magnetic property measurements.
The 500°C isothermal section has been investigated by [1973Viv] in the above mentioned region by means
of X-ray diffraction and microscopy. [2002Hac] studied stable phase equilibria and amorphisation
properties in the Al-rich corner (for x(Al) > 0.75) combining experiments (XRD, TEM-EDS, DTA) and
thermodynamic modelling. Previous evaluations had been compiled by [1992Rei, 1992Rag, 2003Rag].
Binary Systems
The accepted Al-Fe phase diagram [2003Pis] is mainly based on the assessment by [1993Kat], except for
the Fe-rich region where the ordering equilibria between the (Fe), FeAl and Fe3Al solid solutions have been
recently investigated by [2001Ike].
The Al-Gd and Fe-Gd phase diagrams are accepted from the recent assessments by [2002Bod] and
[2000Zin], respectively.
Solid Phases
Crystal structure data are reported in Table 1.
The binary Laves phases GdAl2 and GdFe2 (isostructural, MgCu2 type) dissolve an appreciable amount of
the third element [1967Oes, 1973Viv, 1974Oes, 1975Dwi, 1976Gro]. At intermediate compositions,
however, a different Laves phase ( 1, MgZn2 type) is formed [1969Tes, 1971Oes, 1973Viv, 1973Zar,
1974Oes, 1975Dwi, 1983Bus].
The phases at the Gd2(Fe,Al)17 composition also present appreciable Al solubility. The composition and
temperature ranges of stability of the two structure types Th2Zn17 and Th2Ni17, however, are not well
defined. According to the accepted Fe-Gd binary system the Th2Ni17 type phase should be stable at higher
temperature (at 1335-1225°C). Ternary solubility of these phases has been investigated by [1973Viv,
1976McN].
At higher Al content a ternary phase with a Gd/M (M = Fe, Al) ratio equal to 1/12, is formed ( 2, ThMn12
type) studied by [1973Viv, 1974Viv, 1976Bus, 1987Liu] at the composition GdFe4Al8, and by [1980Fel,
1981Fel, 1987Liu, 1988Che] at GdFe6Al6. The same phase was obtained by melt spinning at higher Fe
concentrations, up to GdFe10Al2 [1988Wan].
Finally, with the same Gd/M ratio, another ternary phase ( 3, at the composition GdFe2Al10) was studied
by [1973Viv, 1998Thi].
Invariant Equilibria
Al-rich invariant equilibria determined by [2002Hac] are reported in Table 2. On the basis of these results
[2003Rag] elaborated the reaction scheme shown in Fig. 1.
Liquidus Surface
The Al-rich liquidus surface shown in Fig. 2 has been determined by [2002Hac] by combining experiments
and thermodynamic modeling. In the same figure the region of good glass formability determined by the
same author is also shown. In order to keep the internal consistency of the figure, isothermal curves have
not been modified and do not exactly meet the accepted Al-Gd binary liquidus, the reliability of which is
rather uncertain.
258
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
Isothermal Sections
The 500°C isothermal section for x(Gd) < 0.33 was first determined by [1973Viv]. The Al-rich corner has
been recently investigated by [2002Hac], who substantially confirmed the results by [1973Viv]. The section
is reported in Fig. 3, where results by [1974Oes, 1983Bus] have also been considered. With respect to
[1973Viv] the solubility of 2 (between the GdFe4Al8 and GdFe6Al6 compositions) has been included and
only one Gd2(Fe,Al)17 phase has been drawn, considering the second one stable at higher temperature. From
a thermodynamic point of view the convergence of five tie triangles at the extremum of the 2 solid solution
may be unlikely: nevertheless in Fig. 3 the equilibria reported in the experimental investigations have been
kept.
Temperature – Composition Sections
Vertical sections at 5 at.% Fe and 5 at.% Gd have been experimentally investigated and thermodynamically
modelled by [2002Hac] in the Al-rich region (x(Al) > 0.75). They are reported in Figs. 4 and 5.
Miscellaneous
Ternary phase 1 has been investigated by Mössbauer spectroscopy [1975Dwi, 1980Ara] and by XRD, XPS
and ESR [2001Jar]. Magnetic, electric and thermal properties have been studied by [1984Sim].
Magnetic properties of 2 have been studied by [1978Bus, 2001Duo1, 2001Duo2] at the GdFe4Al8composition, by [2002Duo] at GdFe5Al7, by [1981Fel, 1988Che, 2001Duo1] at GdFe6Al6 and by [1987Liu,
1988Wan] in the complete solubility range. [1988Wan] extended the measurements to metastable
compositions richer in Fe, up to GdFe10Al2.
Magnetic properties of the phases at the Gd2(Fe,Al)17 composition have been studied by [1976McN] and
reviewed by [1994Liu]. [1998Thi] investigated the low temperature magnetization of 3.
Good glass forming ability in the Al-rich corner (reported in Fig. 2) has been determined by [2002Hac] and
magnetic properties of amorphous alloys at the Gd60Fe30Al10 composition have been studied by
[2002Kon].
References
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-Rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids, 6, 16-37 (1958) (Crys. Structure, Magn.
Prop., Experimental, 49)
[1961Lih] Lihl, F., Ebel, H., “X-ray Examination of the Constitution of Iron-rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenwes., 32, 483-487 (1961) (Crys.
Structure, Experimental, 12)
[1967Oes] Oesterreicher, H., Wallace, W.E., “Studies of Pseudo-Binary Laves-Phase Systems
Containing Lanthanides”, J. Less-Common Met., 13, 91-102 (1967) (Crys. Structure,
Experimental, 22)
[1969Tes] Teslyuk, M.Y., Intermetallic Compounds with Structure of Laves Phases (in Russian),
Moscow, Nauka, 1-138 (1969) (Crys. Structure, Equi. Diagram, Review, Theory)
[1971Oes] Oesterreicher, H., “Structural Studies of Rare-Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Crys. Structure, Experimental, 6)
[1973Viv] Vivchar, O.J., Zarechnyuk, O.S., Ryabov, V.R., “Study of the Gd-Fe-Al System in the Low
Gd Region” (in Russian), Dopov. Akad. Nauk Ukrain. RSR, Ser. A, Fiz-Mat. Tekh. Nauki,
11, 1040-1042 (1973) (Crys. Structure, Equi. Diagram, Experimental, #, 14)
[1973Zar] Zarechnyuk, O. S., Rykhal, R. M., Vivchar, O. I., “Laves Phases in Ternary Systems
Rare-Earth Metal-Transition Metal of the IV Period-Aluminium”, Sb. Nauchn. Rab. Inst.
Metallofiz., Akad. Nauk Ukr. SSR, 42, 92-94 (1973) (Crys. Structure, Experimental,
Review)
259
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
[1974Oes] Oesterreicher, H., “Constitution of Al Base Rare Earth Alloys RT2-RAl2 (R = Pr, Gd, Er; T
= Mn, Fe, Co, Ni, Cu)”, Inorg. Chem., 13, 2807-2811 (1974) (Crys. Structure,
Experimental, 30)
[1974Viv] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12-type Structure in R-Fe-Al
Systems” (in Russian), Tezisy Dokl. - Vses. Konf. Kristallokhim. Intermet. Soedin, Rykhal,
R.M. (Ed.), Vol. 2, L'vov. Gos. Univ., Lvov, 41 (1974) (Crys. Structure, Experimental, 0)
[1975Dwi] Dwight, A.E., Kimball, C.W., Preston, R.S., Taneja, S.P., Weber, L., “Crystallographic and
Mössbauer Study of (Sc,Y,Ln)(Fe,Al)2 Intermetallic Compounds”, J. Less-Common Met.,
40, 285-291 (1975) (Crys. Structure, Experimental, Moessbauer, 8)
[1976Bus] Buschow, K.H.J., van der Vucht, J.H.N., van den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth-3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Crys. Structure, Experimental, 2)
[1976Gro] Groessinger, R., Steiner, W., Krec, K., “Magnetic Investigations of Pseudobinary
RE(Fe,Al)2 Systems (RE = Y, Gd, Dy, Ho)” (in German), J. Magn. Magn. Mater., 2,
196-202 (1976) (Magn. Prop., Experimental, 20)
[1976McN] McNeely, D., Oesterreicher, H., “Structural and Low-Temperature Magnetic Studies on
Compounds Sm2Fe17 with Al Substitution for Fe”, J. Less-Common Met., 44, 183-193
(1976) (Crys. Structure, Magn. Prop., Experimental, 26)
[1978Bus] Buschow, K.H.J., van der Vucht, J.H.N, Kran, A. M., “Magnetic Ordering in Ternary Rare
Earth Iron Aluminium Compounds (RFe4Al8)”, J. Phys., F: Met. Phys., 8, 921-932 (1978)
(Experimental, Magn. Prop., 9)
[1980Ara] Aranjo, S. I., Guimaraes, A. P., “Mössbauer Studies of the Pseudobinary Intermetallic
Compounds Gd(AlxFe1-x)2”, J. Phys. F: Met. Phys., 10, 1313-1321 (1980) (Magn. Prop.,
Moessbauer, 18)
[1980Fel] Felner, I., “Crystal Structures of Ternary Rare Earth-3d Transition Metal Compounds of the
RT6Al6 Type”, J. Less-Common Met., 72, 241-249 (1980) (Experimental, Crys.
Structure, 10)
[1981Fel] Felner, I., Seh, M., Rakavy, M., Nowik, I., “Magnetic Order and Hyperfine Interactions in
RFe6Al6 (R = Rare Earth)”, Phys. Chem. Solids, 42, 369-377 (1981) (Crys. Structure, Magn.
Prop., Experimental, 6)
[1983Bus] Buschow, K.H.J., van Engen, P.G., Jongebreur, R., “Magneto-Optical Properties of
Metallic Ferromagnetic Materials”, J. Magn. Magn. Mater., 38, 1-22 (1983) (Magn. Prop.,
Optical Prop., 23)
[1984Sim] Sima, V., Grossinger, R., Sechovsky, V., Smetana, Z., Sassik, H., “The Effect of Local
Disorder on the Magnetic, Electric and Thermal Properties of RE (Fe1-xAlx)2 (RE = Gd,
Dy)”, J. Phys. F: Met. Phys., 14(4), 981-1004 (1984) (Magn. Prop., Electr. Prop.,
Experimental, 36)
[1987Liu] Liu, W. L., “The Temperature-Composition Magnetic Phase Diagram and Its Relation to the
Site Occupancy of Fe Atom in GdFeAl (GdFe4+xAl8-x, 0 x 2)”, J. Sci. Hiroshima Univ.,
51(3), 221-246 (1987) (Crys. Structure, Magn. Prop., 34)
[1988Che] Chelkowska, G., Chelkowska, A., Winiarska, A., “Magnetic Susceptibility and Structural
Investigations of REAl6Fe6 Compounds for RE = Y, Gd, Tb, Dy, Ho, and Er”, J.
Less-Common Met., 143, L7-L10 (1988) (Crys. Structure, Magn. Prop., Experimental, 12)
[1988Gsc] Gschneidner Jr, K.A., Calderwood, F.W., “The Al-Gd (Aluminum-Gadolinium) System”,
Bull. Alloy Phase Diagrams, 9(6), 680-683 (1988) (Assessment, #, 41)
[1988Wan] Wang, X.-Z., Chevalier, B., Berlureau, T., “Fe-Rich Pseudobinary Alloys with the ThMn12
Structure Obtained by Melt Spinning: Gd(FenAl12-n), n = 6, 8, 10”, J. Less-Common Met.,
138(2), 235-240 (1988) (Crys. Structure, 17)
[1992Rei] Reinsch, B., “Aluminum – Iron - Gadolinium”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.16514.1.20, (1992) (Equi. Diagram, Assessment, Crys.
Structure, 15)
260
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
[1992Rag] Raghavan, V., “The Al-Fe-Gd (Aluminum-Iron-Gadolinium) System”, in “Phase Diagrams
of Ternary Iron Alloys”, Part 6A, Ind. Inst. Metals, Calcutta, 108-112 (1992) (Equi.
Diagram, Crys. Structure, Review, #, 12)
[1993Kat] Kattner, U.R. Burton, B.P., “Al-Fe (Aluminum-Iron)”, in “Phase Diagrams of Binary Iron
Alloys”, Okamoto, H. (Ed.), ASM International, Materials Park, Ohio, 12-28 (1993)
(Assessment, 99)
[1994Liu] Liu, J.P., de Boer, F.R., de Chatel, P.F., Coehoorn, R., Buschow, K.H.J., “On the 4f-3d
Exchange Interaction in Intermetallic Compounds”, J. Magn. Magn. Mater., 132, 159-179
(1994) (Magn. Prop., Review, 64)
[1996Mao] Mao, O., Yang, J., Altounian, Z., Ström-Olsen, J.O., “Metastable RFe7 Compounds (R =
Rare Earths and their Nitrides with TbCu7 Structure)”, J. Appl. Phys., 79(8), 4605-4607
(1996) (Crys. Structure, Magn. Prop., Experimental, 5)
[1997Kog] Kogachi, M., Haraguchi, T., “Quenched-in Vacancies in B2-Structured Intermetallic
Compound FeAl”, Mater. Sci. Eng. A, 230A, 124-131 (1997) (Crys. Structure,
Experimental, 23)
[1998Ali] Aliravci, C.A., Pekgueleryuez, M.O., “Calculation of Phase Diagrams for the Metastable
Al-Fe Phases Forming in Direct-Chill (DC)-Cast Aluminium Alloy Ingots”, Calphad, 22,
147-155 (1998) (Calculation, Equi. Diagram, 20)
[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10 (Ln = Y, La-Nd,
Sm, Cd-Lu and T = Fe, Ru, Os) with YbFe2Al10 Type Structure and Magnetic Properties of
the Iron-Containing Series”, J. Mater. Chem., 8(1), 125-130 (1998) (Crys. Structure,
Experimental, Magn. Prop., 31)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-Rich Fe-Al
Alloys”, Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 16)
[2000Sac] Saccone, A., Cardinale, A.M., Delfino, S., Ferro, R., “Gd-Al and Dy-Al Systems: Phase
Equilibria in the 0 to 66.7 at.% Al Composition Range”, Z. Metallkd, 91(1), 17-23 (2000)
(Experimental, Equi. Diagram, Crys. Structure, #, 12)
[2000Zin] Zinkevich, M., Mattern, N., Seifert H.J., “Reassessment of the Fe-Gd (Iron-Gadolinium)
System”, J. Phase Equilib., 21(4), 385-394 (2000) (Assessment, Calculation, 28)
[2001Duo1] Duong, N.P., Klaasse, J.C.P., Brueck, E., de Boer, F.R., Buschow, K.H.J., “Magnetic
Properties of GdT4Al8 and GdT6Al6 Compounds (T = Cr, Mn, Cu)”, J. Alloys Compd., 315,
28-35 (2001) (Experimental, Magn. Prop., 18)
[2001Duo2] Duong, N.P., Brück, E., de Boer, F:R., Buschow, K.H.J., “Magnetic Properties of GdFe4Al8and Related Compounds”, Physica B, 294B-295B, 212-216 (2002) (Experimental, Magn.
Prop., 5)
[2001Ike] Ikeda, O., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
BCC Phases in the Fe-Rich Portion of the Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Thermodyn., Experimental, 18)
[2001Jar] Jarosz, J., Talik, E., “Electronic Structure and ESR in GdTAl Ternary Compounds; T = 3d,
4d Transition Metals”, J. Alloys Compd., 317-318, 385-389 (2001) (Crys. Structure,
Experimental, Phys. Prop., 7)
[2002Bod] Bodak, O., “Al-Gd (Aluminum-Gadolinium)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), Materials Science International Services GmbH, Stuttgart;
Document ID: 20.12303.1.20 (2002) (Equi. Diagram, Assessment, Crys. Structure, 15)
[2002Duo] Duong, N.P., Brück, E., de Boer, F.R., Buschow, K.H.J., “Magnetic Properties of GdFe5Al7and TbFe4.45Al7.55”, J. Alloys Compd., 338, 213-217 (2002) (Crys. Structure, Experimental,
Magn. Prop., 5)
[2002Hac] Hackenberg, R.E., Gao, M.C., Kaufman, L., Shiflet, G.J., “Thermodynamics and Phase
Equilibria of the Al-Fe-Gd Metallic Glass-Forming System”, Acta Mater., 50, 2245-2258
(2002) (Calculation, Equi. Diagram, Experimental, Thermodyn., 39)
261
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Gd
[2002Kon] Kong, H.Z., Ding, J., Dong, Z.L., Wang, L., White, T., Li, Y., “Observation of Clusters in
Re60Fe30Al10 Alloys and the Associated Magnetic Properties”, J. Phys. D: Appl. Phys.,
35(5), 423-429 (2002) (Experimental, Magn. Prop., 26)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 58)
[2003Rag] Raghavan, V., “Al-Fe-Gd (Aluminum-Iron-Gadolinium)”, J. Phase Equilib., 24(2),
170-173 (2003) (Review, #, 7)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
( Fe)
1538-1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)
1394-912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2, 1993Kat]
dissolves up to 1.2 at.% Al
( Fe)
< 912
cI2
Im3m
W
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
pure Fe at 25°C [Mas2]
dissolves up to 45.0 at.% Al at 1310°C
0 - 18.8 at.%Al, HT [1958Tay]
0 - 19.0 at.% Al, HT [1961Lih]
0 - 18.7 at.% Al, 25°C [1999Dub]
( Gd) hR3
P3m
Sm
a = 361
c = 2603
at 25°C, 3.0 GPa [Mas2]
( Gd)
1313-1235
cI2
Im3m
W
a = 406 [Mas2]
( Gd)
< 1235
hP2
P63/mmc
Mg
a = 363.36
c = 578.10
at 25°C [Mas2]
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [1993Kat]
262
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
1102 - 1232
cI16?
-
a = 598.0 at 61 at.% Al [1993Kat]
FeAl
< 1310
cP8
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5 - 47.5 at.% Al [1961Lih]
36.2 - 50.0 at.% Al [1958Tay]
39.7 - 50.9 at.% Al [1997Kog]
quenched in water from 500°C
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
~24 - ~37 at.% Al [2001Ike]
23.1 - 35.0 at.% Al [1958Tay]
24.7 - 31.7 at.% Al [1961Lih]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [1993Kat]
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
metastable
85.7 at.% Al [1993Kat]
[1998Ali]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[1998Ali]
Fe4Al13
1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7 to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
[2003Pis], 74.16 to 76.7 at. % Al
solid solubility ranges
from 74.5 to 75.5 at.% Al
[2003Pis], at 76.0 at.% Al.
Also denoted FeAl3 or Fe2Al7
Gd2Al
< 940
oP12
Pnma
Co2Si
a = 674.2
b = 525.4
c = 975.6
a = 661.2
b = 515.0
c = 957.8
a = 660.6
b = 514.6
c = 953.1
as cast, [2000Sac]
cooled 10 K min-1, [2000Sac]
[1988Gsc]
Gd3Al2< 970
tP20
P42/mnm
Zr3Al2
a = 832.0
c = 762.8
a = 833.9
c = 762.0
cooled 10 K min-1, [2000Sac]
[1988Gsc]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
263
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
GdAl
< 1070
oP16
Pbcm
DyAl
a = 589.3
b = 1159
c = 569.5
a = 588.8
b = 1152.7
c = 565.6
cooled 10 K min-1, [2000Sac]
[1988Gsc]
Gd(FexAl1-x)2
GdAl2< 1520
cF24
Fd3m
MgCu2
a = 790.6
0 x 0.37 [1967Oes, 1974Oes]
at x = 0, cooled 10 K min-1, [2000Sac]
GdAl3< 1125
hP8
P63/mmc
Ni3Sn
a = 633.1
c = 460.0
[1988Gsc]
Gd(Fe1-xAlx)2
GdFe2
< 1080
cF24
Fd3m
MgCu2
a = 740.0
a = 749.3
a = 752.1
0 x 0.26 [1974Oes]
at x = 0 [2000Zin, V-C2]
at x = 0.2 [1976Gro]
at x = 0.25 [1967Oes]
GdFe3
< 1160
hR36
R3m
PuNi3
a = 514.8
c = 2462
[2000Zin, V-C2]
Gd6Fe23
< 1280
cF116
Fm3m
Th6Mn23
a = 1212 [2000Zin, V-C2]
Gd2(Fe1-xAlx)17
Gd2Fe17
1335-1215
hP38
P63/mmc
Th2Ni17
a = 849.6
c = 834.5
a = 860
c = 840
0 x 0.147 [1973Viv]
at x = 0.0, HT [2000Zin, V-C2]
at x = 0.147, [1973Viv] probably HT
Gd2(Fe1-xAlx)17
Gd2Fe17
< 1215
hR57
R3m
Th2Zn17 a = 851.7
c = 1242.9
a = 875.8 to 882.0
c = 1269.8 to 1279.4
0 x 0.56 [1973Viv]
at x = 0 [2000Zin, V-C2]
at 0.45 x 0.56 [1976McN]
GdFe7 a = 492
c = 415
metastable. [1996Mao]
(lattice parameters from graph)
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
264
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
Table 2: Invariant Equilibria in the Al-rich Corner [2002Hac]
* 1, Gd(Fe1-xAlx)2 hP12
P63/mmc
MgZn2
a = 541.4
c = 881.2
a = 544.5
c = 880.9
a = 538.8
c = 870.9
0.28 x 0.52 [1974Oes]
at x = 0.5 [1971Oes]
GdFeAl
at x = 0.5 [1983Bus]
GdFeAl
at x = 0.4 [1983Bus]
* 2, Gd(FexAl1-x)12 tI26
I4/mmm
ThMn12
a = 875.6
c = 503.6
a = 877.8 to 869.4
c = 505.5 to 502.1
a = 868.7
c = 501.5
a = 857
c = 495
a = 849
c = 489
0.33 x 0.50 [1988Che]
at x = 0.33 [1974Viv, 1976Bus]
GdFe4Al8at x = 0.33 - 0.5 [1987Liu]
at x = 0.5 [1980Fel, 1981Fel]
GdFe6Al6metastable, at GdFe8Al4 [1988Wan]
metastable, at GdFe10Al2 [1988Wan]
* 3, GdFe2Al10 oP52
Cmcm
YbFe2Al10
a = 897.0
b = 1016.2
c = 902.3
[1998Thi]
Reaction T [°C] Type Phase Composition (at.%)
Al Fe Gd
L + Fe2Al5 Gd2(Fe,Al)17 + Fe4Al13 1137 U1 L
Gd2(Fe,Al)17
75.23
50.00
22.56
39.47
2.21
10.53
L + Fe4Al13 Gd2(Fe,Al)17 + 2 1100 U2 L
Gd2(Fe,Al)17
78.20
50.00
14.53
39.47
7.27
10.53
L + Gd2(Fe,Al)17 GdAl2 + 2 1097 U3 L
Gd2(Fe,Al)17
GdAl2
78.18
50.00
-
13.74
39.47
-
8.08
10.53
33.33
L + 2 Fe4Al13 + GdAl2 1092 U4 L
GdAl2
78.58
-
13.28
-
8.14
33.33
L + GdAl2 Fe4Al13 + GdAl3 1041 U5 L
GdAl2GdAl3
82.21
-
74.00
8.20
-
1.00
9.59
33.33
25.00
L + Fe4Al13 + GdAl3 3 1040 P1 L
GdAl3
82.27
74.00
8.15
1.00
9.58
25.00
L + Fe4Al13 (Al) + 3 647 U10 L 98.6 0.80 0.60
L (Al) + GdAl3 + 3 638 E1 L
GdAl3
95.96
75.00
0.20
0
3.84
25.00
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
265
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
Fig. 1: Al-Fe-Gd. Partial Al-Fe-Gd reaction scheme [2003Rag]. Designation "2:17" is used to
denote αGd2(Fe,Al)
17 phase.
Al-Fe Al-Fe-Gd Al-Gd
l+GdAl2
GdAl3
1125 p2
l (Al)+Fe4Al
13
655 e1
L + Fe4Al
13+ GdAl
3τ3
1040 P1
L + Fe4Al
13τ3
+ (Al)647 U10
GdAl2+Fe
4Al
13τ3+τ
21000>U
c>500 U
8
Fe4Al
13+GdAl
3τ3+GdAl
21020 U
6
Fe4Al
13+2:17 τ
2+Fe
2Al
51000 U
7
GdAl2+τ
3GdAl
3+τ
2Uc>U
d>500 U
9
L+GdAl2
Fe4Al13
+GdAl3
1041 U5
L + τ2
GdAl2 + Fe
4Al
131092 U
4
L + 2:17 τ2 + GdAl
21097 U
3
L + Fe4Al
132:17 + τ
21100 U
2
L+Fe2Al
5Fe
4Al
13+2:171137 U
1
L (Al) + GdAl3 + τ
3638 E
1
l+Fe2Al
5Fe4Al
13
1160 p1
L+Fe2Al
5+2:17
L+2:17+GdAl2
L+Fe4Al
13+2:17 Fe
2Al
5+Fe
4Al
13+2:17
L+2:17+τ2
Fe4Al
13+2:17+τ
2
2:17+τ2+GdAl
2L+τ2+GdAl
2
L+GdAl2+Fe
4Al
13τ2+GdAl
2+Fe
4Al
13
L+Fe4Al
13+GdAl
3
Fe4Al13
+GdAl3+τ
3L+GdAl3+τ
3L+Fe
4Al
13+τ
3
GdAl3+τ
3+GdAl
2Fe
4Al
13+τ
3+GdAl
2
Fe4Al
13+τ
2+Fe
2Al5
2:17+τ2+Fe
2Al5
Fe4Al
13+τ
3+τ
2GdAl
2+τ
3+τ
2
GdAl2+GdAl
3+τ
2τ3+GdAl
3+τ
2
Fe4Al
13+τ
3+(Al)
L+τ3+(Al)
(Al)+GdAl3+τ
3
l (Al)+GdAl3
650 e2
GdAl2+Fe
4Al13
+GdAl3
L+τ2+Fe
4Al
13
1105
266
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
10
20
30
10 20 30
70
80
90
Gd 40.00Fe 0.00Al 60.00
Gd 0.00Fe 40.00Al 60.00
Al Data / Grid: at.%
Axes: at.%
1400
1300
1200
1100
GdAl2
1000
GdAl3
900
800
700
Fe4Al13
U4
U5
U2
P1
U10
p2
e2
e1
E1
αGd2(Fe,Al)17
τ2
τ3
good glassforming area
U3
Fig. 2: Al-Fe-Gd.
Al-rich liquidus
surface [2002Hac]
20
40
60
80
20 40 60 80
20
40
60
80
Gd Fe
Al Data / Grid: at.%
Axes: at.%
τ2
τ3
τ1
Fe3Al
FeAl
Fe4Al13Fe2Al5
FeAl2
Gd(Fe1-xAlx)2
GdFe3 Gd6Fe23
GdAl3
GdAl2
(αFe)
αG
d2 (Fe
1-x Al
x )17
Gd(FexAl1-x)2
GdFe2
Gd2Fe17
(Al)Fig. 3: Al-Fe-Gd.
Isothermal section at
500°C [1973Viv,
1974Oes, 1983Bus,
2002Hac]
267
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Gd
10500
600
700
800
900
1000
1100
1200
Gd 5.00Fe 0.00Al 95.00
Gd 5.00Fe 20.00Al 75.00Fe, at.%
Tem
pera
ture
, °C
10411092°C
1100°C
647638
L
L+τ3
L+Fe4Al13+τ3
L+Fe4Al13
(Al)+Fe4Al13+τ3(Al)+GdAl3+τ3
10500
600
700
800
900
1000
1100
1200
Gd 0.00Fe 5.00Al 95.00
Gd 20.00Fe 5.00Al 75.00Gd, at.%
Tem
pera
ture
, °C
L+GdAl3+τ3
L+GdAl2
L+GdAl3
L+τ3
L
(Al)+GdAl3+τ3(Al)+Fe4Al13+τ3
L+Fe4Al13
647 638
1042°C
Fig. 4: Al-Fe-Gd.
Al-rich part of the
isopleth at 5 at.% Gd
[2002Hac]
Fig. 5: Al-Fe-Gd.
Al-rich part of the
isopleth at 5 at.% Fe
[2002Hac]
268
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ho
Aluminium – Iron – Holmium
Gabriele Cacciamani and Laura Arrighi
Literature Data
The Al-Fe-Ho system has been investigated only for x(Ho) < 0.33 and most experimental work concerned
crystal structure determination (either by X-ray and neutron diffraction) and magnetic property
measurements.
The 500°C isothermal equilibria have been investigated by [1971Rya] in the above mentioned region, by
means of X-ray diffraction and microscopy, and by [2001Yan] at the Ho2(Fe,Al)17 composition.
Binary Systems
The accepted Al-Fe phase diagram [2003Pis] is mainly based on the assessment by [1993Kat], except for
the Fe-rich region where the ordering equilibria between the ( Fe), FeAl and Fe3Al solid solutions have
been recently investigated by [2001Ike].
The more recent assessment of the Al-Ho phase diagram [1988Gsc] shows unlikely liquidus curves,
especially around the HoAl2 and Ho2Al compositions. It is here accepted with some reserve, further
experimental investigation on this system being needed.
The Fe-Ho phase diagram is accepted from the assessment by [1993Oka] with the addition of the solubility
range reported by [2001Yan] for the Ho2Fe17 phase.
Solid Phases
Crystal structure data are reported in Table 1.
The binary Laves phases HoAl2 and HoFe2 (isostructural, MgCu2 type) dissolve more than 20 at.% of the
third element. At intermediate compositions, however, a different Laves phase ( 1, MgZn2 type) is formed
[1971Oes, 1971Rya, 1973Zar, 1974Oes, 1975Dwi, 1976Gro].
Ho2Fe17 (Th2Ni17 type) also presents large Al solubility [1996Wan, 1998Yel, 2001Yan]. According to
[2001Yan], at increasing Al compositions it transforms to the related structures TbCu7 and Th2Zn17 type,
respectively. According to [1996Mao] a HoFe7 metastable phase with the TbCu7 type structure is present
in the Fe-Ho binary system.
At even higher Al content another ternary phase, with a larger Ho/M (M = Fe, Al) ratio, is formed ( 4,
ThMn12 type) studied by [1971Rya, 1974Viv, 1976Bus, 1988Sch, 2000Pai] at the composition HoFe4Al8,
and by [1980Fel, 1981Fel, 1988Che, 1998Sch] at HoFe6Al6. At this same composition [1998Sch]
determined the cell parameters at 4.2, 300 and 500 K. [2001Sch] found the same structure at HoFe7Al5;
notice however that the ThMn12 type structure is reported to be metastable in similar R-Fe-Al systems at
this composition.
Finally, with the same Ho/M ratio, another ternary phase ( 5, at the composition HoFe2Al10) was studied
by [1971Rya, 1998Thi].
Isothermal Sections
The 500°C isothermal section for x(Ho)<0.33 was first determined by [1971Rya]. It is reported in Fig. 1
with minor changes in order to be consistent with the homogeneity ranges reported in more recent structural
investigations by [1974Oes, 1981Fel, 2001Sch, 2001Yan].
Miscellaneous
Mössbauer measurements on the 1 phase at the HoFeAl composition have been carried out by [1975Dwi,
1976Gro].
269
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ho
Magnetic properties of the phases at the Ho2(Fe,Al)17 composition have been studied by [1992Jac,
1996Wan, 1999Wan] and reviewed by [1994Liu, 2002Ram].
Magnetic properties of 4 have been investigated by low temperature Cp measurements, neutron diffraction,
etc. by [1978Bus, 1988Sch, 1989Sch, 1998Hag, 2000Hag, 2000Pai] at the HoFe4Al8 composition, by
[1981Fel, 1988Che] at HoFe6Al6 and by [2001Sch] at HoFe7Al5.
[1998Thi] investigated the low temperature magnetisation of 5.
References
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-Rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids, 6, 16-37 (1958) (Crys. Structure., Magn.
Prop., Experimental, 49)
[1961Lih] Lihl, F., Ebel, H., “X-ray Examination fo the Constitution of Iron-Rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenwes., 32, 483-487, (1961) (Crys.
Structure, Magn. Prop., Experimental, 12)
[1971Oes] Oesterreicher, H., “Structural Studies of Rare-Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Crys. Structure, Experimental, 6)
[1971Rya] Ryabov, V.R., Zarechnyuk, O.S., Rabkin, D.M., Vivchar, O.I, “Phase Composition of Fe/Al
Welds Containing Ho” (in Russian), Izv. Akad. Nauk Ukr. SSR, 27 (4), 75-76 (1971) (Crys.
Structure, Equi. Diagram, Experimental, #, 0)
[1973Zar] Zarechnyuk, O.S., Rikhal, R.M. and Vivchar, O.I., “Laves Phases in Ternary Systems of the
Type Rare-Earth Metal-Transition Metal-Al” (in Russian), Akad. Nauk Ukr. SSR,
Metallofiz., 46, 92-94 (1973) (Crys. Structure, Experimental, 22)
[1974Oes] Oesterreicher, H., “Constitution of Al Base Rare Earth Alloys RT2-RAl2 (R = Pr, Gd, Er ;
T = Mn, Fe, Co, Ni, Cu)”, Inorg. Chem., 13, 2807-2811 (1974) (Crys. Structure,
Experimental, 30)
[1974Viv] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12-Type Structure in R-Fe-Al
Systems” (in Russian), Tezisy Dokl. - Vses. Konf. Kristallokhim. Intermet. Soedin., Rykhal,
R.M. (Ed.), Vol. 2, L'vov. Gos. Univ., 41 (1974) (Crys. Structure, Experimental, 0)
[1975Dwi] Dwight, A.E., Kimball, C.W., Preston, R.S., Taneja, S.P., Weber, L., “Crystallographic and
Mössbauer Study of (Sc, Y, Ln) (Fe, Al)2 Intermetallic Compounds”, J. Less-Common Met.,
40, 285-291 (1975) (Crys. Structure, Moessbauer, Experimental, 8)
[1976Bus] Buschow, K.H.J., Van der Vucht, J.H.N., Van den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth-3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Crys. Structure, Experimental, 2)
[1976Gro] Groessinger, R., Steiner, W., Krec, K., “Magnetic Investigations of Pseudobinary RE(Fe,
Al)2 Systems (RE = Y, Gd, Dy, Ho)” (in German), J. Magn. Mater., 2, 196-202 (1976)
(Crys. Structure, Magn. Prop., Experimental, 20)
[1978Bus] Buschow, K.H.J., van der Kran, A.M., “Magnetic Ordering in Ternary Rare Earth Iron
Aluminium Compounds (RFe4Al8)”, J. Phys. F, Met. Phys., 8, 921-932 (1978) (Magn.
Prop., 9)
[1980Fel] Felner, I., “Crystal Structures of Ternary Rare Earth-3d Transition Metal Compounds of the
RT6Al6 Type”, J. Less-Common Met., 72, 241-249 (1980) (Crys. Structure, 10)
[1981Fel] Felner, I., Seh, M., Rakavy, M., Nowik, I., “Magnetic Order and Hyperfine Interactions in
RFe6Al6 (R = Rare Earth)”, J. Phys. Chem. Solids, 42, 369-377 (1981) (Crys. Structure,
Magn. Prop., Experimental, 6)
[1986Gri] Griger, A., Syefaniay, V., Turmezey, T., “Crystallographic Data and Chemical
Compositions of Aluminum-Rich Al-Fe Intermetallic Phases”, Z. Metallkd., 77, 30-35
(1986) (Equi. Diagram, Crys. Structure, Experimental, 23)
[1988Che] Chelkowska, G., Chelkowska, A., Winiarska, A., “Magnetic Susceptibility and Structural
Investigations of Rare Earth-Aluminium-Iron (REAl6Fe6) Compounds for RE = Yttrium,
270
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ho
Terbium, Dysprosium, Holmium, and Erbium”, J. Less-Common Met., 143, L7-L10 (1988)
(Crys. Structure, Magn. Prop., Experimental, 12)
[1988Gsc] Gschneider, K.A. Jr, Caldeerwood, F.W., “Al-Ho (Aluminum-Holmium)”, Bull. Alloy
Phase Diagrams, 9(6), 684-686 (1988) (Equi. Diagram, Review, 19)
[1988Sch] Schaefer, W., Groenefeld, M., Will, G., Gal, J., “Magnetic Helical Ordering in Intermetallic
Rare Earth-Iron-Aluminum Compounds”, Mater. Sci. Forum, 27-28, 243-248 (1988) (Crys.
Structure, Magn. Prop., Experimental, 9)
[1989Sch] Schaefer, W., Will, G., Kalvius, G.M., Gal, J., “Coexistence of Long Range Order and Spin
Glass Similar Behaviour in HoFe4Al8”, Physica B, 156/157, 751-753 (1989) (Magn. Prop.,
Experimental, 11)
[1992Jac] Jacobs, T.H., Buscow, K.H.J., Zhou, G.F., Li, X., de Boer F.R., “Magnetic Interactions in
R2Fe17-xAlx Compounds (R = Ho, Y)”, J. Magn. Magn. Mater, 116(1-2), 220-230 (1992)
(Magn. Prop., Experimental)
[1993Kat] Kattner, U.R., Burton, B.P., “Al-Fe (Aluminum-Iron)”, in “Phase Diagrams of Binary Iron
Alloys”, Okamoto, H. (Ed.), ASM International, Materials Park, Ohio, 12-28 (1993) (Equi.
Diagram, Review, 99)
[1993Oka] Okamoto, H., “Fe-Ho (Iron-Holmium)”, in “Phase Diagrams of Binary Iron Alloys”,
Okamoto, H. (Ed.), ASM International, Materials Park, Ohio, 179-181 (1993) (Equi.
Diagram, Review, 20)
[1994Bur] Burkhardt, U., Grin, J., Ellner, M., Peters, K., “Structure Refinement of the Iron-Aluminium
Phase with the Approximate Composition Fe2Al5”, Acta Crystallogr., Sect. B: Struct.
Crystallogr. Crys. Chem., B50, 313-316 (1994) (Crys. Structure, Experimental, 9)
[1994Gri] Grin, J., Burkhardt, U., Ellner, M., Peters, K., “Refinement of the Fe4Al13 Structure and its
Relationship to Quasihomological Homotypical Structures”, Z. Kristallogr., 209, 479-487
(1994) (Crys. Structure, Experimental, 39)
[1994Liu] Liu, J.P., De Boer, F.R., De Chatel, P.F., Coehoorn, R., Buschow, K.H.J., “On the 4f-3d
Exchange Interaction in Intermetallic Compounds”, J. Magn. Magn. Mater., 132, 159-179
(1994) (Magn. Prop., Review, 64)
[1996Mao] Mao, O., Yang, J., Altounian, Z., Ström-Olsen, J.O., “Metastable RFe7 Compounds
(R=Rare Earths and Their Nitrides with TbCu7 Structure)”, J. Appl. Phys., 79(8), 4605-4607
(1996) (Crys. Structure, Magn. Prop., Experimental, 5)
[1996Wan] Wang J.L., Tang, N., Li, W.Z., Qin W.D., Pan, H.Y., Nasunjilegal B., Yang F.M., De Boer,
F.R., “High-field Magnetic Properties of Ho2Fe15M2 Compounds (M = Al, Ga, Ni and Si)”,
J. Magn. Magn. Mater., 159, 357-360 (1996) (Crys. Structure, Magn. Prop.,
Experimental, 9)
[1997Kog] Kogachi, M., Haraguchi, T., “Quenched-in Vacansies in B2-structured Intermetallic
Compound FeAl”, Mater. Sci. Eng. A, A230, 124-131 (1997) (Crys. Structure,
Experimental, 23)
[1998Ali] Aliravci, C.A., Pekgueleryuez, M.O., “Calculation of Phase Diagrams for the Metastable
Al-Fe Phases Forming in Direct-Chill (DC)-Cast Aluminium Alloy Ingots”, Calphad, 22
(2), 147-155 (1998) (Calculation, Equi. Diagram, 20)
[1998Hag] Hagmusa I.H., Brueck E., de Boer F.R., Buschow K.H.J., “Magnetic Properties of RFe4Al8Compounds Studied by Specific Heat Measurements”, J. Alloy. Compd., 278, 80-82 (1998)
(Magn. Prop., Experimental, 9)
[1998Sch] Schaefer, W., Kockelmann, W., Jansen, E., Fredo, S., Gal, J., “Structural Characteristics of
Rare Earth (R = Tb, Ho, Er) Ternary Magnetic Intermetallics RFexAl12-x with Iron
Concentrations x = 6”, Mater. Sci. Forum, 278-281, 542-547 (1998) (Crys. Structure, Magn.
Prop., Experimental, 14)
[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10 (Ln = Y, La-Nd,
Sm, Cd-Lu and T = Fe, Ru, Os) with YbFe2Al10 Type Structure and Magnetic Properties of
the Iron-Containing Series”, J. Mater. Chem., 8(1), 125-130 (1998) (Crys. Structure, Magn.
Prop., Experimental, 31)
271
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Al–Fe–Ho
[1998Yel] Yelon, W.B., Luo, H., Chen, M., Chang, W.C., Tsai, S.H., “A Neutron Diffraction
Structural Study of R2Fe17-xAlx(C) (R = Tb, Ho) Alloys”, J. Appl. Phys., 83(11), 6914-6916
(1998) (Crys. Structure, Experimental, 14)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-Rich Fe-Al
Alloys”, Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 15)
[1999Wan] Wang, J.Y., Shen, B.G., Wang, F.W., Wen, L.X., Zhang, S.Y., Zhang, H.W., Sun, Z.G.,
Zhan, W.S., Zhang, L.G., “Magnetocrystalline Anisotropy of Ho2(Co1-xFex)15Al2Compounds”, J. Phys.: Condens. Matter, 11, 5539-5546 (1999) (Crys. Structure, Equi.
Diagram, Experimental, Magn. Prop., 33)
[2000Hag] Hagmusa, I.H., Brueck, E., de Boer, F.R., Buschow, K.H.J., “A Specific-Heat Study of
some RFe4Al8 Compounds (R = Ce, Pr, Nd, Dy, Ho, Tm)”, J. Alloy. Compd., 298, 77-81
(2000) (Crys. Structure, Experimental, Thermodyn., 16)
[2000Pai] Paixao, J.A., Silva, M.R., Sorensen, S.A., Lebech, B., Lander, G.H., Brown, P.J., Langridge,
S., Talik, E., Goncalves, A.P., “Neutron-Scattering Study of the Magnetic Structure of
DyFe4Al8 and HoFe4Al8”, Phys. Rev. B, 61(9), 6176-6188 (2000) (Crys. Structure,
Experimental, Magn. Prop., 17)
[2001Ike] Ikeda, O., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
BCC Phases in the Fe-Rich Portion of hte Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Equi. Diagram, Thermodyn., Experimental, 18)
[2001Sch] Schaefer, W., Halevy, I., “Neutron Powder Diffraction of Iron-Rich Rare
Earth-Iron-Aluminium Intermetallics RFe7Al5 (R = Tb, Dy, Ho, Er)”, Mater. Sci. Forum,
378-381, 414-419 (2001) (Crys. Structure, Experimental, Magn. Prop., 12)
[2001Yan] Yanson, T., Manyako, M., Bodak, O., Cerny, R., Yvon, K., “Effect of Aluminium
Substitution and Rare-Earth Content on the Structure of R2(Fe1-xAlx)17 (R = Tb, Dy, Ho,
Er) Phases”, J. Alloy. Compd., 320, 108-113 (2001) (Crys. Structure, Equi. Diagram,
Experimental, 9)
[2002Ram] Rama Rao, K.V.S., Ehrenberg, H., Markandeyulu, G., Varadaraju, U.V., Venkatesan, M.,
Suresh, K.G., Murthy, V.S., Schidt, P.C., Fuess, H., “On the Structural and Magnetic
Properties of R2Fe(17-x)(A, T)x (R = Rare Earth; A = Al, Si, Ga; T = Transition Metal)
Compounds”, Phys. Status Solidi A, 189(2), 373-388 (2002) (Crys. Structure, Magn. Prop.,
Review, 51)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)” MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart, to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 58)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
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Al–Fe–Ho
( Fe)
1538-1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)
1394-912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2, 1993Kat]
dissolves up to 1.2 at.% Al
( Fe)
< 912
cI2
Im3m
W
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
pure Fe at 25°C [Mas2]
dissolves up to 45.0 at.% Al at 1310°C
0 - 18.8 at.% Al, HT [1958Tay]
0 - 19.0 at.% Al, HT [1961Lih]
0 - 18.7 at.% Al, 25C° [1999Dub]
(Ho)
< 1474
hP2
P63/mmc
Mg
a = 357.78
c = 561.78
[Mas2]
Fe4Al13< 1160
mC102
C2/m
Fe4Al13
a =1552.7 to 1548.7
b = 803.5 to 808.4
c =1244.9 to 1248.8
=107.7 to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
74.16 - 76.70 at.% Al [1986Gri]
sometimes called FeAl3 in the literature
at 76.0 at.% Al [1994Gri]
Fe2Al5< 1169
oC24
Cmcm
-
a = 765.59
b = 641.54
c = 421.84
at 71.5 at.% Al [1994Bur]
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75
= 73.27°
= 96.89°
at 66.9 at.% Al [1993Kat]
1102 - 1232
cI16? a = 598.0 at 61 at.% Al [1993Kat]
FeAl
< 1310
cP8
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5 - 47.5 at.% Al [1961Lih]
36.2 - 50.0 at.% Al [1958Tay]
39.7 - 50.9 at.% Al [1997Kog] 500°C
quenched in water
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
~24 -~37 at.% Al [2001Ike]
23.1 - 35.0 at.% Al [1958Tay]
24.7 - 31.7 at.% Al [1961Lih]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [1993Kat]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
273
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Al–Fe–Ho
FeAl6 oC28
Cmc21FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
metastable
85.7 at.% Al [1993Kat]
[1998Ali]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[1998Ali]
Ho2Al
<1018
oP12
Pnma
Co2Si
a = 652.8
b = 505.3
c = 934.7
[V-C2]
Ho3Al2<994
tP20
P42nm
Gd3Al2
a = 818.2
b = 752.5
[V-C2]
HoAl
<1115
oP16
Pbcm
AlDy
a = 580.1
b = 1133.9
c = 562.1
[V-C2]
Ho(FexAl1-x)2
HoAl2<1530
cF24
Fd3m
Cu2Mg a = 781.6
0 x 0.35 (0 to 23 at.% Fe)
[1974Oes, 1975Dwi]
[V-C2]
HoAl3<1087
hR60
R3m
HoAl3
a = 605.9
c = 3586
[V-C2]
Ho(Fe1-xAlx)2
HoFe2<1285
cF24
Fd3m
MgCu2 a = 730.14
0 x 0.35 (0 to 23 at.% Al)
[1974Oes,1975Dwi]
[1993Oka]
HoFe3<1293
hR36
R3m
PuNi3
a = 510.97
c = 245.26
[1993Oka]
Ho6Fe23<1332
cF116
Fm3m
Th6Mn23
a = 120.32 [1993Oka]
Ho2(Fe1-xAlx)17
Ho2Fe17<1343
hP38
P63/mmc
Th2Ni17 a = 843.4
c = 828.4
a = 843.5 to 855.6
c = 828.8 to 838.0
a = 849.61
c = 831.45
a = 852.26
c = 832.78
a = 854.2
c = 834.1
0 x 0.3 (x(Al) = 0.0 - 0.27)
[2001Yan]
at x=0.0 [1993Oka]
at x(Al)=0.0-0.20
(from graph in [2001Yan])
at x=0.059 [1998Yel]
Ho2Fe16Al1at x=0.118 [1998Yel]
Ho2Fe15Al2at x=0.118, T=143°C
Ho2Fe15Al2 [1996Wan]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
274
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Ho
HoFe7 hP8
P6/mmm
TbCu7
a = ~487
c = ~418
metastable phase [1996Mao]
(lattice parameters from graph)
* 1, Ho(Fe1-xAli)2
HoFeAl
hP12
P63/mmc
MgZn2 a = 536.2
c = 870.6
0.375 x 0.55(25 to 36 at.% Al)
[1971Rya]
at x = 0.33 [1974Oes, 1975Dwi]
* 2, Ho2(Fe1-xAlx)17 hP8
P6/mmm
TbCu7 a = 495.0 to 496.0
c = 419.0 to 420.5
0.25 x 0.33 (x(Al) = 0.22 - 0.30)
[2001Yan]
at x(Al) = 0.21 - 0.25
(from graph in [2001Yan])
* 3, Ho2(Fe1-xAlx)17 hR57
R3m
Th2Zn17 a = 859.49
c = 1256.50
a = 864.3 to 866.0
c = 1260
0.30 x 0.45(x(Al) = 0.26-0.40)
[2001Yan]
at x = 0.24 [1998Yel]
HoFe13Al4at x(Al) = 0.30-0.32
(from graph in [2001Yan])
* 4, Ho(FexAl1-x)12 tI26
I4/mmm
ThMn12 a = 874.9
c = 504.9
a = 866.9
c = 500.5
a = 862.5
c = 502.3
a = 865.7
c = 504.4
a = 863.6
c = 498.5
a = 861.0
c = 499.7
0.33 x 0.50 [1971Rya]
[1981Fel, 1988Che]
at x = 0.33 [1976Bus]
HoFe4Al8neutron diffr. at RT [2000Pai]
HoFe4Al8[1988Che]
HoFe6Al6neutron diffr. at 27°C
HoFe6Al6 [1998Sch]
[1980Fel]
HoFe6Al6neutron diffr. at 20°C
HoFe7Al5 [2001Sch] (metastable?)
* 5, HoFe2Al10 oP52
Cmcm
YbFe2Al10
a = 895.3
b = 1013.7
c = 899.7
[1998Thi]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/ References
275
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Ho
20
40
60
80
20 40 60 80
20
40
60
80
Ho Fe
Al Data / Grid: at.%
Axes: at.%
τ5
τ4
τ1
HoAl3
HoAl2
HoFe2 Ho6Fe23Ho2Fe17
FeAl
FeAl2
Fe2Al5
Fe4Al13
Fe3Al
(Fe)
τ2
τ3
?
?
HoFe3
(Al)Fig. 1: Al-Fe-Ho.
Isothermal section at
500°C
276
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Al–Fe–La
Aluminium – Iron – Lanthanum
Riccardo Ferro, Paola Riani, Laura Arrighi
Literature Data
Literature data up to 1986 have been reported and discussed by [1992Gri], and in the following summarized.
[1968Zar] studied an isothermal section at 500°C up to about 33.3 at.% La, investigating 101 ternary alloys.
Alloys were arc-melted on a water cooled Cu hearth under argon using 99.98 mass% Al, 99.99 mass% Fe
and 98.9 mass% La, with 0.8% other rare earth metals. The alloys were then annealed at 500°C for 2000 h,
quenched and studied by metallographic and X-ray powder diffraction techniques. Subsequently
[1993Tan], and [1995Tan1] investigated the system in the complete range of compositions. The alloys were
repeatedly melted by arc furnace in a purified argon atmosphere. The ingots, sealed in silica ampoules under
vacuum were annealed at 500 to 900°C for several weeks and cooled in the furnace; samples were mainly
analyzed by X-ray powder diffraction analysis. Following compounds have been reported: LaFeAl by
[1968Zar, 1971Oes], LaFe4Al8 by [1974Viv] and [1976Bus], La2Fe7Al10 and LaFe6Al6 by [1982Fel],
La(Fe1-xAlx)13 by [1986Hel] and [1986Pal]. Moreover [1982Erm] reported partial and integral enthalpies
of formation of liquid alloys.
Crystal structures of some intermediate phases and a tentative phase equilibria description in the (Fe,Al)
rich region of the system was presented by [1997Sri]. Alloys of a total weight of 1-2 g were melted in an
arc furnace under argon from 99.9 mass% purity elements; cast and annealed (800°C for 120 h) alloys were
examined by X-ray powder diffraction.
Alloys with composition R6Fe11Al3 (R = La, Ce, Pr, Nd, Sm) were prepared and studied by [1992Hu]: the
samples were prepared by arc melting and annealed at 600-800°C for 120 h and quenched.
Alloys with composition LnT2Al10 (Ln = Y, La-Nd, Sm, Gd-Lu and T = Fe, Ru, Os) have been prepared
and studied by X-ray diffraction and magnetic measurement [1998Thi].
The isothermal section at room temperature suggested by [2001Rag] mainly on the basis of [1995Tan1], is
shown in Fig. 1.
Binary Systems
The accepted Al-Fe phase diagram [2003Pis] is mainly based on the assessment by [1993Kat], except for
the Fe-rich region where the ordering equilibria between the ( Fe), FeAl and Fe3Al solid solutions have
been recently investigated by [2001Ike].
The other accepted binary systems are: Al-La from [2003Gro], based mainly on the papers by [1996Sac,
2000Yin, 2001Bor], and Fe-La assessed by [1997Zha]. This simple eutectic system presents an unusual
liquidus flattening.
Solid Phases
Crystal structure data of the phases identified in isothermal section determination and in the preparation of
specific alloys are given in Table 1.
[1968Zar] reported a phase ( 9) with a homogeneity range: LaFe1.4-1Al0.6-1 with unknown structure; the
existence of a phase, with unknown structure, at a composition close to LaFeAl was confirmed by
[1971Oes]. In his investigation [1995Tan1] proposed the La36Al20Fe44 (at.%) composition (see Fig. 1).
The ThMn12 type structure was investigated at the composition LaFe4Al8 [1974Viv, 1976Bus] and
LaFe3.5Al8.5 [1997Sri]; a different unknown structure was proposed for LaFe2Al10 by [1968Zar].
The Th2Zn17 structure type corresponds to 4 La2(Fe1-xAlx)17 with 0.35 x 0.41 [1968Zar], subsequently
described as a stoichiometric phase La2Fe7Al10 [1995Tan1].
The NaZn13 type cubic structure 1,La(FexAl1-x)13 has been investigated by several authors: [1968Zar,
1982Fel, 1986Hel, 1995Tan1, 1997Sri, 1999Moz]. Different ranges of composition have been proposed for
the homogeneity field of this phase, as reported in Table 1. For specific compositions data have been
277
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Al–Fe–La
reported by [1982Fel] and [1999Moz] who studied also the occupation of N in LaFe11Al2 after
nitrogenation.
The crystal structure of 5,La6Fe11Al3 was studied by [1992Hu] as pertaining to the I4/mcm space group.
The crystal structure of 6,LaFe2Al10 was studied by [1998Thi] as pertaining to the Cmcm space group. The
crystal structure of LaFe2Al8 was studied by [2000Tam] as pertaining to the Pbam space group. The
structural transition from cubic to orthorhombic and magnetic properties of La6Fe13-xAlx (x = 6.7) were
studied by [1995Tan2].
Finally the following compounds with unknown structures have been observed: by [1968Zar] ~LaFe2Al7(possibly corresponding to LaFe2Al8 [2000Tam]), by [1995Tan1] LaFe1.2Al7.8, and by [1997Sri]
La2Fe2Al15 (possibly corresponding to 6,LaFe2Al10 [1998Thi]) and La5Fe6Al4 (possibly corresponding
to 7).
Isothermal Sections
An isothermal section in the range 0 to 33.3 at.% La at 500°C was constructed by [1968Zar]. These data
were accepted, with some changes in the compositions of some phases, in the assessment by [1992Gri].
[1992Gri] changed the homogeneity range of the La(FexAl1-x)13 (NaZn13 type phase) from
0.462 x 0.539 to 0.46 x 0.92 according to data of [1986Hel] and changed the stoichiometry of the
Al-richest Al-La phase from LaAl4 to La3Al11.
The evaluation by [2001Rag] was based on [1995Tan1]: however the isothermal section was redrawn by
[2001Rag] to agree with the binary data. On the Al-Fe edge [1995Tan1] reported only FeAl and FeAl2 as
point compounds and on the Al-La edge included La3Al which on cooling undergoes a eutectoid
decomposition [1996Sac]. The version by [2001Rag] is shown in Fig. 1.
Notes on Materials Properties and Applications
Mössbauer measurements on the LaFe2Al8 phase have been carried out by [2000Tam] at temperature from
78 to 300 K and in applied magnetic fields up to 1.05 T.
Magnetic properties of the phase LaFe4Al8 have been studied experimentally by neutron diffraction at
temperatures between 1.5 and 240 K by [1998Sch] and theoretically, applying symmetry analysis, by
[2000Sik].
Magnetic properties of the phases La(FexAl1-x)13 have been investigated by several authors: [1986Pal] by
means of neutron diffraction and magnetostriction measurements; [1998Guo] calculating the magnetic
properties and the electronic structures for x = 0.69, 0.91, 1.0; [2000Iri] for 0.861 x 0.869 by means of
a SQUID magnetometer; [2000Moz] for x = 0.83 by means of high resolution neutron powder
diffractometry at 15 K; [2001Iri1] for x = 0.89 by means of electrical and magnetic resistivity
measurements; [2001Iri2] studying the effect of pressure on the magnetic properties; [2001Iri3] studying
the effect of the hydrogenation on the magnetic state of La(Fe0.88Al0.12)13.
The magnetic and transport properties of La6Fe11Al3 have been studied by means of SQUID magnetometer
and/or neutron diffraction by [1998Gro, 2000Wan] and [2002Jon] (La6Fe11-xAl3+x with x = 0, 1, 2).
Magnetic properties of the phase LaFe2Al10 have been investigated by [1998Thi]. This phase is Pauli
paramagnetic.
References
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-Rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids, 6, 16-37 (1958) (Crys. Structure,
Experimental, 49)
[1961Lih] Lihl, F., Ebel, H., “X-Ray Examination of the Constitution of Iron-Rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenwes., 32, 483-487, (1961) (Crys.
Structure, Experimental, 12)
[1965Bus] Buschow, K.H.J., Phillips Res. Rep., 20, 337 (1965) (Equi. Diagram, Thermodyn.,
Experimental) as quoted by [2000Yin] and by [2003Pis]
278
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–La
[1968Zar] Zarechnyuk, O.S., Emes-Misenko, E.I., Ryabov, V.R., Dikiy, I.I., “Investigation of the
Phase Composition of La-Fe-Al Alloys”, Russ. Metall. (Engl. Transl.), (3), 152-154 (1968),
translated from Izv. Akad. Nauk SSSR, Met., (3), 219-221 (1968) (Crys. Structure, Equi.
Diagram, Experimental, 6)
[1971Oes] Oesterreicher, H., “Structural Studies of Rare-Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Crys. Structure, Experimental, 6)
[1974Viv] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12-type Structure in R-Fe-Al
Systems” (in Russian), Tezisy. Dokl. -Vses. Konf. Kristallokhim. Intermet. Soedin., R.M.
Rykhal (Ed.), Vol. 2nd, Gos. Univ., Lvov, 41 (1974) (Crys. Structure, Experimental, 0)
[1976Bus] Buschow, K.H.J., van Vucht, J.H.N., van den Haagenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth 3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50(1), 145-150 (1976) (Crys. Structure, Experimental, 2)
[1982Erm] Ermakov, A.F., Esin, Yu.O., Gel’d, P.V., “Partial and Integral Enthalpies of Formation of
Liquid Alloys of Iron Monoaluminide with Yttrium, Lanthanum and Cerium”, Russ. Metall.
(Engl. Transl.), (5), 56-58 (1982), translated from Izv. Akad. Nauk SSSR, Met., (5), 69-70
(1982) (Thermodyn., Experimental, 3)
[1982Fel] Felner, I., Nowik, I., “Magnetic Properties of RM6Al6 (R = Light Rare Earth, M = Cu, Mn,
Fe)”, J. Phys. Chem. Solids, 43(5), 463-465 (1982) (Crys. Structure, Experimental, Magn.
Prop., 4)
[1986Hel] Helmholdt, R.B., Palstra, T.T.M., Nieuwenhuys, G.J., “Magnetic Properties of
La(FexAl1-x)13 Determined via Neutron Scattering and Moessbauer Spectroscopy”, Phys.
Rev. B, Condens. Matter, B34(1), 169-173 (1986) (Crys. Structure, Experimental, 17)
[1986Gri] Griger, A., Syefaniay, V., Turmeze, T., “Crystallographic Data and Chemical Compositions
of Aluminum-Rich Al-Fe Intermetallic Phases”, Z. Metallkd., 77, 30-35 (1986) (Equi.
Diagram, Crys. Structure, Experimental, 23)
[1986Gsc] Gschneidner, K. A., Calderwood, “Intra Rare Earth Binary Alloys: Phase Relationships,
Lattice Parameters and Systematics“ F. W., Handbook of the Physics and Chemistry of Rare
Earths, Gschneidner, K.A., Eyring, L. (Eds.), Vol. 8, North-Holland Physics Publishing,
Amsterdam, pp. 1-161 (1986) (Review)
[1986Pal] Palstra, T.T.M., Nieuwenhuys, G.J., Mydosh, J.A., Helmholdt, R.B., Buschow, K.H.J.,
“Neutron Diffraction and Magnetostriction of Cubic La(FexAl1-x)13 Intermetallic
Compounds”, J. Magn. Magn. Mater., 54-57, 995-96 (1986) (Crys. Structure, Magn. Prop.,
Experimental, 5)
[1992Gri] Grieb, B., “Aluminium-Iron-Lanthanum”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.16121.1.20, (1992) (Crys. Structure, Equi. Diagram,
Assessment, 9)
[1992Hu] Hu, B.P., Coey, J.M.D., Klesnar, H., Rogl, P., “Crystal Structure, Magnetism and 57Fe
Moesbauer Spectra of Ternary RE6Fe11Al3 and RE6Fe13Ge Compounds”, J. Magn. Magn.
Mater., 117, 25-231 (1992) (Crys. Structure, Experimental, Magn. Prop., Moessbauer, 14)
[1993Kat] Kattner, U.R., Burton, B.P., “Al-Fe (Aluminum-Iron)”, Phase Diagrams of Binary Iron
Alloys, Okamoto, H. (Ed.), ASM International, Materials Park, OH, 12-28 (1993) (Equi.
Diagram, Review, 99)
[1993Tan] Tang, W.H., Liang, J.K., Yan, X.H., Yie, S.S., “Subsolidus Relations of the La-Fe-Al
Ternary System and Magnetic Phase Realtion of La(FexAl1-x)13 Solid Solution”, Proc. 17th
Nat. Symp. Phase Diagrams, 4-7 (1993) (Equi. Diagram, Experimental) as quoted by
[1997Eff]
[1994Bur] Burkhardt, U., Grin, J., Ellner, M., Peters, K., “Structure Refinement of the Iron-Aluminium
Phase with the Approximate Composition Fe2Al5”, Acta Crystallogr., B50, 313-316 (1994)
(Crys. Structure, Experimental, 9)
279
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–La
[1994Gri] Grin, J., Burkhardt, U., Ellner, M., Peters, K., “Refinement of the Fe4Al13 Structure and its
Relationship to Quasihomological Homotypical Structures”, Z. Kristallogr., 209, 479-487
(1994) (Crys. Structure, Experimental, 39)
[1995Tan1] Tang, W., Liang, J., Rao, G., Guo, Y., Zhao, Y., “Subsolidus Phase Relations of the
La-Fe-Al Ternary System” J. Alloys Compd., 218, 127-130 (1995) (Crys. Structure, Equi.
Diagram, Experimental, 20)
[1995Tan2] Tang, W., Liang, J., Yang, Y., Zhou, Y., Yan, X., Xie, S., “Structural Transition and
Magnetic Properties of La6Fe13-xAlx Intermetallic Compounds”, Prog. Nat. Sci., 5(6),
747-52 (1995) quoted in [C.A.] 124:182135g
[1996Sac] Saccone, A., Cardinale A., Delfino S., Ferro R., “Phase Equilibria in the Rare Earth Metals
(R)-Rich Regions of the R-Al Systems (R = La - Ce - Pr - Nd)”, Z. Metallkd., 87(2), 82-86
(1996) (Crys. Structure, Equi. Diagram, Experimental, 18)
[1997Eff] Effenberg, G., Bodak, O.I., Petrova, L.A., Red Book. Constitutional Data and Phase
Diagrams of Metallic Systems (Summaries of the publication year 1993), MSI GmbH,
Stuttgart, Vol. 38 (1997)
[1997Kog] Kogachi, M., Haraguchi, T., “Quenched-in Vacansies in B2-Structured Intermetallic
compound FeAl”, Mater. Sci. Eng. A, A230, 124-131 (1997) (Crys. Structure,
Experimental, 23)
[1997Sri] Srinivasan, S., Raman, A., Ferrel, R.E.Jr., Grenier, C.G., “Lanthanum-Containing Ternary
Solid Solutions with NaZn13-, ThMn12- and Th2Zn17-Type Crystal Structures”,
Z. Metallkd., 88(6), 474-479 (1997) (Equi. Diagram, Crys. Structure, Experimental, Magn.
Prop., Review, 22)
[1997Zha] Zhang, W., Li, C., “The Fe-La (Iron-Lanthanum) System”, J. Phase Equilib., 18(3) 301-304
(1997) (Equi. Diagram, Review, 19)
[1998Ali] Aliravci, C.A., Pekgueleryuez, M.O., “Calculation of Phase Diagrams for the Metastable
Al-Fe Phases Forming in Direct-Chill (DC)-Cast Aluminium Alloy Ingots”, Calphad, 22,
147-155 (1998) (Calculation, Equi. Diagram, 20)
[1998Gro] Groot de, C.H., Buschow, K.H.J., Boer de, R.F., “Magnetic Properties of R6Fe13-xM1+x
Compounds and Their Hydrides”, Phys. Rev. B, Condens. Matter, 57(18), 11472-11482
(1998) (Crys. Structure, Experimental, Magn. Prop., 34)
[1998Guo] Guo, Y.Q., Yu, R.H., Zhang, R.L., Zhang, X.H., Tao, K., “Calculation of Magnetic
Properties and Analysis of Valence Electronic Structures of LaT13-xAlx (T = Fe, Co)
Compounds”, J. Phys. Chem. B, B102(1), 9-16, (1998) (Calculation, Magn. Prop., Electr.
Prop., 30)
[1998Lei] Leineweber, A., Jacobs, H., “Preparation of Single Crystals of LaAl and X-Ray Structure
Determination”, J. Alloys Compd., 278, L10-L12 (1998) (Crys. Structure, Experimental, 11)
[1998Sch] Schobinger-Papamantellos, P., Buschow, K.H.J., Ritter, C., “Magnetic Ordering and Phase
Transitions of RFe4Al8 (R = La, Ce, Y, Lu) Compounds by Neutron Diffractioin”, J. Magn.
Magn. Mater., 186, 21-32 (1998) (Crys. Structure, Experimental, Magn. Prop., 13)
[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10(Ln = Y, La = Nd,
Sm, Gd = Lu and T=Fe, Ru, Os) with YbFe2Al10 Type Structure and Magnetic Properties
of the Iron-Containing Series“, J. Mater. Chem., 8(1), 125-130 (1998) (Crys. Structure,
Magn. Prop., Experimental, 31)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-Rich Fe-Al
Alloys”, Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 15)
[1999Moz] Moze, O., Kockelmann, W., Liu, J.P., de Boer, F.R., Buschow, K.H.J., “Structure and
preferred site occupation of N in the compound LaFe11Al2 after nitrogenation”, J. Magn.
Magn. Mater., 195, 391-395 (1999) (Crys. Structure, Experimental, 13)
[2000Iri] Irisawa, K., Fujita, A., Fukamichi, K., “Magnetic Phase Diagram of La(FexAl1-x) 3 in the
Vicinity of the Ferromagnetic-Antiferromagnetic Phase Boundary”, J. Alloys Compd., 305,
17-20 (2000) (Crys. Structure, Experimental, Magn. Prop., 15)
280
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–La
[2000Moz] Moze, O., Kockelmann, W., Liu, J.P., de Boer, F.R., Buschow, K.H.J., “Magnetic Structure
of LaFe10.8Al2.2 and LaFe10.8Al2.2N3 Cluster Compounds”, J. Appl. Phys., 87(9),
5284-5286 (2000) (Crys. Structure, Experimental, Magn. Prop., 13)
[2000Sik] Sikora, W., Schobinger-Papamantellos, P., Buschow, K.H.J., “Symmetry Analysis of the
Magnetic Ordering in RFe4Al8 (R = La, Ce, Y, Lu and Tb) Compounds (II)”, J. Magn.
Magn. Mater., 213, 143-156 (2000) (Calculation, Crys. Structure, Magn. Prop., 8)
[2000Tam] Tamura, I., Mizushima, T., Isikawa, Y., Sakurai, J., “Mössbauer Effect and Magnetization
Studies of CeFe2Al8 and LaFe2Al8”, J. Magn. Magn. Mater., 220, 31-38 (2000) (Crys.
Structure, Experimental, Moessbauer, 4)
[2000Yin] Yin, F., Su, X., Li, Z., Huang, M., Shi, Y., “A Thermodynamic Assessment of the La-Al
System”, J. Alloys Compd., 302, 169-172 (2000) (Assessment, Equi. Diagram, Thermodyn.,
14)
[2000Wan] Wang, F., Zhang, P., Shen, B., Yan, Q., “Transport Properties of R6Fe11Al3 Compounds (R
= La, Nd)”, J. Appl. Phys., 87(9), 6043-6045 (2000) (Experimental, Magn. Prop., 10)
[2001Bor] Borzone, G., Parodi, N., Ferro, R., Bros, J.P., Dubes, J.P., Gambino, M., “Heat Capacity and
Phase Equilibria in Rare Earth Alloy System. R-Rich R-Al Alloys (R = La, Pr and Nd)”,
J. Alloys Compd., 320(2), 242-250 (2001) (Equi. Diagram, Thermodyn., Experimental, 36)
[2001Iri1] Irisawa, K., Fujita, A., Fukamichi, K., Mitamura, H., Goto, T., “Magnetic Phase Transition
in the Antiferromagnetic Compound La(Fe0.89Al0.11)13”, J. Alloys Compd., 327, 17-20
(2001) (Crystal Structure, Magn. Prop., Experimental, 10)
[2001Iri2] Irisawa, K., Fujita, A., Fukamichi, K., Mitamura, H., Goto, T., “Effect of Pressure on
Magnetic Properties of La(FexAl1-x) 13 Ferromagnetic Compounds”, J. Alloys Compd., 329,
42-46 (2001) (Crys. Structure, Magn. Prop., Experimental, 24)
[2001Iri3] Irisawa, K., Fujita, A., Fukamichi, K., Yamazaki, Y., Iijima, Y., Matsubara, E., “Change in
the Magnetic State of Antiferromagnetic La(Fe0.88Al0.12)13 by Hydrogenation”, J. Alloys
Compd., 316, 70-74 (2001) (Crys. Structure, Magn. Prop., Experimental, 24)
[2001Ike] Ikeda, O., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
bcc Phases in the Fe-Rich Portion of hte Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Equi. Diagram, Termodyn., Experimental, 18)
[2001Rag] Raghavan, V., “Al-Fe-La (Aluminum-Iron-Lanthanum)”, J. Phase Equilib., 22(5), 566-567
(2001) (Equi. Diagram, Crys. Structure, Review, 6)
[2002Jon] Jonen, S., Rechenberg, H.R., Campo, J., “Rare Earth Effects on the Magnetic Behavior of
R6Fe11-xAl3+x Compounds”, J. Magn. Magn. Mater., 242-245, 803-805 (2002) (Crys.
Structure, Magn. Prop., Experimental, 7)
[2003Gro] Gröbner, J., “Al-La (Aluminium-Lanthanum)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 23)
[2003Pis] Pisch, A., “Al-Fe (Aluminium-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 58)
281
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–La
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( La)
918-865
cI2
Im3m
W
a = 426.0 [1986Gsc]
( La)
865-310
cF4
Fm3m
Cu
a = 530.3 [1986Gsc]
( La)
< 310
hP4
P63/mmc
La
a = 377.4
c = 1217.1
[1986Gsc]
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
( Fe)
1538-1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)
1394-912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2, 1993Kat]
dissolves up to 1.2 at.% Al
( Fe)
< 912
cI2
Im3m
W
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
pure Fe at 25°C [Mas2]
dissolves up to 45.0 at.% Al at 1310°C
0 - 18.8 at.% Al, HT [1958Tay]
0 - 19.0 at.% Al, HT [1961Lih]
0 - 18.7 at.% Al, 25°C [1999Dub]
Fe4Al13
< 1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7 to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
74.16-76.70 at.% Al [1986Gri]
at 76.0 at.% Al [1994Gri]
Fe2Al5< 1169
oC24
Cmcm
Fe2Al5
a = 765.59
b = 641.54
c = 421.84
at 71.5 at.% Al [1994Bur]
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [1993Kat]
282
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–La
1232-1102
cI16? a = 598.0 at 61 at.% Al [1993Kat]
FeAl
< 1310
cP8
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5 - 47.5 at.% Al [1961Lih]
36.2 - 50.0 at.% Al [1958Tay]
39.7 - 50.9 at.% Al [1997Kog] 500°C
quenched in water
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
24 - 37 at.% Al [2001Ike]
23.1 - 35.0 at.% Al [1958Tay]
24.7 - 31.7 at.% Al [1961Lih]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [1993Kat]
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
metastable
85.7 at.% Al [1993Kat]
[1998Ali]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[1998Ali]
La3Al
~520-400
hP8
P63/mmc
Ni3Sn
a = 722.8
c = 551.7
[1965Bus]
LaAl
< 873
oC16
Cmcm
CeAl
a = 945.5
b = 775.3
c = 579.1
[1998Lei]
LaAl2< 1405
La(FexAl1-x)2
cF24
Fm3m
MgCu2
a = 814.2
a = 814.7
a = 811.1
at x = 0 [1965Bus]
0 x 0.2 at 25°C [1995Tan1]
at x = 0 [1995Tan1]
at x = 0.2 [1995Tan1]
LaAlx1240-1090
hP3
P63/mmm
AlB2
a = 447.8
c = 434.7
x ≅ 2.3
[1965Bus]
LaAl3< 1170
hP8
P63/mmc
Ni3Sn
a = 666.4
c = 461.5
[1965Bus]
La3Al11
1240-915
tI10
I4/mmm
BaAl4
a = 445.6
c = 1033
[1965Bus]
La3Al11
< 915
oI28
Immm
La3Al11
a = 443.3
b = 1315
c = 1013
[1965Bus]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
283
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–La
* 1, La(FexAl1-x)13 cF112
Fm3c
NaZn13
a =1197 to 1183
a =1196
a = 1173.8 to 1157.9
a = 1198.3 to 1166.8
a = 1199 to 1174
a = 1162.81
0.462 x 0.539 [1968Zar]
[1982Fel] for LaFe6Al60.46 x 0.92 [1986Hel] (range in
which the phase may be stabilized)
0.44 x 0.82 [1995Tan1]
0.425 x 0.575 [1997Sri]
[1999Moz] at x = 0.84
* 2, LaFe4Al8
LaFe3.5Al8.5
tI26
I4/mmm
ThMn12
a = 890.0
c = 507.5
a = 882
c = 519
a = 892
c = 510
[1976Bus]
[1968Zar]
A composition range included between
62 and 65 at.% Al at 800°C was shown
in a partial tentative phase diagram by
[1997Sri]
* 3, LaFe2Al8
~LaFe2Al7
oP44
Pbam
CeFe2Al8
a = 1257
b = 1445
c = 406.3
[2000Tam]
observed in La10Fe17.5Al72.5
[1968Zar]
* 4, La2(FexAl1-x)17 hR57
R3m
Th2Zn17
a = 905 to 899
c = 1313 to 1304
a = 896.2
c = 1298
a = 869.0
c = 1300
0.35 x 0.41 [1968Zar]
at x = 0.41 [1995Tan1]
at x = 0.41 [1982Fel]
* 5, La6Fe11Al3 tI80
I4/mcm
La6Co11Ga3
a = 822.3
c = 2382.1
[1992Hu]
* 6, LaFe2Al10
LaFe1.2Al7.8
La2Fe2Al15
oC52
Cmcm
YbFe2Al10
?
?
a = 905.1
b = 1024.9
c = 912.2
[1968Zar, 1998Thi]
[1995Tan1] observed as unknown
structure phase
[1997Sri] observed as unknown
structure phase
* 7, La(Fe1-xAlx)2
LaFeAl
La36Fe44Al201
La5Fe6Al4
? 0.3 x 0.5 (33.3 at.% La, 46.7-33.3
at.% Fe) [1968Zar]
x = 0.5 (33.3 at.% La, 33.3 at.% Fe)
[1971Oes]
[1995Tan1]
[1997Sri]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
284
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–La
20
40
60
80
20 40 60 80
20
40
60
80
La Fe
Al Data / Grid: at.%
Axes: at.%
τ6Fe4Al13
Fe2Al5
FeAl2
τ7
τ1
La3Al11
LaAl3
LaAl2
LaAl
(αFe)
(αLa)
τ2
τ4
(Al)Fig. 1: Al-Fe-La.
The isothermal section
at room temperature
suggested by
[2001Rag], mainly on
the basis of
[1995Tan1]
285
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mg
Aluminium – Iron – Magnesium
Ibrahim Ansara†, Michael Hoch, Nigel Saunders, Eberhard E. Schmid, updated by Ibrahim Ansara
†, Yong
Du and Patrick Wollants
Literature Data
By adding Mg to liquid iron ductile iron alloys can be obtained with much improved mechanical properties.
This alkaline metal is also used as an addition in liquid steels for desulfurization, deoxidation and also for
control and modification of non-metallic inclusions. Most of the experimental phase diagram data were
determined in the aluminium-rich corner, limited by the section Fe4Al13-Mg2Al3. [1934Fus] determined the
fields of primary crystallization by metallography. [1938Bar] analyzed 34 alloys by DTA and
metallography. They observed that an as-cast alloy containing about 10.4 mass% Mg and 3.2 mass% Fe,
which had been annealed below the eutectic temperature, 435°C, was two-phase (with an Al-rich solid
solution and Fe4Al13) whereas the as-cast sample contained substantial ternary eutectic. [1938Hof] by
X-ray diffraction compared the pattern of Fe4Al13 in an alloy on the Fe4Al13-Mg2Al3 section with that of
pure Fe4Al13 and could not find any difference in the lattice parameters. Thus he concluded that, in the four-
phase equilibrium, no magnesium dissolves in Fe4Al13. [1941Phi] studied the constitution of alloys of
aluminium in detail in the composition range 0 to 5 mass% Mg and 0 to 2.5 mass% Fe, using thermal
analysis and metallography. He also redetermined the position of the monovariant line, liquidus, solidus,
solvus and invariant temperatures. The alloys were not in thermodynamic equilibrium because [1941Phi]
studied them in the as-cast state. [1958Gul], by thermal analysis, determined some liquidus temperatures
along the section Fe4Al13-Mg2Al3 as well as the microstructure for selected alloy compositions. The only
available information for the Mg-rich corner concerns the solubility in the liquid state versus temperature
which was determined by [1944Bee] and confirmed later by [1951Bak]. [1984Age] measured the solubility
of Mg in Fe-rich liquid Al-Fe alloys at 1600°C. No ternary compounds have been identified in this system.
Binary Systems
Phase diagram of the Al-Mg binary system is accepted from the evaluation by [2003Luk]. The Al-rich part
of the Al-Fe system is taken from [Mas] or from [1982Kub], whereas [1981Sch] was chosen for the Al-rich
phase boundaries of the Al-Mg system. The non-stoichiometry range of Fe4Al13 (also designated as FeAl3)
is not well defined (0.745 < xAl < 0.766) [Mas2]. The solubility range of Al (molar fraction) ranges from
0.385 to 0.403. The decomposition of Fe4Al13 at ~ 1152°C could be congruent [1986Len] but remains
uncertain.
Solid Phases
Table 1 lists the solid phases of the partial system (Al)-Mg2Al3-Fe4Al13. No ternary compounds have been
identified.
Pseudobinary Systems
[1934Fus] and [1958Gul] consider “Fe4Al13”-Mg2Al3 to be a pseudobinary section of nearly degenerate
type. However, according to the accepted binary diagrams this is not quite the case. [1958Gul] noted
thermal arrests at approximately 650 and 550°C in addition to the 451°C eutectic arrest. No explanation was
given for the higher-temperature thermal effects.
Invariant Equilibria
According to [1934Fus, 1938Bar, 1938Hof, 1941Phi], there is a eutectic reaction
L (Al)+“Fe4Al13”+Mg2Al3 in the Al-rich corner whose temperature is very close to the l (Al)+Mg2Al3binary eutectic. [1938Bar] suggested that the iron content in the ternary eutectic liquid was 3.0 mass% Fe
286
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mg
at 445°C (3 K lower than the measured binary eutectic). In later work [1934Fus] and [1958Gul] proposed
that in fact the amount of iron is much smaller. [1958Gul] refers to the solubility of “Fe4Al13” in the liquid
state of the section to Mg2Al3 as ~ 0.2% at 500°C. In the reviews of [1961Phi] and [1976Mon], the values
of the iron composition are given as 0.14 mass% and approximately 0.15 mass%, respectively. Within
experimental errors, the temperature of the ternary eutectic is indistinguishable from that of the binary
Al-Mg2Al3 eutectic. In addition, [1961Phi] quotes that the composition of the Al solid solution at the
eutectic contains ~ 15 mass% Mg and 0.05 mass% Fe. The invariant reaction is therefore considered to be
degenerate, as shown in the reaction scheme, Fig. 1.
Liquidus Surface
In his review, [1961Phi] presented the liquidus surface for the Al-rich alloys based on his earlier work
[1941Phi]. Nine alloys were analyzed by sampling the liquid after equilibrating at various fixed
temperatures between 650 and 700°C (Fig. 2). Figure 3 presents the solidus surface.
Isothermal Sections
From the solubility measurements of [1941Phi] at the eutectic temperature, the solubility of both iron and
magnesium in the Al-rich solid solution is virtually unchanged. Based on this observation, an isothermal
section at 400°C was constructed, as shown in Fig. 4.
Temperature – Composition Sections
[1941Phi] presents three isopleths (1.0 mass% Fe, 1.0 mass% Mg, 4.0 mass% Mg) for Al-rich alloys,
determined by thermal analysis. Liquidus, solidus and solvus temperatures were thus measured. Some
solidus temperatures were determined by a heating-quench method. The measured ternary eutectic
temperature is equal to 451°C, which is in agreement with [1958Gul] experiments, who used thermal
analysis for alloy compositions in the “MgAl3-Fe4Al13” section, which is nearly of a degenerate type.
However, there are inconsistencies in [1941Phi]. The limiting binary systems defined by this section are
substantially different from the accepted Al-Mg diagram. Due to these inconsistencies, no figures are
reproduced.
Miscellaneous
Solubility curves for magnesium-rich alloys were determined by [1944Bee] by sampling equilibrated liquid
alloys. His results are shown in Figs. 5 and 6. For the iron-rich corner, the solubility curve at 1600°C from
[1984Age] is presented in Fig. 7. The effect of Al on the solubility of Mg in liquid Fe at 1600°C was
measured by a vapor-molten Fe equilibration method [1996Li]. The equation lnxMg = 9.73+12.30xAl fits
the data. From these measurements the interaction coefficient (MgAl) as derived from
the-Margules-Wagner formalism is equal to 12.30. By rapid solidification and consolidation, the increase
of Mg concentration in Al-Fe-Mg alloys leads to a decrease of the maximum solid solubility extension
[1994Abr]. The maximum solubility for the Al-4Mg-Fe (at.%) alloys is 2 at.%, and for a Al-6Mg (at.%) the
maximum solubility is only equal to 1 at.% Fe [1994Abr].
References
[1934Fus] Fuss, V., “Metallography of Aluminium and its Alloys” (in German), Springer Verlag,
Berlin, 141-142 (1934), translated Anderson R.J., The Sherwood Press Inc. Cleveland,
(1936) (Equi. Diagram, Experimental, 300)
[1938Bar] Barnick, M., Hanemann, H., “A Contribution to the Knowledge of the
Aluminium-Iron-Magnesium System” (in German), Aluminium, 20, 771-774 (1938) (Equi.
Diagram, Experimental, 4)
[1938Hof] Hofmann, W., “X-ray Methods for the Investigation of Aluminium Alloys” (in German),
Aluminium, 7, 865-872 (1938) (Crys. Structure, Equi. Diagram, Experimental, 19)
287
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mg
[1941Phi] Phillips, H.W.L., “The Constitution of Alloys of Aluminium with Magnesium and Iron”,
J. Inst. Met., 67, 275-287 (1941) (Equi. Diagram, Experimental, 8)
[1944Bee] Beerwald, A., “On the Solubility of Iron and Manganese in Magnesium and in Magnesium
- Aluminium Alloys” (in German), Metallwirtschaft, 23, 404-407 (1944) (Equi.Diagram,
Experimental, #, 10)
[1951Bak] Baker, W.A., Eborall, M.D., “Note on the Solubility of Iron in Liquid
Magnesium-Aluminium Alloys”, Metallurgia, 44, 145-146 (1951) (Experimental, 2)
[1958Gul] Gul'din, I.T., Dokukina, N.V., “The Aluminium-Magnesium-Iron-Silicon System”,
J. Inorg. Chem., 3, 359-378 (1958), translated from Zh. Neorg. Khim., 3, 799 (1958) (Equi.
Diagram, Experimental, #, 5)
[1961Phi] Phillips, H.W.L., “Equilibrium Diagrams of Aluminium Alloy Systems”, The Aluminium
Development Association, London, 84-86 (1961) (Equi. Diagram, Review, 0)
[1976Mon] Mondolfo, L.F., “Aluminium Alloys: Structure and Properties”, Butterworths,
London-Boston (1976) (Equi. Diagram, Review, Phys. Prop., Crys. Structure)
[1981Sch] Schürmann, E., Voss, H.-J., “Investigation of the Melting Equilibria of Lithium-Aluminium
Alloys. IV. Melting Equilibria of the Binary Magnesium-Aluminium System” (in German),
Giessereiforschung, 33, 43-46 (1981) (Equi. Diagram, Experimental, #, 17)
[1982Kub] Kubaschewski, O., “Iron Binary Phase Diagrams”, Springer Verlag, Berlin (1982) (Equi.
Diagram, Review)
[1984Age] Ageev, Yu.A., Archugov, S.A., “On the Solubility of Mg in Liquid Fe and Some Fe-based
Binary Liquid Alloys”, Russ. Metall., (3), 72-74 (1984), translated from Izv. Akad. Nauk
SSSR, Met., (3), 78-80 (1984) (Experimental, #, 6)
[1986Len] Lendvai, A., “Phase Diagram of the Al-Fe System up to 45 mass% Iron”, J. Mater. Sci., 5,
1219-1220 (1986) (Equi. Diagram, Experimental, 7)
[1990Sau] Saunders, N., “A Review and Thermodynamic Assessment of the Al-Mg and Mg-Li
Systems”, Calphad, 14, 61-70 (1990) (Equi. Diagram, Thermodyn., Review, Theory, 59)
[1994Abr] Abramov, V.O., Sommer, F., “Structure and Mechanical Properties of Rapidly Solidified
Al-(Fe,Cr) and Al-Mg-(Fe,Cr) Alloys”, Mater. Lett., 20, 251-255 (1994) (Experimental,
Crys. Structure, Mechan. Prop., 6)
[1996Li] Li, X., Song, B., Han, Q., “Thermodynamic Properties of Liquid Fe-Mg-Al and Fe-Mg-Si
Dilute Ternary Solutions”, J. Phase Equilib., 17, 21-23 (1996) (Equi. Diagram,
Experimental, 11)
[2003Luk] Lukas, H.L., “Al-Mg (Aluminium-Magnesium)”, MSIT Binary Evaluation Program, in
MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 49)
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Al–Fe–Mg
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group
Prototype
Lattice Parameters
[pm]
Comments/ References
(Al) cF4
Fm3m
Cu
a = 404.88 pure Al at 24°C [V-C]
Fe4Al13
1152
mC102
C2/m
Fe4Al13
a = 1548.9
b = 808.31
c = 1247.6
= 107.72°
[V-C]
0.745 < xAl < 0.766
Mg2Al3 cF1832
Fd3m
Mg2Al3
a = 2823.9 [V-C]
Fig. 1: Al-Fe-Mg. Reaction scheme
A-B-CFe4Al
13 - Al Al - Mg
2Al
3"Fe
4Al
13 - Mg
2Al
3"Al - Fe - Mg
l (Al)+Fe4Al
13
652 e1
l (Al)+Mg2Al3
450 e2
l Fe4Al
13+Mg
2Al
3
450 e3
L (Al)+Mg2Al
3, Fe
4Al
13450 D
(Al)+Fe4Al
13+Mg
2Al
3
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Al–Fe–Mg
2
4
6
8
10
0
0
1 2 3 4 5 6
520°C
540
560
580
600
620
640
(Al)+Fe Al4 13
AlFe, mass%
Mg,mass%
Fig. 3: Al-Fe-Mg.
Solidus surface
[1961Phi]
2
4
6
8
10
0
0
1 2 3 4 5 6
Al Fe, mass%
Mg,mass%
610°C
615
620
625
630
635
640
645
650
655
67
5
700
725
750
775
800
825 850
Fe Al134
(Al)
Fig. 2: Al-Fe-Mg.
Liquidus surface
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Al–Fe–Mg
10
20
30
10 20 30
70
80
90
Mg 40.00Fe 0.00Al 60.00
Mg 0.00Fe 40.00Al 60.00
Al Data / Grid: at.%
Axes: at.%
Mg2Al3
(Al)
Fe4Al13
(Al)+Mg2Al3+Fe4Al13
0
0
0.01
0.02
0.03
0.04
0.05
0.06
0.07
1 2 3 4 5 6 7
Al, mass%
Fe,mass%
800°C
750
700
660
Fig. 4: Al-Fe-Mg.
Isothermal section of
the Al-rich corner at
400°C
Fig. 5: Al-Fe-Mg.
Solubility curves of
Fe in Mg-rich alloys
at constant
temperature
[1944Bee]
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Al–Fe–Mg
10
90
10
Mg 20.00Fe 80.00Al 0.00
Mg 0.00Fe 80.00Al 20.00 Data / Grid: at.%
Axes: at.%
L1
L1+L2
Fe
0.010 0.02 0.03 0.04 0.05 0.06 0.07
700
750
800
Fe, mass%
Temperature,°C
7 2.7 1 0
Fig. 7: Al-Fe-Mg.
Position of the L1/
(L1+L2) phase
boundary in Fe-rich
Al-Fe-Mg alloys at
1600°C [1984Age]
Fig. 6: Al-Fe-Mg.
Solubility curves of
Fe with respect to
temperature for
selected alloy
compositions
[1944Bee]
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Al–Fe–Mn
Aluminium – Iron – Manganese
Quingsheng Ran, updated by Alexander Pisch
Literature Data
This system has been the object of a number of investigations, but, partly because of the limitation in
composition ranges interested and partly because of the complicated boundary binary systems, the
constitution has not been established for the whole system. Most investigations are confined to the Fe-Mn
side and to the Al rich-corner. Solid solubilities of several binary intermediate phases, order-disorder
transition of some alloys, some magnetic and quasicrystalline phases were also investigated. The
constitution has been reviewed from time to time [1939Han, 1943Mon, 1952Han, 1961Phi, 1980Bra,
1983Riv, 1994Rag].
The most important experimental phase diagram works are [1933Koe, 1939Deg, 1943Phi, 1974Mur,
1974Shv, 1977Cha, 1981Bra, 1984Den, 1990Liu2, 1990Xu, 1992Xu, 1993Hao, 1993Liu1, 1993Liu2,
1997Mue], whereas [1944Ray, 1950Phr, 1952Han, 1959Sch, 1960Tsu, 1962Tsu, 1974Fau, 1975Urs,
1978Urs, 1987Den, 1990Liu1] provided additional information related to phase equilibria. Mostly pure Al
(~ 99.9% or higher) was used, whereas Mn and Fe were added as master alloys. Methods used are:
metallography [1933Koe, 1939Deg, 1943Phi, 1974Shv, 1977Cha, 1981Bra, 1984Den, 1990Liu2, 1990Xu,
1992Xu, 1992Liu, 1993Liu1, 1993Liu2, 1997Mue]; X-ray diffraction [1939Deg, 1974Mur, 1977Cha,
1981Bra, 1990Xu]; dilatometry [1933Koe]; thermal analysis [1939Deg, 1943Phi, 1993Hao, 1993Liu2];
electron microprobe [1984Den, 1990Liu2, 1990Xu, 1992Xu, 1992Liu, 1993Liu1, 1993Liu2] and diffusion
couples [1990Liu2, 1992Liu, 1993Liu1, 1993Liu2].
Binary Systems
The binary systems Al-Fe and Al-Mn are accepted from [2003Pis1] and [2003Pis2], respectively. The
Fe-Mn binary phase diagram has been taken from [1993Oka].
Solid Phases
The solid phases ( Fe) and ( Mn) form a continuous solid solution extended from Fe-Mn side in the
direction to the Al corner.
The solid solutions of Al in ( Fe) and ( Mn) form a continuous range of solid solutions above temperatures
1000 to 1200°C. This may also be true for lower temperatures, but there is no experimental work clarifying
this question.
The binary compound MnAl6 can dissolve a considerable amount of Fe [1939Deg, 1944Ray, 1950Phr,
1973Kow, 1975Bar, 1984Den, 1994Ser, 1995Ser, 1998Wei]. Generally these investigations agree on
solubility up to Mn0.5Fe0.5Al6. Only [1984Den] gave a value of Mn0.25Fe0.75Al6, significantly higher than
the other studies. [1944Ray] stated this as a replacement of Mn by Fe atom by atom. Lattice parameters for
the solid solutions were determined by several studies. The solubility of Fe increases with falling
temperature [1987Den].
In the Fe4Al13 phase the solubility of Mn is also due to substitution of Fe by Mn [1944Ray]. The amount of
dissolved Mn in this phase reported by [1944Ray] and [1984Den] is approximately 3 at.%. [1994Ser,
1995Ser, 1998Wei] reported a value of 5 at.% Mn at 550°C at the Al rich boundary, which is higher than
that given as “quite low” by other investigations [1939Deg, 1943Phi, 1950Phr, 1952Han, 1974Mur]. A
maximum solubility value of 9.5 at.% Mn can be reached at 550°C for lower Al contents in the ternary
[1998Wei].
[1960Tsu] and [1962Tsu] reported a ferromagnetic phase, called , with the compositions range 35 to 47.5
Mn, 40 to 47.5 Al and 10 to 17.5 at.% Fe, with the CsCl type structure.
[1969Ily] studied the MnFe2Al alloy by X-ray diffraction. After annealing at 650°C for several hours, a new
phase with the composition Mn6Fe9Al5 precipitated. Its structure was determined as Mn type. [1987Lu]
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obtained a precipitate with the composition Mn6Fe9Al5 from an alloy Fe-9.1 Al-29.9 Mn-2.9 mass% Cr.
This was proposed to be a ternary phase. Its crystal structure has been determined to be similar to Mn, but
not the same. The space group was given as P4332. [1975Zal] and [1977Ath] also studied the structure of
alloys of similar compositions, but suggested ordering to the CsCl type by cooling to between 700 and
750°C and another ordering to the MnCu2Al type between 500 and 600°C [1975Zal]. The structural
characteristics of alloys with this composition need still to be clarified. Earlier [1937Moe] and [1939Deg]
suggested ternary phases with unknown compositions. However, their existence was denied by later works
[1939Deg, 1944Ray].
[1964Var] reported the determination of joint solubilities of Mn and Fe in solid (Al) by X-ray analysis. The
results report Al to dissolve 1.5 mass% Mn and 1.5 mass% Fe simultaneously. This, however, is
incompatible with the accepted binary solubilities of Fe and Mn in solid (Al), which are significantly less.
(Al) should dissolve 0.62 at.% Mn and nearly no Fe, as reported by [1939Deg] and [1952Han].
Several papers deal with a decagonal phase, at a composition (Mn0.7Fe0.3)2Al7 [1986Dub, 1987Ma,
1987Wou, 1988Pau, 1988Sch]. This alloy and the alloys at compositions Mn2Al7 and Fe2Al7 are 5-fold
twins and there are 1664 atoms in an orthorhombic unit cell in 16 icosahedral clusters of 104 atoms with the
lattice parameters a = 3286, b = 3123 and c = 2480 pm [1988Pau].
[1998Wei] reported the existence of four new ternary phases in the Al-rich corner at 550°C: 1,
Mn1-xFexAl4 with unknown structure, 2, (MnxFe1-x)4Al13 being isostructural to the high temperature
modification of Fe4Al13, 3,(Mn1-xFex)3Al10 which is of the Mn3Al10 type and 4, (Mn1-xFex)Al3-x with a
Mn4Al11(HT) type structure. 4 is probably not a true ternary phase, because the binary equivalent is stable
at higher temperatures.
Mn substitution in the ordered B2 FeAl phase has been studied theoretically by [1999Mek] and
experimentally using the ALCHEMI (Atom Location by Channeling Enhanced Microanalysis) technique
by [1997And]. Conclusion could be made that Mn atoms substitute mainly on Fe sites in the phase lattice.
[1986Sch] claimed a single phase decagonal quasicrystal in an Mn18Fe2Al80 alloy.
The quasicrystalline icosahedral phase of the approximate Mn14-xFexAl86 composition with fivefold
symmetry was obtained in rapidly solidified alloys by [1993Nis, 1995Sin] and by mechanical alloying in
[1999Sch, 2000Sch].
Invariant Equilibria
So far two invariant equilibria have been identified [1939Deg, 1943Phi, 1950Phr, 1952Han, 1984Den,
1987Den, 1995Ser]. Different investigations agree on the temperatures and compositions of the liquid in
these reactions fairly well. [1939Deg] suggested a eutectic reaction L (Al) + Fe4Al13 + (Mn,Fe)Al6 which
was confirmed by later works and a transition reaction L + -MnAl4 (Mn,Fe)Al6 + with being an
unknown ternary phase. [1943Phi] later denied the existence of the phase and established the reaction to
be a peritectic one, L + Fe4Al13 + -MnAl4 (Mn,Fe)Al6. This has found support by later work [1950Phr,
1952Han] and is accepted in this evaluation (see also the section “Liquidus Surface”). The two reactions are
given in Table 2. The temperatures have been taken from the most recent DSC measurements by [1995Ser].
Liquidus Surface
Reports on the liquidus surface are only given for the Al corner [1939Deg, 1943Phi, 1950Phr, 1984Den,
1987Den]. Concerning the invariant reactions and univariant liquid troughs they agree with each other fairly
well, but [1939Deg] and [1943Phi] showed different extensions of the primary region of MnAl6. [1939Deg]
proposed a more extended region of primary solidification of MnAl6 and an unidentified, perhaps ternary,
phase participating in the ternary peritectic reaction. [1943Phi] however presented the MnAl6 primary
solidification closed by a trough between the ternary peritectic and the ternary eutectic reaction and denied
the existence of any ternary phases in the investigated region. The diagram proposed by [1939Deg]
demands quite improbable liquidus isotherms. The liquidus projection of [1943Phi] is supported by
[1950Phr]. Figure 1 shows the liquidus surface projection mainly based on the results of [1943Phi].
[1943Phi] also presented a projection of the surface of secondary separation.
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Isothermal Sections
Isothermal sections constructed are shown in Figs. 2 to 8.
Experimental results on the 1000°C section have been presented by [1974Shv, 1977Cha, 1981Bra,
1990Liu2, 1990Xu, 1992Liu, 1993Liu1, 1993Liu2], whereas [1990Liu1, 1993Liu3] gives a calculated
partial section. [1977Cha, 1981Bra, 1990Liu2] agree with a three-phase equilibrium between ( Fe, Mn),
( Mn) and ( Fe, Mn). [1990Xu] determined only two-phase equilibria between ( Fe, Mn) and
( Fe, Mn), with results in agreement with other experimental works. [1977Cha, 1981Bra, 1990Liu2] give
different Al contents for the phases in this equilibrium. The diffusion couple determination of phase
boundaries by [1990Liu2] is strongly supported by the results of metallography, X-ray analysis and electron
microprobe analysis of [1990Xu, 1992Xu] and does not contradict the measurements of [1981Bra],
although [1981Bra] gives higher Al contents of the phases at equilibrium. The highest Al contents are given
by [1977Cha]. Their results agree qualitatively with the accepted Al-Mn binary but the overall Al contents
seem to be systematically too high. The Al-Mn rich part has been estimated according to their work and the
accepted Al-Mn binary. The equilibrium between ( Mn) and ( Fe, Mn) to the Al-Mn boundary, suggested
by [1990Liu2], is in agreement with the calculation of [1990Xu]. The equilibria ( Fe, Mn)/ determined
by [1990Liu2, 1981Bra] and by [1974Shv] for 1000 to 1150°C are in good agreement. The results are
summarized in Fig. 5. Examination of several samples support the homogeneity range of ( Fe) extending
at least to 30 at.% Mn at 25 at.% Al [1988Per].
Figure 4 shows the partial isothermal section at 1100°C on the Al-poor edge, determined by [1990Liu2,
1992Liu] and [1990Xu], in agreement with the calculation of [1990Liu1, 1993Liu3] adjusted to the
accepted binary systems. The equilibrium between ( Fe, Mn) and ( Fe, Mn) at 1200°C, Fig. 3, is from
[1990Liu2, 1993Liu1] who measured over the whole region, revealing a lower Al content than [1990Xu,
1990Liu1].
[1993Liu2] presented a partial isothermal section at 1300°C with ( Fe, Mn)-L and ( Fe, Mn)-( Fe, Mn)
two phase equilibria at low Al content (Fig. 2).
Equilibria between ( Fe, Mn), ( Fe, Mn) and ( Mn) are also determined for 900 and 800°C [1990Xu,
1992Xu], 760°C [1959Sch] and 850, 750, 650°C [1974Shv], showing similar equilibrium relationships, but
with decreasing Mn contents with falling temperature for the three-phase equilibrium. Those for 760°C
[1959Sch] and for 800°C [1990Xu] are in very good agreement and are shown in Fig. 6. The ( Fe) - FeAl
order-disorder transformation was missing in the original works and has been added tentatively in Fig. 2, 5
and 6.
[1974Mur] proposed an isothermal section for 600°C from X-ray phase analysis. This work has not been
taken into account in the present evaluation due to strong deviations from the accepted binary systems.
The equilibria including the ferromagnetic phase at 700°C have been established by [1997Mue] by
metallography and optic emission spectroscopy. The phase is in equilibrium with 2 and ( Mn). The
partial isothermal section is redrawn in Fig. 7.
[1994Ser, 1995Ser, 1998Wei] determined the partial isothermal section in the Al rich corner at 550°C.
[1995Ser] claimed in their extensive study, that equilibrium is not attained even after 3000h of anneal and
that the phases and their composition depend on the solidification path. This has not been confirmed in
[1998Wei] where equilibria seem not to depend on initial conditions. There are some contradictions
between the text and the published diagram in [1998Wei]. They have been corrected according to the
accepted binaries and the solid phases table given by [1998Wei]. The modified isothermal section of
[1998Wei] is presented in Fig. 8.
Temperature – Composition Sections
A series of vertical sections have been investigated: 2 and 6 mass% Mn and 4 mass% Fe [1943Phi]; 4, 7, 10
mass% Al [1974Shv]; 2, 10, 30 mass% Al, 20 mass% Mn and 40 mass% Fe [1933Koe]; 45 at.% Al
[1975Urs, 1978Urs]. Among these only the 2 mass% Mn of [1943Phi] can be considered as acceptable; the
others contradict either the isothermal sections or the phase rule or differ strongly from the accepted binary
systems. The partial section at 2 mass% Mn is redrawn in Fig. 9, and Fig. 10 gives an amended partial
section with 4 mass% Fe.
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Notes on Materials Properties and Applications
[1990Wer] investigated decagonal (Mn0.7Fe0.3)Al7 and icosahedral Al80Mn20-xFex samples by Mössbauer
spectroscopy. The latter compound obeys the Hume-Rothery rule on alloy stability for x = 9. The magnetic
properties of metastable ferromagnetic Mn60-xFexAl40 thin films prepared by DC magneton sputtering have
been determined by [1991Mat]. The saturation magnetization and coercitivity increased compared to pure
Mn60Al40 with a maximum at x = 0.05 to 0.1. [2001Gon] studied the magnetic properties of the same alloys
by Mössbauer, and ac susceptibility with x ranging from 20 to 60 on samples obtained by mechanical
alloying for 48 hours. A magnetic phase diagram has been drawn at low temperature: alloys with x < 40
show paramagnetic behavior at room temperature and become ferromagnetic for x > 45. [1997Zam1,
1997Zam2, 2002Ric] measured the magnetic properties of Mn0.7-xFexAl0.3 (0.4 < x < 0.58) by means of57Fe Mössbauer spectroscopy and magnetic ac susceptibility on samples prepared either by arc melting
under Ar and annealed at 1000°C or by mechanical alloying [2002Ric]. A magnetic phase diagram has been
proposed based on the experimental results and theoretical calculations using a mean-field normalization
group method to the Ising model. [1998Abu] performed magnetization measurements on MnxFeAl1-x (0.27
< x < 0.6) samples from 85K to 300K up to 8 kOe. The compound is paramagnetic for x < 0.31 and becomes
ferromagnetic for x > 0.35 and the magnetic susceptibility obeys the Curie-Weiss law with negative
paramagnetic temperature. [2000Res1, 2000Res2] performed magnetic ordering measurements by XRD,
Mössbauer, high and low field magnetization measurements as well as magnetic susceptibility on
Mn0.1Fe0.9-xAlx alloys. A tentative magnetic phase diagram as function of temperature has been established
and compared to theoretical calculations. [2000Zam] studied the magnetic properties of a Mn0.3FexAl0.7-x
solid solution by Mössbauer spectroscopy, ac magnetic susceptibility and magnetization measurements for
0.275 < x < 0.525.
Miscellaneous
The crystallization behavior of rapidly quenched (Mn,Fe)Al6 alloys has been examined by [1986Wan]. The
Al activity of an Fe-1% Al-2% Mn alloy has been discussed by [1980Sud].
The diffusion behavior of Mn impurities through a Al-Fe layer has been studied by [1998Akd]. Mn
increases the activity coefficient of Al and tends also to increase the thickness of the reaction layer.
References
[1933Koe] Koester, W., Tonn, W., “The Iron Corner of the Iron-Manganese-Aluminium System” (in
German), Arch. Eisenhuettenwes., 7, 365-366 (1933) (Equi. Diagram, Experimental, 1)
[1937Moe] Moeckel, E., “The Al-Mg Alloys in Micrograph” (in German), Aluminium, 19(7), 433-439
(1937) (Experimental, 6)
[1939Deg] Degischer, E., “The Aluminium Corner of the Ternary System Aluminium - Iron -
Manganese” (in German), Aluminium-Archiv, 18, 5-19 (1939) (Equi. Diagram,
Experimental, 4)
[1939Han] Hanemann, H., Schrader, A., “On Several Ternary Aluminium Systems” (in German),
Aluminium, 21(5), 381-383 (1939), and Z. Metallkd., 31(6), 183-185 (1939) (Equi.
Diagram, Review, 5)
[1943Mon] Mondolfo, L.F., “Metallography of Aluminum Alloys”, John Wiley & Sons, Inc., New York,
92-93 (1943) (Equi. Diagram, Review, 1)
[1943Phi] Phillips, H.W.L., “The Constitution of Alloys of Aluminium with Manganese, Silicon and
Iron. I. - The Binary System: Aluminium-Manganese. II. - The Ternary Systems:
Aluminium-Manganese-Silicon and Aluminium-Manganese-Iron”, J. Inst. Met., 69,
275-316 (1943) (Equi. Diagram, Experimental, 25)
[1944Ray] Raynor, G.V., “The Effect on the Compound MnAl6 of Iron, Cobalt and Copper”, J. Inst.
Met., 70, 531-542 (1944) (Equi. Diagram, Experimental, 15)
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Al–Fe–Mn
[1950Phr] Phragmen, G., “On the Phases Occurring in Alloys of Aluminium with Copper, Magnesium,
Manganese, Iron and Silicon”, J. Inst. Met., 77, 489-552 (1950) (Equi. Diagram,
Experimental, 67)
[1952Han] Hanemann, H., Schrader, A., Ternary Alloys of Aluminium (in German), Verlag Stahleisen
m.b.H., Düsseldorf, 103-105 (1952) (Equi. Diagram, Experimental)
[1959Sch] Schmatz, D.J., “Formation of -Manganese-Type Structure in Iron-Aluminum-Manganese
Alloys”, Trans. Met. Soc. AIME, 215, 112-114 (1959) (Equi. Diagram, Experimental, 8)
[1960Tsu] Tsuboya, I., Sugihara, M., “On the Ferromagnetism in Manganese-Aluminium-Iron
System”, J. Phys. Soc. Jpn., 15, 1534 (1960) (Equi. Diagram, Experimental, 3)
[1961Phi] Phillips, H.W.L., “Al-Fe-Mn”, in “Equilibrium Diagrams of Aluminium Alloy Systems”,
Vol. 25, Aluminium Development Association, London, 87-88 (1961) (Equi. Diagram, 0)
[1962Tsu] Tsuboya, I., Sugihara, M., “The Magnetic Phase in Mn-Al-Co, -Cu, -Fe and -Ni Ternary
Alloys”, J. Phys. Soc. Jpn., 17, Suppl. BI, 172-175 (1962) (Crys. Structure, Experimental, 5)
[1964Var] Varivoda, I.Kh., Polesya, A.F., “Study of the Simultaneous Solubility of Fe and Mn in Al”
(in Russian), Tsvet. Met., (6), 98-103 (1964) (Experimental, 7)
[1969Ily] Il'yushin, A.S., Zakharova, M.I., “Structural Changes on Disintegration of the
Supersaturated Solid Solution Fe2MnAl”, Phys. Met. Metallogr., 28(5), 204-207 (1969),
translated from Fiz. Met. Metalloved., 28(5), 955-958 (1969) (Crys. Structure,
Experimental, 4)
[1973Kow] Kowatschewa, R., Dafinowa, R., Kamenowa, Z., Momtschilov, E., “Metallographic
Determination of Intermetallic Compounds in Aluminium Alloys”, Prak. Metallogr., 10(3),
131-143 (1973) (Crys. Structure, Experimental, 9)
[1974Fau] Faulring, G.M., Forgeng, W.D., Pappas, N.J., “Examination of Manganese-Aluminum
Alloys Containing up to 2.0% Iron”, “Light Metals”, Proc. 103rd AIME Annual Meeting,
Vol. 2, Forberg, H. (Ed.), New York, 547-569 (1974) (Experimental, 10)
[1974Mur] Muravyova, A.A., Zarechnyuk, O.S., Ryabov, V.R., “Investigation of the
Manganese-Iron-Aluminium System” (in Russian), Vestn. L'vov. Univ. Khim., 16, 3-4
(1974) (Equi. Diagram, Experimental, 8)
[1974Shv] Shvedov, L.I., Goretskii, G.P., “Structure of Fe-Mn-Al Alloys” (in Russian), in “Struktura
i Svoistva Met. i Splavov”, Nauka i Tekhn., Minsk, 199-204 (1974) (Equi. Diagram,
Experimental, 6)
[1975Bar] Barlock, J.G., Mondolfo, L.F., “Structure of Some Aluminium - Iron - Magnesium -
Manganese - Silicon Alloys”, Z. Metallkd., 66, 605-611 (1975) (Equi. Diagram, Crys.
Structure, Experimental, 7)
[1975Urs] Ursache, M., “Contributions to the Study of Some Magnetic Materials from the Al-Mn-Fe
System” (in Romanian), Cercet. Metal., 16, 489-500 (1975) (Experimental, 6)
[1975Zal] Zalutskiy, V.P., Nesterenko, Y.G., Osipenko, I.A., “Investigation of Ordering Processes in
the Alloy Fe2MnAl”, Phys. Met. Metallogr., 39(5), 113-119 (1975), translated from Fiz.
Met. Metalloved., 39, 1026-1032 (1975) (Crys. Structure, Experimental, 6)
[1977Ath] Athanassiadis, G., Le Caer, G., Foct, J., Rimlinger, L., “Study of Ternary Ordered Solid
Solutions Derived from Fe3Al by Substitution”, Phys. Status Solidi A, 40A, 425-435 (1977)
(Crys. Structure, Experimental, 20)
[1977Cha] Chakrabarti, D.J., “Phase Stability in Ternary Systems of Transition Elements with
Aluminum”, Metall. Trans. B, 8B, 121-123 (1977) (Equi. Diagram, Experimental, 13)
[1978Urs] Ursache, M., “Studies of the Possibilities of Using Some Alloys of the Al-Mn-M System for
the Fabrication of Permanent Magnets” (in Romanian), Bul. Inst. Politech. Bucuresti Chim.
Met., 40(3), 105-112 (1978) (Experimental, 9)
[1980Bra] Brandes, E.A., Flint, R.F., “Mn-Al-Fe”, in “Manganese Phase Diagrams”, Manganese
Centre, Paris, 80-81 (1980) (Equi. Diagram, Review, 4)
[1980Sud] Sudavtsova, V.S., Batalin, G.I., “Aluminium Activity in Liquid Iron Alloys” (in Russian),
Ukr. Khim. Zh., 46(3), 268-270 (1980) (Thermodyn., Experimental, 8)
297
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
[1981Bra] Branco, J.R.T., Boratto, F.J.M., “The Austenite Phase Field in the Fe-Mn-Al System at
1000°C” (in Portuguese), 36th Annual Congress of ABM, Vol. 1, Recife, Mexico, 5-10 July
1981, 175-185 (Publ. 1981) (Equi. Diagram, Experimental, 12)
[1983Riv] Rivlin, V.G., “Phase Equilibria in Iron Ternary Alloys. 12: Critical Review of Constitution
of Aluminium-Iron-Manganese and Iron-Manganese-Silicon Systems”, Int. Met. Rev.,
28(6), 309-337 (1983) (Equi. Diagram, Review, 61)
[1984Den] Denholm, W.T., Esdaile, J.D., Siviour, N.G., Wilson, B.W., “Crystallization Studies in the
Aluminium-Rich Corner of the Aluminium-Iron-Manganese System”, Metall. Trans. A,
15A, 1311-1317 (1984) (Equi. Diagram, Experimental, 6)
[1986Dub] Dubois, J.-M., Janot, Ch., Pannetier, J., Pianelli, A., “Diffraction Approach to the Structure
of Decagonal Quasi-Crystals”, Phys. Lett. A, 117(8), 421-427 (1986) (Crys. Structure,
Experimental, 21)
[1986Sch] Schaefer, R.J., “The Metallurgy of Quasicrystals”, Scr. Metall., 20(9), 1183-1312 (1986) as
quoted in [1995Sin]
[1986Wan] Wang, R., Gui, J., Yao, S., Cheng, Y., Lu, G., Huang, M., “High-Temperature X-Ray
Diffraction Study of the Crystallization Process in Rapidly Quenched Al6(Mn,Fe) Alloys”,
Phil. Mag. B, 54, L33-L37 (1986) (Experimental, 7)
[1987Den] Denholm, W. T., Esdaile, J.D., Siviour, N.G., Wilson, B.W., “The Nature of the FeAl3Liquid-(FeMn)Al6 Reaction in the Al-Fe-Mn System”, Metall. Trans. A, 18A, 393-397
(1987) (Equi. Diagram, Experimental, 3)
[1987Lu] Lu, T.-H., Liu, T.-F., Wan, C.-M., “X-Ray Structure Determination of Fe9Mn6Al5Precipitate in a Fe-Mn-Al-Cr Alloy”, “Anal. Tech. Mater. Charact.”, Proc. Int. Workshop
1987, 233-241 (Publ. 1987) (Crys. Structure, Experimental, 8)
[1987Ma] Ma, Y., Stern, E.A., “Fe and Mn Sites in Noncrystallographic Alloy Phases of Al-Mn-Fe
and Al-Mn-Fe-Si”, Phys. Rev. B, Condens. Matter, 35B, 2678-2681 (1987) (Crys. Structure,
Experimental, 22)
[1987Wou] Van der Woude, F., Schurer, P.J., “A Study of Quasi-Crystalline Al-Fe Alloys by
Mössbauer-Effect Spectroscopy and Diffraction Techniques”, Can. J. Phys., 65, 1301-1308
(1987) (Crys. Structure, Experimental, 39)
[1988Pau] Pauling, L., “Structure of the Orthorhombic Form of Mn2Al7, Fe2Al7 and (Mn0.7Fe0.3)2Al7that by Twinning Produces Grains with Decagonal Point-Group Symmetry”, Proc. Natl.
Acad. Sci. U.S.A., Vol. 85, 2422-2423 (1988) (Crys. Structure, Experimental, 8)
[1988Per] Perez Alcazar, G.A., Plascak, J.A., Galvao da Silva, E., “Magnetic Properties of Fe-Mn-Al
Alloys in the Disordered Phase”, Phys. Rev. B, Condens. Matter, 38B, 2816-2819 (1988)
(Crys. Structure, Experimental, 17)
[1988Sch] Schurer, P.J., Van Netten, T.J., Niesen, L., “The Structure of Decagonal Al7(Mn1-xFex)2
Alloys”, J. de Physique, 49, 237-241 (1988) (Crys. Structure, Experimental, 17)
[1990Liu1] Liu, X., Hao, S., “Thermodynamic Calculation on the Phase Diagram of the Fe-Mn-Al
System” (in Chinese), Proc. 6th National Symposium on Phase Diagrams, 46-48 (1990)
(Equi. Diagram, Thermodyn., Theory, 4)
[1990Liu2] Liu, X., Sun, R., Hao, S., “Study of Phase Equilibria at 1000, 1100 and 1200°C in the
System Fe-Mn-Al” (in Chinese), Proc. 6th National Symposium on Phase Diagrams,
146-149 (1990) (Equi. Diagram, Experimental, 3)
[1990Xu] Xu, L., Guo, Y., Liang, G., LI, Y., “Experimental Investigation of the Equilibrium Diagram
of Fe Corner in Fe-Mn-Al System” (in Chinese), Proc. 6th National Symposium on Phase
Diagrams, 160-162 (1990) (Equi. Diagram, Experimental, 2)
[1990Wer] Werkman, R.D., Schurer, P.J., van der Woude, F., “Quasicrystals”, Hyperfine Interact.,
53(1-4), 241-251 (1990) (Crys. Structure, Experimental, 50)
[1991Mat] Matsumoto, M., Morisako, A., Ohshima, J., “Properties of Ferromagnetic MnAl Thin Films
with Additives”, J. Appl. Phys., 69(8), 5172-5174 (1991) (Electr. Prop., Experimental,
Magn. Prop., Mechan. Prop., 4)
298
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
[1992Liu] Liu, X., Hao, S., Sun, R., “Isothermal Section at 1000 and 1100°C of Fe-Mn-Al System
Phase Diagram” (in Japanese), Acta Met. Sin.(Jinshu Xuebao) B, 28B(7), B288-B292
(1992) (Experimental, Equi. Diagram, 6)
[1992Xu] Xu, L., Guo, Y., Liang, G., Li, Y., “Determination of the Phase Diagram of Fe-Mn-Al by
Means of EPMA” (in Japanese), Cailiao Kexue Jinzhan, 6(3), 185-189 (1992)
(Experimental, Equi. Diagram, 3)
[1993Hao] Hao, S., Chen, H., Liu, X., “Study of Transverse Section of 4 wt% Al and 8 wt% Al in
Fe-Mn-Al System Phase Diagram” (in Japanese), J. Northeast Univ. Technol (China),
14(2), 150-154 (1993) (Experimental, Equi. Diagram, 5)
[1993Liu1] Liu, X., Shiming, H., “Phase Equilibria and (bcc) Phase Region Continuity at 1000°C in
the Fe-Mn-Al System”, Scr. Metall. Mater., 28(5), 611-616 (1993) (Experimental, Phase
Diagram, 6)
[1993Liu2] Liu, X., Chen, H., Hao, Sh., “Phase Equilibria of the Fe-Mn-Al System at 1200°C and
1300°C” (in Japanese), Dongbei Gongxueyuan Xuebao, 14(3), 249-252 (1993)
(Experimental, Equi. Diagram, 7)
[1993Liu3] Liu, X., Hao, Sh., “A Thermodynamic Calculation of the Fe-Mn-Al Ternary System”
Calphad, 17(1), 79-91 (1993) (Thermodyn., 16)
[1993Nis] Nistor, L.C., Teodorescu, V., Manaila, R., “Disorder in Al-Mn-Fe Icosahedral Alloys
Introduced by Iron”, Microscopy Res. Techniq., 25(2), 183-184 (1993) (Crys. Structure,
Experimental, 8)
[1993Oka] Okamoto, H., “Fe-Mn (Iron-Manganese)” in “Phase Diagrams of Binary Iron Alloys”
Okamoto, H. (Ed.), ASM International Materials Park, OH (USA), 203-213 (1993)
(Review, 184)
[1993Sin] Singh, A., Ranganathan, S., “Quasicrystalline and Crystalline Phases and their Twins in
Rapidly Solidified Al-Mn-Fe Alloys”, J. Non-Cryst. Solids., 153-154, 86-91 (1993) (Crys.
Structure, Experimental, 17)
[1994Rag] Raghavan, V., “The Al-Fe-Mn System”, J. Phase Equilib., 15(4), 410-411 (1994) (Equi.
Diagram, Review, 14)
[1994Ser] Serneels, A., Davignon, G., Niu, X., Lebrun, P., Froyne, L., Verlinden, B., Delay, L., “An
Overview of the Research Activities in the Al-Fe-Mn System”, in “MTM-COST 507”, II,
1-10 (1994) (Experimental, Equi. Diagram, 7)
[1995Ser] Serneels, A., Davignon, G., Verlinden, B., Delaey, L., “Experimental Investigation of
Selected Key Compositions in Order to Detemine the Al-Fe-Mn Phase Diagram” in
“IWT-COST 507”, II, 1-49 (1995) (Experimental, Equi. Diagram, 4)
[1995Sin] Singh, A., Ranganathan, S., “A Transition Electron-Miscroscopic Study of Icosahedral
Twins. 1. Rapidly Solidified Al-Mn-Fe-Alloys”, Acta Metall. Mater., 43(9), 3539-3551
(1995) (Crys. Structure, Experimental, 36)
[1997And] Anderson, I.M., “Alchemi Study of Site Distributins of 3d-Transition Metals in B2-Ordered
Iron Aluminides”, Acta Mater., 45(9), 3897-3909 (1997) (Calculation, Crys. Structure,
Experimental, Theory, 26)
[1997Mue] Mueller, C., Stadelmaier, H.H., Reinsch, B., Petzow, G., “Constitution of Mn-Al-(Cu, Fe,
Ni or C) Alloys Near the Magnetic Phase”, Z. Metallkd., 88(8), 620-624 (1997)
(Experimental, Equi. Diagram, Review, 15)
[1997Zam1] Zamora, L.E., Perez Alcazar, G.A., Bohorquez, A., Marco, J.F., “Magnetic Phase Diagram
of the FexMn0.7-xAl0.3 Alloys Series Obtained by Moessbauer Spectroscopy”, Hyperfine
Interact., 110, 177-182 (1997) (Experimental, 7)
[1997Zam2] Zamora, L.E., Perez-Alcazar, G.A., Bohorquez, A., “Magnetic Properties of the
FexMn0.70-xAl0.30 (0.40 x 0.58) Alloy Series”, J. Appl. Phys., 82(12), 6165-6169 (1997)
(Experimental, Magn. Prop., 14)
[1998Abu] Abu-Aljarayesh, I., Al-Khateeb, S., Said, M.R., “Magnetic Properties of the System
Fe(Al,Mn)”, J. Magn. Magn. Mater., 185(2), 220-224 (1998) (Experimental, Magn. Prop.,
Equi. Diagram, 14)
299
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
[1998Akd] Akdeniz, M.V., Mekhrabon, A.O., “The Effect of Substitutional Impurities on the Evolution
of Fe-Al Diffusion Layer”, Acta Mater., 46(4), 1185-1192 (1998) (Calculation,
Thermodyn., 55)
[1998Wei] Weitzer, F., Rogl, P., Bohn, M., “Phase Relations in the Aluminium Rich Part of the System
Aluminium-Iron-Manganese”, in “COST507, Definition of Thermochemical and
Thermophysical Properties to Provide a Database for the Development of New Light Metal
Alloys”, Vol. 1, 53-57 (1998) (Experimental, Equi. Diagram, Crys. Structure, 13)
[1999Mek] Mekhrabov, A.O., Akdeniz, M.V., “Effect of Ternary Alloying Elements Addition on
Atomic Ordering Characteristics of Fe-Al Intermetallics”, Acta Mater., 47(7), 2067-2075
(1999) (Calculation, Theory, Thermodyn., 63)
[1999Sch] Schurack, F., Eckert, J., Schultz, L., “High-Strength Al-Alloys with Nano-Quasicrystalline
Phase as Main Component”, Nanostruct. Mater., 12, 107-110 (1999) (Experimental, Crys.
Structure, 5)
[2000Sch] Schurack, F., Eckert, J., Schultz, L., “Quasicrystalline Al-Alloys with High Strength and
Good Ductility”, Mater. Sci. Eng. A, 294-296, 164-167 (2000) (Crys. Structure,
Experimental, Mechan. Prop., 6)
[2000Res1] Restrepo, J., Alcazar, P.G.A., “Magnetic Properties of Fe0.9-qMn0.1Alq Disordered Alloys:
Theory”, Phys. Rev. B, 61B(9), 5880-5883 (2000) (Magn. Prop., Theory, 15)
[2000Res2] Restrepo, J., Perez Alcazar, G.A., Ganzalez, J.M, “Magnetic Properties of Disordered
Fe0.9-xMn0.1Alx Alloys”, J. Appl. Phys., 87(10), 7425-7429 (2000) (Crys. Structure,
Experimental, Magn. Prop., Moessbauer, 10)
[2000Zam] Zamora, L.E., Perez Alcazar, G.A., Taberas, J.A., Bohorguez, A., Marco, J.F., Gonzalez,
J.M., “Magnetic Properties of FexMn0.3Al0.7-x (0.275 x 0.525) Disordered Alloys”, J.
Phys.: Condens. Matter, 12, 611-621 (2000) (Experimental, Magn. Prop., Equi. Diagram,
13)
[2001Gon] Gonzales, C., Medina, G., Greneche, J.M., Perez Alcazar, G.A., Surinach, S., Munoz, J.S.,
Baro, M.D., “Magnetic Phase Diagram of the FexMn0.60-xAl0.40 (0.20 x 0.60) Alloys
Mechanically Alloyed for 48 Hours”, Mater. Sci. Forum, 360-362, 565-570 (2001)
(Experimental, Magn. Prop., Moessbauer, Equi. Diagram, 14)
[2002Ric] Rico, M.M., Medina, G., Perez Alcazar, G.A., Munoz, J.S., Surinach, S., Baro, M.D.,
“Magnetic and Structural Properties of Mechanically Alloyed FexMn0.70-xAl0.30 (x = 0.40
and 0.45) Alloys”, Phys. Status Solidi A, 189(3), 811-816 (2002) (Crys. Structure,
Experimental, Magn. Prop., 11)
[2003Pis1] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart, to be published, (2003) (Equi. Diagram, Review, 58)
[2003Pis2] Pisch, A., “Al-Mn (Aluminium-Manganese)”, MSIT Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart, to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 40)
300
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
( Fe)
1538-1394
cI2
Im3m
W
a = 293.15
dissolves up to 10 at.% Mn at 1473°C
[1993Oka]
( Fe, Mn)
< 1394-912
cF4
Fm3m
Cu
a = 364.67
a = 386.0
continuous solid solution,
pure Fe at 915°C [V-C2, Mas2],
dissolves up to 15 at.% Al at 800 C.
pure Mn [Mas2]
( Fe, Mn),
( Fe)
< 1138
cI2
Im3m
W
a = 286.65
a = 286.60 to 289.99
a = 286.60 to 290.12
a = 308.0
pure Fe at 25°C [Mas2]
dissolves up to 45.0 at.% Al at 1310°C
0-19.0 at.% Al, HT [2003Pis1]
0-18.7 at.% Al, 25°C [2003Pis1]
pure Mn
dissolves 9 at.% Fe at 1235°C [1993Oka]
( Mn)
1100-727
cP20
P4132
Mn
a = 631.52 pure Mn [Mas2]
dissolves up to 30 at.% Fe at 700°C
[1993Oka]
( Mn)
< 727
cI58
I43m
Mn
a = 891.26 pure Mn [Mas2]
dissolves up to 30 at.% Fe at 700°C
[1993Oka]
(Mn1-xFex)4Al13-i
< 1160
mC102
C2/m
Fe4Al13
a = 1552.7 - 1548.7
b = 803.5 - 808.4
c = 1244.9 - 1248.8
= 107.7°- 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
a = 1566.15
b = 799.49
c = 1245.61
= 107.6
74.16-76.70 at.% Al, x = 1 [2003Pis1]
sometimes called Fe3Al14 in the literature
at 76.0 at.% Al, x = 1 [2003Pis1]
Mn9.5Fe18Al72.5 [1998Wei]
solubilities at 550°C
0.2 < x < 0.22 and 0 < y < 2.72
Fe4Al13 (h) oB~50
Bmmm
a = 775.10 ± 0.09
b = 403.36 ± 0.05
c = 2377.1 ± 0.3
high temperature modification
by splat cooling. metastable?
[2003Pis1]
301
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
(Mn1-xFex)2Al5-y
< 1169
oC24
Cmcm
-
a = 765.59
b = 641.54
c = 421.84
a = 769.03
b = 642.02
c = 421.61
at 71.5 at.% Al [2003Pis1]
Mn5.9Fe23.6Al70.5 [1998Wei]
solubilities at 550°C:
0 < x < 0.14 at y = 0
0 < x < 0.22 at y = 0.3
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [2003Pis1]
1102 - 1232
cI16? a = 598.0 [2003Pis1]
FeAl
< 1310
cP2
Pm3m
CsCl
a = 289.81 to 291.01
a = 289.76 to 190.78
39.7-50.9 at.% Al [2003Pis1] quenched
from 500°C in water
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
~24-~37 at.% Al [2003Pis1]
23.1-35.0 at.% Al [2003Pis1]
24.7-31.7 at.% Al [2003Pis1]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [2003Pis1]
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
metastable
85.7 at.% Al [2003Pis1]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[2003Pis1]
MnAl12
< 500
cI26
Im3
Al12W
a = 747 [V-C2]
(Mn1-xFex)Al6< 705
oC28
Cmcm
MnAl6
a = 755.51
b = 649.94
c = 887.24
a = 754.5 ± 0.2
b = 649.0 ± 0.3
c = 868.1 ± 0.2
a = 754.5 ± 0.2
b = 649.0 ± 0.3
c = 868.1 ± 0.2
at x = 0 [V-C2]
at x = 0 [2003Pis2]
Mn5.4Fe8.8Al85.8 [1998Wei]
0 < x < 0.6 at 550°C
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
302
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
, MnAl4< 693
hP586
P63/m
a = 2838.2
c = 1238.9
a = 2842.49
c = 1241.61
space group does not fit 100%, probably
P63 [2003Pis2]
Mn18Fe1.6Al80.4 [1998Wei]
, MnAl4< 923
hP574
P63/mmc
MnAl4
a = 1998
c = 2467.3
Mn4Al11 (LT)
< 916
aP30
P1
Mn4Al11
a = 509.5 ± 0.4
b = 887.9 ± 0.8
c = 505.1 ± 0.4
= 89.35 ± 0.04°
= 100.47 ± 0.05°
= 105.08 ± 0.06°
a = 507.11
b = 882.51
c = 505.94
= 89.89°
= 100.52°
= 105.26°
[V-C2]
Mn26.7Fe4Al73.3 [1998Wei]
Mn4Al11 (HT)
916 - 1002 Pna21
a = 1483.7
b = 1245.7
c = 1250.5
at 62.05 at.% Al, designated as MnAl3[2003Pis2]
,
< 1177
cI2Im3m
W
[2003Pis2]
1
< 1048
[2003Pis2]
2, Mn5Al8< 991
hR26
R3m
Cr5Al8
a = 1267.1
c = 793.6
a = 1261.1
c = 792.7
a = 1259.73
c = 790.23
at 63 at.% Al [2003Pis2]
at 55 at.% Al [2003Pis2]
Mn26.7Fe4Al73.3 [1998Wei]
< 1312
hP2
P63/mmc
Mg
a = 270.5 to 270.5
c = 436.1 to 438
44.2 - 44.9 at.% Al [2003Pis2]
- Mn3Al10
< 860
hP26
P63/mmc
Co2Al5
a = 754.6 ± 0.3
c = 289.5 ± 0.2
[2003Pis2]
metastable
D tP2
P4/mmm
CuAu
a = 278 to 279
c = 356 to 357
44.2 - 44.9 at.% Al metastable [2003Pis2]
ico-MnAl icosahedral
m35
80-82 at.% Al
quasicrystal, metastable [2003Pis2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
303
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
Table 2: Invariant Equilibria
deca-MnAl decagonal ~78 at.% Al
quasicrystal, metastable [2003Pis2]
* 1,
Mn1-xFex Al4
0.1 < x < 0.2 [1998Wei]
* 2,
(MnxFe1-x)4 Al13
oB~50
Bmmm
Fe4Al13 (h)
a = 784.3
b = 399.2
c = 2376.5
0.3825 < x < 0.425 [1998Wei]
* 3,
(Mn1-xFex)2Al10
hP26
P63/mcm
Mn3Al10
a = 755.21
b = 786.98
single phase at x = 0.3 [1998Wei]
ternary character not completely sure
* 4,
(Mn1-xFex)Al3-x Pna21
a = 1472.1 ± 0.9
b = 1233.9 ± 0.8
c = 1243.1 ± 0.8
Al72Mn23Fe5 [1998Wei]
* ,
Mn8Fe3Al9
ordered
CsCl
a = 296 to 297 ferromagnetic [1960Tsu]
solubility range from 35 to 47.5 at.% Mn,
40 to 47.5 at.% Al and 10 to 17.5 at.% Fe
*Mn6Fe9Al5 Mn
like
a = 631 space group P4332 [1987Lu]
ternary character not completely sure
*Mn258Fe111Al1295 o?1664 a = 3286
b = 3123
c = 2480
[1988Pau]
Mn14-xFexAl86 icosahedral
ai = 4530
ai = 4470
obtained in rapidly solidified alloys or by
mechanical alloying [1995Sin, 2000Sch]
in AlMn10Fe10 multiphase sample
[1993Sin]
in AlMn5Fe5 multiphase sample [1993Sin]
Reaction T [°C] Type Phase Composition (at.%)
Al Fe Mn
L+Fe4Al13+ (Mn,Fe)Al6 747 P L
Fe4Al13
(Mn,Fe)Al6
97.1
75
86
1.2
25
6
1.7
0
8
L (Al)+Fe4Al13+(Mn,Fe)Al6 652 E L
(Al)
Fe4Al13
(Mn,Fe)Al6
98.8
99.75
75
86
0.8
0
25
7
0.4
0.25
0
7
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
304
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
20
40
60
80
20 40 60 80
20
40
60
80
Mn Fe
Al Data / Grid: at.%
Axes: at.%
(γFe, γMn)
(αFe,δMn)
L
L FeAl
Fig. 2: Al-Fe-Mn.
Partial isothermal
section at 1300°C
after [1993Liu2]
Mn 10.00Fe 0.00Al 90.00
Mn 0.00Fe 10.00Al 90.00
Al Data / Grid: at.%
Axes: at.%
(Al)
(Mn,Fe)Al6
µ Fe4Al13
P
E
e
p
e
Fig. 1: Al-Fe-Mn.
Partial liquidus
surface
305
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
20
40
60
80
20 40 60 80
20
40
60
80
Mn Fe
Al Data / Grid: at.%
Axes: at.%
(γFe,γMn)
(αFe,δMn)
20
40
60
80
20 40 60 80
20
40
60
80
Mn Fe
Al Data / Grid: at.%
Axes: at.%
(γFe,γMn)
(αFe,δMn)
(βMn)
(γMn)
Fig. 3: Al-Fe-Mn.
Partial isothermal
section at 1200°C
Fig. 4: Al-Fe-Mn.
Partial isothermal
section at 1100°C
306
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Mn
20
40
60
80
20 40 60 80
20
40
60
80
Mn Fe
Al Data / Grid: at.%
Axes: at.%
(γFe,γMn)
(βMn)
ε
γ
FeAl2
FeAl
(αFe,δMn)
Fig. 5: Al-Fe-Mn.
Partial isothermal
section at 1000°C
20
40
60
80
20 40 60 80
20
40
60
80
Mn Fe
Al Data / Grid: at.%
Axes: at.%
(αFe,δMn)(βMn)
(γFe,γMn)
γ2
FeAl
Fig. 6: Al-Fe-Mn.
Partial isothermal
section at 800°C
307
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Mn
40
50
60
70
10 20 30 40
30
40
50
60
Mn 80.00Fe 0.00Al 20.00
Mn 30.00Fe 50.00Al 20.00
Mn 30.00Fe 0.00Al 70.00 Data / Grid: at.%
Axes: at.%
(βMn)
γ2
κ
10
20
30
10 20 30
70
80
90
Mn 31.40Fe 0.00Al 68.60
Mn 0.00Fe 31.40Al 68.60
Al Data / Grid: at.%
Axes: at.%
τ1
τ2τ3
τ4
λ
µ
Mn4Al11(LT)(Mn1-xFex)2Al5-y
γ2
(Mn1-xFex)Al6
(Mn1-xFex)4Al13-y
Fig. 7: Al-Fe-Mn.
Partial isothermal
section at 700°C after
[1997Mue]
Fig. 8: Al-Fe-Mn.
Partial isothermal
section for Al-rich
region at 550°C after
[1998Wei]
308
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Mn
600
700
800
900
Mn 1.00Fe 3.00Al 96.00
Mn 1.00Fe 0.00Al 99.00Al, at.%
Tem
pera
ture
, °C
L
(Al)+(Mn1-xFex)Al6
L+(Mn1-xFex)Al6
L+(Mn1-xFex)4Al13-y
(Al)+(Mn1-xFex)4Al13-y+(Mn1-xFex)Al6
97.0 98.0
600
700
800
900
Mn 0.00Fe 2.00Al 98.00
Mn 5.30Fe 2.10Al 92.60Mn, at.%
Tem
pera
ture
, °C
L
L+(Mn1-xFex)4Al13-y
+(Mn1-xFex)Al6
L+µ+(Mn1-xFex)4Al13-y
(Mn1-xFex)4Al13-y
L+(Mn1-xFex)4Al13-y+(Mn1-xFex)Al6
(Al)+(Mn1-xFex)Al6(Al)+(Mn1-xFex)4Al13-y
(Al)+
2.0 4.0
Fig. 9: Al-Fe-Mn.
Partial vertical section
at 2 mass% Mn
[1943Phi]
Fig. 10: Al-Fe-Mn.
Partial vertical section
at 4 mass% Fe
309
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–N
Aluminium – Iron – Nitrogen
Hermann A. Jehn and Pierre Perrot, up-dated by Pierre Perrot
Literature Data
Al-Fe alloys, in the presence of N, form aluminium nitride which plays an important role in steelmaking
because of grain refining and texture development. Most of the investigations have been directed at the
solubility of N in Al-Fe melts [1960Peh, 1963Mor, 1978Wad, 1979Wad, 1982Ish] and phase boundaries in
the liquid state [1963Mor, 1964Eva, 1968Isa] and in austenite [1951Dar, 1961Isa] represented by the
solubility product of AlN [1984Rag, 1987Rag]. [1961Sta] nitrided four ternary alloys at 600°C for 20 h and
analyzed the resulting phases. A review of the Al-Fe-N system has been presented by [1987Rag] and
updated by [1993Rag]. A Calphad assessment of the Al-Fe-N system has been reported by [1992Hil].
Kinetics of precipitation of AlN in steels has been investigated by [1972Oga, 1988Lan, 1995Big]. Since the
years 1980, no more experimental determinations of the solubilities of nitrogen in Al-Fe alloys are
available. The actual trend is to use the accepted results to calculate the solubility of nitrogen in more
complex alloys, then to check the calculated solubilities with experimental observations.
This evaluation incorporates and continues the critical evaluation made by [1992Jeh] considering new
published data.
Binary Systems
The binaries Al-Fe, Al-N and Fe-N are taken from [2003Pis], [2003Fer] and [2003Per], respectively.
N is practically insoluble in Al(s). The solubility of N in liquid Al under 0.1 MPa is given by [1986Wri]:
log10 (at.% N) = 2.633 - 1157/T
The only stable phase, AlN, melts at 2800 ± 50°C under nitrogen pressure of 10 to 50 MPa. AlN sublimates
congruently, the decomposition pressure being 0.1 MPa at 2435°C. Metastable AlN9 is also reported
[1986Wri].
All Fe modifications dissolve more or less N [1976Kru, 1982Fro, 1987Wri]. The ( Fe) phase is stabilized
to lower temperatures and then decomposes eutectoidally into ( Fe) and 'Fe4N at 590°C and 8.75 at.% N.
Fe4N, stable up to 670°C transforms into , hexagonal nitride with a wide homogeneity range. Fe2N
(orthorhombic) is stable up to 500°C [H, 1976Kru]. For the Fe-rich part of the Fe-N phase diagram,
including T-c isobars, see [1976Kru]. A Calphad assessment of the Fe-N diagram has been carried out by
[1987Fri] and an extensive review presented by [1987Wri]. The solubility of nitrogen in pure liquid iron
had been determined between 1580 and 2000°C under 0.1 MPa by [1960Mae, 1960Peh, 1964Eva,
1978Wad, 1982Ish] and [1986Wad].
Solid Phases
No ternary compounds are known. According to [1961Sta], considerable amount of Al is dissolved in the
' and iron nitrides (Fig. 1). The lattice parameter of nitride containing 57 at.% Fe, 19 at.% Al and 24
at.% N (79 mass% Fe, 12.7 mass% Al, 8.3 mass% N) is slightly increased compared to binary iron nitride
of the same N content (see Table 1). The N solubility in austenite containing Al was determined by direct
chemical analysis of alloys equilibrated in gaseous nitrogen [1951Dar]. At low Al content, the N solubility
is independent of the Al content and given by the relation ((%N) in mass%, T in K):
(%N)=0.0404-1.2 10-5T. At higher Al content, the precipitation of AlN is observed. The solubility product
of AlN in Fe is represented by the equations:
log10((%Al)(%N)) = 1.95 - 7400/T ((%) in mass%, T in K) [1976Kru]
log10(cAlcN) = 2.866 - 7400/T (c in at.%, T in K).
Phase boundaries calculated from the above equations are shown in Fig. 2. Few data exist on the solubility
of N in ( Fe)-Al alloys. They have been obtained when studying the precipitation kinetics of AlN in ferrite
containing 0.19 at.% Al and 0.04 at.% N [1972Oga] or 2 at.% Al and 0.02 at.% N, the maximum amount of
310
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–N
nitrogen dissolved in the ferrite matrix at 575°C [1988Lan]. An appreciable rate of precipitation was found
between 450 and 620°C; the rate was greater in cold-worked samples than in as-quenched ones.
Liquidus Surface
After early measurements by [1939Ekl], a number of investigations on the solubility of N in liquid Al-Fe
alloys were undertaken in the 1960's. [1960Mae, 1960Peh, 1964Eva] and [1982Ish] report first order
interaction coefficients to be slightly positive indicating that Al increases the activity coefficient of N in the
melt and decreases its solubility at a given N2 pressure. On the contrary, [1963Mor, 1968Isa], confirmed by
more recent work of [1978Wad], found an increase of the N solubility with the Al content of the liquid.
According to [1978Wad], the isobaric N solubility in Al-Fe melts obeys Sieverts' law (cN ~ p(N2)1/2) and
can be represented by the equation:
logcN = 0.5logp(N2)+A+BcAl+Cc2Al
Numerical data for A, B and C are given in Table 2. These results were confirmed by the model of an ideally
associated mixture proposed by [2000Yag]. The solubility product of AlN in Al-Fe melts, is given at
1580°C by [1961Isa], at 1580°C and 1675°C by [1963Mor, 1968Isa] and [1973Mok]. [1978Wad] proposed
the following equation (T in K, (%) in mass%, c in at.%):
log10((% Al)(% N)) = 6.10+5.88 10-2(%Al) - 14000/T
log10(cAl cN) = 7.016+2.84 10-2cAl - 14000/T
Figure 3 gives the liquidus isotherms under 0.1 MPa N2 and between 1550 and 1700°C according to
[1978Wad]. The solubility of N2 in liquid Al-Fe alloys calculated by [1992Hil] under 0.1 MPa pressure at
1900 K is shown in Fig. 4. A reasonable agreement is observed with experimental solubilities measured by
[1978Wad] in the iron-rich part of the diagram.
The first order interaction parameter of nitrogen for the Al-Fe liquid alloys was experimentally determined
by [1979Wad] between 1600 and 1700 K and may be represented by the following expression:
eN(Al) = d(log10 fN / d(%Al)) = - 0,81+(1426/T) with fN = (%N)pure Fe / (%N)Fe,Al alloy.
(%Al) or (%N) in the above formula represent mass%. In the liquid alloys, eN(Al) < 0, which means that the
solubility of N in liquid alloys increases with the Al content of the alloy. As shown in Fig. 3, once the
solubility product of AlN obtained, the solubility of N in liquid alloy does not increase any more, but
decreases because of the precipitation of AlN. [1982Ish] measures a positive first order interaction
parameter, which implies a decrease of the nitrogen solubility due to aluminium, result which contradicts
the well established experimental observations.
Isothermal Sections
From the phases found by [1961Sta] in four ternary alloys, a partial isothermal section at 600°C is
constructed. It is given in Fig. 1, including the composition of the four alloys and the phases observed.
[1978Tro, 1985Sch] show that the mixture AlN+Fe is thermodynamically stable at 1950°C under a N2
atmosphere, it decomposes above 1750°C under an Ar atmosphere with formation of a FeAl alloy.
Miscellaneous
[1995Big] investigated the kinetics of precipitation of AlN on internal nitriding the Fe-2 at.% Al alloy in
the temperature range 530 - 580°C. The precipitation of AlN is associated with a Gibbs energy barrier for
the formation of a precipitate of critical size and thus is controlled by nucleation and growth.
Multilayered thin films Fe-N/Al-N are currently receiving increasing attention [1991Bar, 2001Liu] due to
their excellent soft magnetic properties with large saturation magnetization of 19 kG and a high relative
permeability of 4300 at high frequency [1991Kub]. These layers are prepared by ion sputtering under a
mixture of Ar and N2 introduced under the sputtering ion source. The layers are generally oversaturated and
the thinnest (less than 12 nm) exhibits an essentially amorphous structure.
311
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–N
References
[1939Ekl] Eklund, L., “The Solubility of Nitrogen in Steel” (in Swedish), Jernkontorets Ann., 123,
545-556 (1939) (Equi. Diagram, Experimental, 13)
[1951Dar] Darken, L.S., Smith, R.P., Filer, E.W., “Solubility of Gaseous Nitrogen in Gamma Iron and
the Effect of Alloying Constituents - Aluminium Nitride Precipitation”, Trans. Metall. Soc.
AIME, 191, 1174-1179 (1951) (Equi. Diagram, Experimental, *, 12)
[1960Mae] Maekawa, S., Nagakawa, Y., “Effect of Titanium, Aluminium and Oxygen on the Solubility
of Nitrogen in Liquid Iron” (in Japanese), Tetsu to Hagane, 46, 1438-1441 (1960) (Equi.
Diagram, Thermodyn., Experimental, 8)
[1960Peh] Pehlke, R.D., Elliott, J.F., “Solubility of Nitrogen in Liquid Iron
Alloys-I-Thermodynamics”, Trans. Metall. Soc. AIME, 218, 1088-1101 (1960) (Equi.
Diagram, Experimental, Thermodyn., *, 32)
[1961Isa] Isaev, V.F., Morozov, A.N., “Conditions of Formation of AlN in Liquid Fe” (in Russian),
Sb. Nauchn.-Tehn. Trud., Nauchno-Issled. Inst. Met. Chelyab. Sovnarkhoz, (4), 12-18
(1961) (Thermodyn., Experimental, 8)
[1961Sta] Stadelmaier, H.H., Yun, T.S., “Alloys of Nitrogen and the Transition Metals Mn, Fe, Co and
Ni with Mg, Al, Zn and Cd”, Z. Metallkd., 52, 477-480 (1961) (Crys. Structure, Equi.
Diagram, Experimental, *, 22)
[1963Mor] Morozov, A.N., Isaev, V.F., Korolev, L.G., “Conditions of Nitride Formation and Solubility
of N in Alloys of Fe with Al, Ti and V” (in Russian), Izv. Akad. Nauk SSSR, Metall. i Gorn.
Delo, (4), 141-144 (1963) (Equi. Diagram, Experimental, 6)
[1964Eva] Evans, D.B., Pehlke, R.D., “The Aluminium Nitrogen Equilibrium in Liquid Iron”, Trans.
Metall. Soc. AIME, 230, 1651-1656 (1964) (Equi. Diagram, Experimental, 12)
[1968Isa] Isaev, V.F., Danilovich, Yu.A., Morozov, A.N., “Solubility of Nitrogen for the Formation
of Nitrides in Molten Alloys Based on Iron and Nickel” (in Russian), Fiz-Khim. Osn. Pro.
Stali. Publ. Nauka, Samarin, A.M. (Ed.), Nauka, Moscow, 296-301 (1968) (Equi. Diagram,
Thermodyn., Experimental, 11)
[1972Oga] Ogawa, R., Fukutsuwa, T., Yagi, Y., “Precipitation of AlN in Cold Worked High Purity
Fe-Al-N Alloys” (in Japanese), Tetsu to Hagane, 58, 872-884 (1972) (Equi. Diagram,
Experimental, 21)
[1973Mok] Mokrov, I.A., Aleshchenko, G.M., Stomakhin, A.Ya., “Thermodynamic Evaluation of
Oxides and Nitrides in Metallic Melts”, (in Russian), Izv. Vyss. Uchebn. Zaved., Chern.
Metall., (7), 63-67 (1973) (Equi. Diagram, Thermodyn., 9)
[1976Kru] Krueger, J., Kunze, H.D., Schuermann, E., “Eisen” (in German), in “Gases and Carbon in
Metals”, Fromm, E., Gebhardt, E, (Eds.), Springer, Berlin, 578-613 (1976) (Equi. Diagram,
Review, *, 241)
[1978Tro] Trontelj, M., Kolar, D., “Reactions of AlN with the Iron Group Elements”, Vestn. Sloven.
Kem. Drus., 25(2), 165-172 (1978) (Thermodyn., Eperimental, 8)
[1978Wad] Wada, H., Pehlke, R.D., “Nitrogen Solubility and Aluminium Nitride Precipitation in
Liquid Fe, Fe-Cr, Fe-Cr-Ni, and Fe-Cr-Ni-Mo Alloys”, Metall. Trans. B, 9B, 441-448
(1978) (Equi. Diagram, Thermodyn., Experimental, *, 12)
[1979Wad] Wada, H., Pehlke, R.D., “Nitrogen Solubility and Aluminium Nitride Precipitation in
Liquid Iron Alloys containing Nickel and Aluminum”, Metall. Trans. B, 10B, 409-412
(1979) (Equi. Diagram, Thermodyn., Experimental, *, 4)
[1982Fro] Fromm, E., Jehn, H., Hehn, W., Speck, H., Hörz, G., “Gases and Carbon in Metals, Pt XV,
Ferrous Metals (3), Iron - Nitrogen”, Phys. Data, Fachinformationszentrum Energie,
Physik, Mathematik, Karlsruhe, 85, 5-17 (1982) (Equi. Diagram, Review, 40)
[1982Ish] Ishii, F., Ban’ya, B., Fuwa, T., “Effect of C, Al, Si, P, Mn and Ni on the Solubility of
Nitrogen in Liquid Iron Alloys” (in Japanese), Tetsu to Hagane, 68, 1551-1559 (1982)
(Equi. Diagram, Experimental, Thermodyn., 43)
312
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–N
[1984Rag] Raghavan, V., “The Al-Fe-N System”, Trans. Indian Inst. Met., 37, 411-415 (1984) (Equi.
Diagram, Review, 16)
[1985Sch] Schuster, J.C., Bauer, J., Nowotny, “Applications to Materials Science of Phase Diagrams
and Crystal Structures in the Ternary Systems Transition Metal-Aluminum-Nitrogen”, Rev.
Chim. Miner., 22(4), 546-554 (1985) (Equi. Diagram, Review, #, 20)
[1986Wad] Wada, H., Lee, S.W., Pehlke, R.D. “Nitrogen Solubility in Liquid Fe and Mn-Fe Alloys”,
Metall. Trans. B, 17B, 238-239 (1986) (Experimental, 17)
[1986Wri] Wriedt, H.A., “The Al-N (Aluminium-Nitrogen) System”, Bull. Alloy Phase Diagrams, 7,
329-333 (1986) (Equi. Diagram, Review, #, 54)
[1987Fri] Frisk, K., “A New Assessment of the Fe-N Phase Diagram”, Calphad, 11, 127-134 (1987)
(Equi. Diagram, Thermodyn., Theory, 34)
[1987Rag] Raghavan, V., “The Al-Fe-N System”, in “Phase Diagrams of Ternary Iron Alloys, Part I”,
ASM International, 1, 145-147 (1987) (Equi. Diagram, Review, 13)
[1987Wri] Wriedt, H.A., Gokcen, N.A., Nafziger, R.H., “The Fe-N (Iron-Nitrogen) System”, Bull.
Alloy Phase Diagrams, 8(4), 355-377 (1987) (Equi. Diagram, Thermodyn., Review, #, 126)
[1988Lan] Lankreijer, L.M., Somers, M.A.J., Mittemeijer, E.T., “Kinetics and Nitride Precipitation in
Fe-Al and Fe-Si Alloys on Nitriding”, Proc. Internat. Conf. High Nitrogen Steels, Lille,
Edited 1989 by the Institute of Metals, London, 108-111 (1988) (Equi. Diagram,
Experimental, 17)
[1991Bar] Barnard, J.A., Tan, M., Waknis, A., Haftek, E., “Magnetic Properties and Structure of Al/
Fe-N Periodic Multilayer Thin Films”, J. Appl. Phys., 69(8), 5298-5300 (1991) (Crys.
Structure, Magn. Prop., 8)
[1991Kub] Kubota, K., Naoe, M., “Magnetic Properties of Fe-N/Al-N Multilayerd Films Pprepared by
Ar Ion-Assist Sputtering”, J. Appl. Phys., 70(10), 6430-6432 (1991) (Crys. Structure, Magn.
Prop., 2)
[1992Jeh] Jehn, H.A., Perrot, P., “Aluminium - Iron - Nitrogen”, MSIT Ternary Evaluation Program,
in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; Document ID: 10.14876.1.20, (1992) (Crys. Structure, Equi. Diagram,
Assessment, 23)
[1992Hil] Hillert, M., Jonsson, S., “An Assessment of the Al-Fe-N System”, Metall. Trans. A, 23A
(11), 3141-3149 (1992) (Equi. Diagram, Thermodyn., Assessment, #, 27)
[1993Rag] Raghavan V., “Al-Fe-N (Aluminum-Iron-Nitrogen)”, J. Phase Equilib., 14 (5), 617-618
(1993) (Equi. Diagram, Review, 7)
[1995Big] Biglari, M.H., Brakman, C.M., Mittemeijer, E.J., Zwaag, S.V.D., “The Kinetics of the
Internal Nitriding of Fe-2 at.Pct. Al Alloy”, Metall. Mater. Trans. A, 26A, 765-776 (1995)
(Calculation, Experimental, Kinetics, Thermodyn., 41)
[2000Yag] Yaghmaee, M.S., Kaptay, G., Janosfy, G., “Equilibria in the Ternary Fe-Al-N System”,
Mater. Sci. Forum, 329-330, 519-524 (2000) (Equi. Diagram, Theory, 9)
[2001Liu] Liu, Y.-K., Harris, V.G., Kryder, M.H., “Evolutions of Magnetic and Structural Properties
of FeAlN Thin Films via N Doping”, IEEE Trans. Magn., 37(4), 1779-1782 (2001)
(Experimental, Magn. Prop., 8)
[2003Fer] Ferro, R., Bochvar, N., Sheftel, E., Ding, J.J., “Al-N (Aluminum-Nitrogen)”, MSIT
Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science
International Services GmbH, Stuttgart; to be published, (2003) (Equi. Diagram, Crys.
Structure, Assessment, 33)
[2003Per] Perrot, P., “Fe-N (Iron-Nitrogen)”, MSIT Binary Evaluation Program, in MSIT Workplace,
Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH, Stuttgart; to be
published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 35)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 58)
313
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–N
Table 1: Crystallographic Data of Solid Phases
Table 2: Isobaric Nitrogen Solubility in Al-Fe Melts [1978Wad] log10cN=0.5log10pN2+A+BcAl+Cc2Al (cN,
cAl in at.%, PN2 in Pa)
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
( Fe)
912-1394
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2]
dissolves 0.1 at.% N at 912°C, 0.1 MPa
( Fe)
912
1394-1538
cI2
Im3m
W
a = 286.65 at 25°C [Mas2]
dissolves up to 54.0 at. % Al at 1102°C
dissolves 0.0166 at.% N at 912°C,
0.1 MPa
(Al)
660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C, [Mas2]
', Fe4N
680
cP5
Pm3m
Fe4N
a = 378.7 [1987Rag]
19.3 to 20.0 at.% N
, Fe3N1±x
(Fe,Al)3N1±x
hP3
P63/mmc
Fe3N1±x
a = 272.9
c = 439.2
a = 272.9
c = 440.4
a = 276
c = 442
~ 15 to ~ 33 at.%
23 at.% N
30 at.% N
Fe57Al19N24 [1961Sta]
Fe2N
500
oP12
Pbcn
Fe2N
a = 551.2
b = 482.0
c = 441.6
33.7 at.% N, [1984Rag]
AlN
< 2437.4
hP4
P63mc
ZnS- wurtzite
a = 311.14
c = 497.92
at 25°C, [1986Wri]
T [°C] A B C
1550
1600
1650
1700
- 3.859
- 3.856
- 3.852
- 3.849
+ 1.25 10-2
+ 2.34 10-2
+ 3.37 10-2
+ 4.34 10-2
+ 9.8 10-3
+ 8.2 10-3
+ 6.9 10-3
+ 5.7 10-3
314
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–N
20
40
60
80
20 40 60 80
20
40
60
80
Fe Al
N Data / Grid: at.%
Axes: at.%
AlN
(γFe)
γ'+AlNε
γ',Fe4Nγ'+ε
γ'
pure ε
(γFe)+γ'
c
γ'+AlN
ε+AlN
ε+γ'+AlN
0.125
0.100
0.075
0.050
0.025
0
0 0.1 0.2 0.3 0.4
Al, at.%
( Fe)� + N2
+ AlN( Fe)�
1350°C
1200°C
1050°C
( Fe)� + AlN( Fe)�
+ AlN( Fe)�
N,at.%
+N +AlN2( Fe)�
Fig. 1: Al-Fe-N.
Partial isothermal
section at 600°C,
after [1961Sta]
Fig. 2: Al-Fe-N.
Solubility limits in the
( Fe) phase
after [1951Dar]
315
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–N
0.3
0.2
0.1
00 2 4 6
Al, at.%
N,at.%
L
L +AlN
L +AlN
L +AlNL + N2
1550°C
1600°C
1650°C
1700°C
0.02
0.08
0.06
0.04
604020 80
0
100Fe Al
T = 1627°C
P(N ) = 1 bar2
Al, mass%
N,mass%
0
Fig. 3: Al-Fe-N.
Solubility limits in the
liquid phase after
[1978Wad]
Fig. 4: Al-Fe-N.
Solubility of N2 in
Al-Fe liquid alloys at
1627°C under 1 bar
N2
316
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
Aluminium – Iron – Neodymium
Riccardo Ferro, Paola Riani, Laura Arrighi
Literature Data
First investigations in this system were undertaken by [1970Viv] who determined phase relations at 500°C
in the range up to 33.3 at.% Nd and structures of binary and ternary phases by X-ray analysis. Structures,
homogeneity ranges and magnetic properties of the phases were determined in more detail by [1971Oes1,
1971Oes2, 1975Dwi] for Nd(Fe1-xAlx)2, by [1988Hu, 1989Wei] for Nd2(Fe1-xAlx)17 and by [1974Viv,
1976Bus] for NdFe4Al8. [1990Gri, 1991Gri1] studied the Al-poor region (< 30 at.% Al) of the system by
DTA, X-ray, EDAX and optical microscopy; moreover [1992Gri] performed a complete assessment of the
system. On the basis of experimental data and thermodynamic consideration several isopleth sections were
constructed and presented together with isothermal sections and a liquidus projection.
Binary Systems
The accepted Al-Fe phase diagram [2003Pis] is mainly based on the assessment by [1993Kat], except for
the Fe-rich region where the ordering equilibria between the ( Fe), FeAl and Fe3Al solid solutions have
been recently investigated by [2001Ike].
The accepted Al-Nd binary system is from [2003Leb]. The accepted Fe-Nd phase diagram, reported by
[2000Oka] is based on [1990Lan, 1991Lan], who found and studied the Nd5Fe17 phase. This is formed only
after very long heat treatments; so that it is easy to have metastable phase equilibria without the formation
of this phase.
Solid Phases
Table 1 summarizes the crystal structure data relevant to all the solid phases.
A number of linear solid solution fields (generally parallel to the Al-Fe axis) have been described. Those
based on binary phases are the following: for the NdAl2-based (cF24-MgCu2 type) a solubility up to 20 at.%
Fe [1991Gri2], for the Nd2Fe17-based (hR57-Th2Zn17 type) a solubility up to more then about 50 at.% Al
[1970Viv, 1989Wei, 1991Gri2] have been determined. A transition, at a temperature above ~800°C, to a
high temperature Nd2Fe17 form (with an unknown structure), was suggested by [1991Gri2] on the basis of
DTA results. Towards the Fe-Nd binary system the transition temperature increases above the temperature
of peritectic formation of the binary Nd2Fe17 phase. A neutron diffraction refinement of the crystal structure
of Nd2Fe17-xAlx was performed by [1996Gir, 1997Gir]. The site occupation of a number of isostructural
compounds was discussed and also related to the mixing enthalpy [1998Gir].
All the other binary phases show negligible ternary solid solutions.
Ternary phases observed by [1970Viv] are 1 NdFe4-xAl8+x (ThMn12 structure type), 2 NdFe2Al10 and 3
NdFe2-xAlx (0.35 < x < 0.8). [1974Viv, 1976Bus] refined the crystal structure of 1 to be of the CeMn4Al8type, an ordered variant of the ThMn12 type. The two papers give slightly different lattice parameters
(a = 878.2, c = 505.1 pm [1974Viv]; a = 881.3, c = 505.8 pm [1976Bus]). The structure of the 2 NdFe2Al10
was determined to be of the YbFe2Al10 type [1998Thi], an orthorhombic stacking variant of the ThMn12
type. The composition of 3 was corrected by [1991Gri1] to be Nd30Fe62-xAl8+x (0 < x < 17) with a
tetragonal structure. [1992Hu] determined the crystal structure to be of the La6Co11Ga3 type established by
[1985Sic]. Similarly as in La6Co11Ga3 the mutual substitution is almost restricted to the 16(l2) position.
Structure and nature of mutual substitution were confirmed by [1995Bre, 1997Kun, 2000Nag]. Crystal
structure data and experimental homogeneity range of 3 are well represented by the formula
Nd6Fe9Al1(Fe1-xAlx)4 (0.15 < x < 1).
Another ternary phase, 4, with a Nd:(Fe+Al) ratio of 1:2 was detected by [1991Gri1] with a small
homogeneity range for Al (2.5 to 5 at.%); its structure is unknown. [1995Bre] studied the Al-Fe substitution
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in the 3 and 4 phases by Mössbauer spectroscopy. They characterized the still unknown structure of 4 as
“long-period stacking of planes, typical for polytypism”.
Invariant Equilibria and Liquidus Surface
A partial not completely confirmed Scheil reaction scheme, was suggested together with a few vertical
sections and a liquidus projections by [1991Gri1, 1991Gri2]. The phase transitions during solidification of
the ternary alloys were deduced from the microstructures of arc melted alloys (cooling rate 200 to 400
Ksec-1) and DTA specimens (10 Kmin-1); the transition temperatures obtained by DTA were combined
with optical microscopic analysis to deduce the reaction sequence. The transition between the
high-temperature and room-temperature modifications of the Nd2(Fe,Al)17 compound could be given only
tentatively. The transition temperature is around 800°C at Al contents above 20 at.%. With Al content
decreasing to zero it increases above the temperature of peritectic formation of Al-free Nd2Fe17(r) phase.
The corresponding invariant equilibria could not be identified or located. Therefore in the reaction scheme
reproduced here in Fig. 1 these two modifications are not distinguished and treated as a single phase.
Furthermore missing links of the reaction scheme were tentatively completed by equilibria drawn by dashed
lines.
[1991Gri1, 1991Gri2] assumed for U2 an equilibrium L+? NdAl2+Nd2Fe17 with “?” standing for a not
determined phase. The only phase known to be stable at this high temperature and Al contents below 50
at.%, however, is ( Fe). The two-phase field ( Fe)+( Fe) forms a closed loop in the binary Al-Fe system.
As both modifications of Fe do not dissolve significant amounts of Nd (in the binary Fe-Nd system), this
closed loop forms one edge of a series of three-phase equilibria in the ternary system near the Fe corner.
Together with the binary equilibrium p1 there necessarily follows the equilibrium U1. The equilibrium
L+( Fe)+NdAl2 goes towards the Al corner, very probably over a maximum due to the high melting
temperatures of NdAl2 and ( Fe).
The equilibria U4 and U9 follow from the accepted binary systems. U4 corresponds to the most likely form,
how the phase Nd5Fe17 may participate in the reaction scheme. U9 follows from the three-phase equilibria
containing both modifications of Nd, ( Nd) and ( Nd).
[1991Gri1, 1991Gri2] postulated a maximum of the three-phase equilibrium L+( Nd)+Nd2Fe17 between
the binary Al-Fe system and U6. Nd2Fe17 here has to be replaced by Nd5Fe17. As the arguments for this
maximum are not exclusive, it is not taken into account in Fig. 1.
A partial liquidus surface presented by [1991Gri1, 1991Gri2] was classified as tentative by the authors,
especially the equilibria connected with the allotropic transformation between the two modifications of
Nd2Fe17. The most recent binary Al-Nd phase diagram at the Nd side is very different from that used by
[1991Gri1, 1991Gri2]. A trial to adjust the liquidus surface to the accepted binary Al-Nd phase diagram
seems to need too many speculative estimates regarding the compositions of liquid at the nonvariant
equilibria. Therefore this partial liquidus diagram is not presented here.
Isothermal Sections
Partial isothermal sections at 500 and at 600°C are presented in Figs. 2 and 3, respectively. Fig. 2 is taken
from [1970Viv] with compositions re-determined by [1991Gri1, 1991Gri2]. The homogeneity ranges of the
Al-Fe phases are adjusted to the accepted binary Al-Fe system. Fig. 3 is re-drawn from [1992Gri], it
represents the metastable system with suppressed Nd5Fe17 phase, as it is usually found after normal heat
treatment. Two more isothermal sections, at 750 and 900°C, were given by [1991Gri1, 1991Gri2].
Temperature – Composition Sections
[1991Gri1] gave 11 temperature-concentration sections, at constant Nd contents of 20, 30, 40, 50, 60, 70
and 80 at.% and constant Al contents of 5, 10, 20 and 30 at.%. Five of these sections were reproduced by
[1991Gri2]. In Fig. 4 the section at 70 at.% Nd is shown. At both sides this figure is adjusted to the accepted
binary systems, shown by dashed lines.
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Notes on Materials Properties and Applications
Magnetic properties of ternary phases, microstructures of phases and sketched diagrams of the system are
published in [1990Gri, 1990Hen, 1990Kno, 1991Gri2].
Magnetic and/or transport properties and Mössbauer spectra of the Nd6Fe13-xAl1+x phase have been
investigated by several authors: for x = 1 [1997Kun], for x = 2 [1992Hu], [1996Zha], [1998Gro] and
[2000Wan], for x = 2.2, 3.5 [2000Nag] and for x = 3 [2002Jon].
The magnetic properties of NdFe4Al8 compound have been studied by specific heat measurements by
[1998Hag] and [2000Hag] while atomistic simulation of the lattice constants and lattice vibrations in
NdFe4Al8 have been performed by [2003Kan].
Spin rearrangement and ferromagnetic field magnetization for Nd2(Fe1-xAlx)17 (x = 0.04) have been
determined by [1995Koi], while high field magnetization and spin reorientation have been studied by
[1996Kat]; moreover anomalous thermal expansion have been measured by room temperature to 400°C by
[1995Zha].
Due to their large glass-forming ability amorphous Al-Fe-Nd alloys have been studied in the last few years.
Inoue et al. studied the thermal stability and the hard magnetic properties of Nd(70,65,60)Fe(20,25,30)Al10
[1997Ino, 1996Ino], while [2001Car] investigated microstructure, thermal stability microhardness as a
function of powder particle size in Nd5Fe5Al90 alloy obtained by gas atomization. [1997Mat] determined
by X-ray diffraction the local atomic structure of Nd(65,30,20,10)Fe(25,40,70,5)Al(10,30,10,85). Several other
authors described the magnetic properties of these phases [1999Din], [1999Phu], [1999Si], [1999Wan],
[2001Chi], [2001Dan], [2001Si], [2001Wan1, 2001Wan2], [2002Bil], [2002Hon], [2002Kon], [2002Lai],
[2002Sat], [2003Bra] and [2003Kum].
References
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-Rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids, 6, 16-37 (1958) (Crys. Structure,
Experimental, 49)
[1961Lih] Lihl, F., Ebel, H., “X-ray Examination of the Constitution of Iron-Rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenw., 32, 483-487 (1961) (Crys.
Structure, Experimental, 12)
[1970Viv] Vivchar, O.I., Zarechnyuk, O.S., Ryabov, V.R., “Phase Composition of Neodymium
Iron-Aluminum Alloys in the 0-33.3 at.% Neodymium Range”, Russ. Metall., (1), 140-143
(1970), translated from Izv. Akad. Nauk SSSR, Met., (1), 211-213 (1970) (Experimental,
Crys. Structure, Equi. Diagram, #, 12)
[1971Oes1] Oesterreicher, H., “Structural Studies of Rare-Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Experimental, Crys. Structure, 6)
[1971Oes2] Oesterreicher, H., “Structural and Magnetic Studies on ErFe2-ErAl2”, J. Appl. Phys., 42,
5137-5143 (1971) (Experimental, Crys. Structure, 31)
[1974Viv] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12- Type Structure in R-Fe-Al
Systems” (in Russian), Tezisy Dokl.-Vses. Konf. Kristallokhim. Intermet. Soedin., Rykhal,
R.M. (Ed.),Vol. 2, Gos. Univ., Lvov, 41 (1974) (Experimental, Crys. Structure, 0)
[1975Dwi] Dwight, A.E., Kimball, C.W., Preston, R.S., Taneja S.P., Weber, L., “Crystallographic and
Mössbauer Study of (Sc,Y,Ln)(Fe,Al)2 Intermetallic Compounds”, J. Less-Common Met.,
40, 285-291(1975) (Experimental, Crys. Structure, 8)
[1976Bus] Buschow, K.H.J., van der Vucht, J.H.N., van den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth-3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Experimental, Crys. Structure, 2)
[1985Sic] Sichevich, O.M., Lapunova, R.V., Sobolev, A.N., Grin, Yu.N., Yarmolyuk, Ya.P., “Crystal
Structures of the Compounds La6Ga3Co11 and R6Ga3Fe11 (R = Pr, Nd, Sm)”, Sov.
Phys.-Crystallogr. (Engl. Transl.), 30, 627-629 (1985) (Experimental, Crys. Structure, 7)
319
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
[1986Gri] Griger, A., Syefaniay, V., Turmezey, T., “Crystallographic Data and Chemical
Compositions of Aluminum-Rich Al-Fe Intermetallic Phases”, Z. Metallkd., 77, 30-35
(1986) (Equi. Diagram, Crys. Structure, Experimental, 23)
[1988Hu] Hu, B.P., Coey, J.M.D., “Effect of Hydrogen on the Curie Temperature of Neodymium Iron
Ternary Alloys Nd2(Fe15M2), M = Al, Si, Co”, J. Less-Common Met., 142, 295-300 (1988)
(Experimental, Crys. Structure, 15)
[1989Wei] Weitzer, F., Hiebl, K., Rogl, P., “Al, Ga Substitution in RE2Fe17 (RE = Ce, Pr, Nd):
Magnetic Behavior of RE2Fe15(Al,Ga)2 Alloys”, J. Appl. Phys., 65, 4963-4967 (1989)
(Experimental, Crys. Structure, 22)
[1990All] Allemand, J., Letant, A., Moreau, J.M., Nozières, J.P., Perrier de la Bâthie, J., J.
Less-Common Met., 166, 73 (1990)
[1990Gri] Grieb, B., Henig, E.-Th., Martinek, G., Petzow, G., Stadelmaier, H.H., “Phase Relations and
Magnetic Properties of New Phases in the Fe-Nd-Al and Fe-Nd-C Systems”, IEEE Trans.
Magn., 26, 1367-1369 (1990) (Experimental, Equi. Diagram, Crys. Structure, #, 8)
[1990Hen] Henig, E.T., Grieb, B., “Phase Diagrams for Permanent Magnet Materials”, “Supermagnets,
Hard Magnetic Materials”, Proc. NATO Advanc. Study Ins., Ser. C, IL Ciocco, Italy, 331,
171-226 (1990) (Review, Equi. Diagram, #, 27)
[1990Kno] Knoch, K.G., “Nd-Fe-B Permanent Magnets, Correlation of Coercivity and Microstructure
of Al and Ga Dotation” (in German), Dessertation, Stuttgart, (1990) (Experimental,
Review, Crys. Structure, 115)
[1990Kon] Kononenko, V.I.; Golubev, S.V., “Phase Diagrams of Binary Systems of Aluminum with
La, Ce, Pr, Nd, Sm, Eu, Yb, Sc, and Y”, Russ. Metall., 2, 193-195 (1990), translated from
Izv. Akad. Nauk SSSR, Met., 2, 197-199 (1990) (Equi. Diagram, 8)
[1990Lan] Landgraf, F.J.G., Schneider, G., Villas-Boas, V., Missell, F.P., “Solidification and Solid
State Transformations in Fe-Nd: A Revised Phase Diagram”, J. Less-Common Met., 163,
209-218 (1990) (Experimental, Crys. Structure, Equi. Diagram, #, 28)
[1991Gri1] Grieb, B., “Constitution of the Systems and Microstructures of the Alloys of Optimized
Fe-Nd-B Hardmagnetic Materials with the Substituents Dy, Al, Ga or C” (in German),
Dissertation, Stuttgart, (1991) (Experimental, Equi. Diagram, Review, Crys. Structure, #, *,
127)
[1991Gri2] Grieb, B., Henig, E.-Th., “The Ternary Al-Fe-Nd System”, Z. Metallkd., 81, 560-567 (1991)
(Experimental, Crys. Structure, #, *, 17)
[1991Lan] Landgraf, F.J.G., Schneider, G., Villas-Boas, V., Missel, F.P., “Solidification and Solid
Phase Transformations in FE-Nd: A Revised Phase Diagram”, J. Less-Common Met., 163,
209-218 (1990) (Experimental, Crys. Structure, Equi. Diagram, #, 28)
[1992Gri] Grieb, B., “Aluminium-Iron-Neodymium”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.19198.1.20, (1992) (Crys. Structure, Equi. Diagram,
Assessment, 20)
[1992Hu] Hu, B.P., Coey, J.M.D., Klesnar, H., Rogl, P., “Crystal Structure, Magnetism and 57Fe
Moesbauer Spectra of Ternary RE6Fe11Al3 and RE6Fe13Ge Compounds”, J. Magn. Magn.
Mater., 117, 25-231 (1992) (Crys. Structure, Experimental, Magn. Prop., Moessbauer, 14)
[1993Bor] Borzone, G., Cardinale, A.M., Cacciamani G., Ferro R., “On the Thermochemistry of the
Nd-Al Alloys”, Z. Metallkd., 84(9), 635-40 (1993) (Thermodyn., Experimetal, 75)
[1993Kat] Kattner, U.R., Burton, B.P., “Al-Fe (Aluminum-Iron)”, in “Phase Diagrams of Binary Iron
Alloys”, Okamoto, H. (Ed.), ASM Intl., Materials Park, OH, 12-28 (1993) (Review, 99)
[1994Bur] Burkhardt, U., Grin, J., Ellner, M., Peters, K., “Structure Refinement of the Iron-Aluminium
Phase with the Approximate Composition Fe2Al5”, Acta Crystallogr., Sect. B: Struct.
Crystallogr. Crys. Chem., B50, 313-316 (1994) (Crys. Structure, Experimental, 9)
[1994Gri] Grin, J., Burkhardt, U., Ellner, M., Peters, K., “Refinement of the Fe4Al13 Structure and its
Relationship to Quasihomological Homotypical Structures”, Z. Kristallogr., 209, 479-487
(1994) (Crys. Structure, Experimental, 39)
320
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[1995Koi] Koide, T., Motokawa, M., Kato, H. “Spin Rearrangement and Ferromagnetic Field
Magnetization Procedure of R2(Fe1-xAlx)17 Single Crystal” (in Japanese), Tohoku Daigaku
Kinzoku Zairyo Kenkyusho Kyojiba Chodendo Zairyo Kenkyu Senta Nenji Hokoku, 191-194
(1995) (Experimental, Magn. Prop.)
[1995Bre] Le Breton, J.M., Teillet, J., Lemarchand, D., de Pauw, V., “Investigation of the Delta and
My Phases in the Nd-Fe-Al System”, J. Alloys Compd., 218, 31-35 (1995) (Crys. Structure,
Experimental, 12)
[1995Zha] Zhang, X.D., Shumsky, M.G., James, W.J., “Anomalous Thermal Expansion in Substituted
Nd2Fe17-xSix and Nd2Fe17-xAlx Compounds”, IEEE Trans., Magn., 31(6), 3662-3664
(1995) (Crys. Structure, Experimental, 10)
[1996Gir] Girt, Er., Altounian, Z., Ming, M., Swainson, I.P., Donaberger, R.L., “Neutron Diffraction
Study of Fe Substitutions in Nd2Fe17X (X = Al, Si, Ga, Mo, W)”, J. Magn. Magn. Mater.,
163, L251-L-256 (1996) (Crys. Structure, Experimental, Magn. Prop., 15)
[1996Ino] Inoue, A., Zhang, T., Takeuchi, A., Zhang, W., “Hard Magnetic Bulk Amorphous Nd-Fe-Al
Alloys of 12 mm in Diameter Made by Suction Casting”, Mater. Trans., JIM, 37(4),
636-640 (1996) (Experimental, Magn. Prop.)
[1996Kat] Kato, H., Knide, T., Yamada, M., Motokawa, M., Miyazaki, T., “High Field Magnetization
and Spin Reorientation in Sm2(Fe1-xAlx)17 and Nd2(Fe1-xAlx)17 Single Crystals”, Sci. Rep.
Res. Inst. Tohoku Univ., A42(2), 283-288 (1996) (Experimental, Magn. Prop.)
[1996Sac] Saccone, A., Cardinale, A.M., Delfino, S., Ferro, R., “Phase Equilibria in the Rare Earth
Metals (R)-Rich Regions of the R-Al Systems (R = La, Ce, Pr, Nd),” Z. Metallkd., 87(2),
82-87 (1996) (Crys. Structure, Equi. Diagram, Experimental, 18)
[1996Zha] Zhao, Z.G., de Boer, F.R., Buschow, K.H.J., “Magnetic Properties of R6Fe11Al3 and
R6Fe12Al2 Compounds with R = Pr, Nd”, J. Alloys Compd., 239(2), 147-149 (1996)
(Experimental, Magn. Prop., 12)
[1997Gir] Girt, Er., Altounian, Z., Swainson, I.P., “The influence of the enthalpy of mixing on the
Fe-substitution in Nd2Fe16.5X0.5 (X = Al, Ti, Nb, W)”, Physica B (Amsterdam),
B234-B236, 637-639 (1997) (Crys. Structure, Experimental, 4)
[1997Ino] Inoue, A., Zhang, T., “Thermal Stability and Glass-Forming Ability of Amorphous
Nd-Al-TM (TM = Fe, Co, Ni or Cu) Alloys”, Mater. Sci. Eng. A, A226-A228, 393-396
(1997) (Experimental, 12)
[1997Kog] Kogachi, M., Haraguchi, T., “Quenched-in Vacansies in B2-Structured Intermetallic
Compound FeAl”, Mater. Sci. Eng. A, A230, 124-131 (1997) (Crys. Structure,
Experimental, 23)
[1997Kun] Kuncser, V., Rosenberg, M., Buschow, K.H.J., Filoti, G., “Site Occupation and 57Fe
Mössbauer Spectra of RE6Fe14-xMx with RE = Nd, Pr and M = Ga, Al”, J. Alloys Compd.,
255, 60-66 (1997) (Experimental, Magn. Prop., Moessbauer, 14)
[1997Mat] Matsubara, E., Zhang, T., Inoue, A., “Distinctive Structural Features of Nd-Fe-Al
Amorphous Alloy System”, Sci. Rep. Res. Inst. Tohoku Univ., Ser. A Phys. Chem. Metall.,
43(2), 83-87 (1997) (Experimental)
[1998Ali] Aliravci, C.A., Pekgueleryuez, M.O., “Calculation of Phase Diagrams for the Metastable
Al-Fe Phases Forming in Direct-chill (DC)-Cast Aluminium Alloy Ingots”, Calphad, 22,
147-155 (1998) (Calculation, Equi. Diagram, 20)
[1998Gir] Girt, E., Altounian, Z., “Origin of Fe Substitution in Nd2Fe17X”, Phys. Rev. B: Condens.
Matter, B57(10), 5711-5714 (1998) (Calculation, Crys. Structure, Experimental,
Thermodyn., 20)
[1998Gro] Groot de, C.H., Buschow, K.H.J., Boer de, R.F., “Magnetic Properties of R6Fe13-xM1+x
Compounds and Their Hydrides”, Phys. Rev. B: Condens. Matter, B57(18), 11472-11482
(1998) (Crys. Structure, Experimental, Magn. Prop., 34)
[1998Hag] Hagmusa, I.H., Brueck, E., de Boer, F.R., Buschow, K.H.J., “Magnetic Properties of
RFe4Al8 Compounds Studied by Specific Heat Measurements”, J. Alloys Compd., 278,
80-82 (1998) (Experimental, Magn. Prop., 9)
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[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10 (Ln = Y, La-Nd,
Sm, Cd-Lu and T = Fe, Ru, Os) with YbFe2Al10 Type Structure and Magnetic Properties of
the Iron-Containing Series”, J. Mater. Chem., 8(1), 125-130 (1998) (Crys. Structure,
Experimental, Magn. Prop., 31)
[1999Din] Ding, J., Si, L., Wang, X.Z., “Magnetoresistivity and Metamagnetism of the Nd33Fe50Al17
Alloy”, Appl. Phys. Lett., 75(12), 1763-1765 (1999) (Crys. Structure, Experimental, Magn.
Prop., 12)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-Rich Fe-Al
Alloys”, Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 15)
[1999Phu] Phuc, N.X., Dan, N.H., Ding, J., Li, Y., Wang, X.Z., “Observation of Continuos and
Step-Like Thermomagnetization in Nd-Fe-Al Amorphous Alloys”, IEEE Trans. Magn.,
35(5), 3460-3462 (1999) (Experimental, Magn. Prop., 12)
[1999Si] Si, L., Ding, J., Li, Y., Wang, L., Wang, X.Z., “A Structural, Magnetic and Mössbauer
Investigation on Melt-Spun Nd0.33(Fe0.75Al0.25)0.67 Ribbons”, J. Phys.: Condens. Matter,
11, 10557-10566 (1999) (Crys. Structure, Experimental, Magn. Prop., Moessbauer, 17)
[1999Wan] Wang, X.Z., Li, Y., Ding, J., Si, L., Kong, H.Z., “Structure and Magnetic Characterization
of Amorphous and Crystalline Nd-Fe-Al Alloys”, J. Appl. Phys., 290, 209-215 (1999)
(Crys. Structure, Experimental, Magn. Prop., 12)
[2000Hag] Hagmusa, I.H., Brueck, E., de Boer, F.R., Buschow, K.H.J., “A Specific-Heat Study of
some RFe4Al8 Compounds (R = Ce, Pr, Nd, Dy, Ho, Tm)”, J. Alloys Compd., 298, 77-81
(2000) (Crys. Structure, Experimental, Magn. Prop.,16)
[2000Nag] Nagata, Y., Kamonji, M., Kurihara, M., Yashiro, S., Samata, H., Abe, S., “Magnetism and
Transport Properties of Nd6Fe13-xAl1+x Crystals”, J. Alloys Compd., 296, 209-218 (2000)
(Crys. Structure, Electr. Prop., Experimental, Magn. Prop., 16)
[2000Oka] Okamoto, H., “Desk Handbook Phase Diagrams for Binary Alloys”, ASM International,
Materials Park, OH 44073-0002 (2000)
[2000Wan] Wang, F., Zhang, P., Shen, B., Yan, Q., “Transport Properties of R6Fe11Al3 Compounds (R
= La, Nd)”, J. Appl. Phys., 87(9), 6043-6045 (2000) (Experimental, Magn. Prop., 10)
[2001Car] Cardoso, K.R., Escorial, A.G., Lieblich, M., Botta, W.J.F., “Amorphous and
Nanostructured Al-Fe-Nd Powders Obtained by Gas Atomization”, Mater. Sci. Eng. A,
A315, 89-97 (2001) (Crys. Structure, Experimental, 20)
[2001Chi] Chiriac, H., Lupu, N., “The Magnetic and Structural Properties of the High-Coercivity
Nd50Fe40Al10 Amorphous Alloys”, J. Non-Cryst. Solids, 287, 135-139 (2001)
(Experimental, Magn. Prop., 13)
[2001Dan] Dan, N.H., Phuc, N.X., Hong, N.M., Ding, J., Givord, D., “Multi-Magnetic Phase
Behaviour of the Nd60Fe30Al10 Amorphous Hard Magnetic Alloy”, J. Magn. Magn. Mater.,
226-230, 1385-1387 (2001) (Experimental, Magn. Prop., 3)
[2001Goe] Goedecke, T., Sun, W., Lück, R., Lu, K., “Phase Equilibria of the Al-Nd and the Al-Nd-Ni
Systems”, Z. Metallkd., 92, 723-730 (2001) (Equi. Diagram, Experimental, *, #, 24)
[2001Ike] Ikeda, O., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
BCC Phases in the Fe-Rich Portion of hte Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Thermodyn., Experimental, 18)
[2001Si] Si, L., Ding, J., Wang, L., Li, Y.,Tan, H., Yao, B. “Hard Magnetic Properties and
Magnetocaloric Effect in Amorphous NdFeAl Ribbons”, J. Alloys Compd., 316, 260-263
(2001) (Experimental, Magn. Prop., 16)
[2001Wan1] Wang, L., Ding, J., Li, Y., Feng, Y.P., Phuc, N.X., Dan, N.H., “Model of Ferromagnetic
Clusters in Amorphous Rare Earth and Transition Metal Alloys”, J. Appl. Phys., 89(12),
8046-8053 (2001) (Experimental)
[2001Wan2] Wang, L., Ding, J., Li, Y., Feng, Y.P., Wang, X.Z., Phuc, N.X., Dan, N.H., “A Mössbauer
Study of Melt-Spun Nd60Fe30Al10”, J. Magn. Magn. Mater., 224, 143-152 (2001)
(Experimental, Moessbauer, Magn. Prop., 22)
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[2002Bil] Billoni, O.V., Villafuerte, M., Urreta, S., Fabietti, L.M., “Magnetic Viscosity in
Nd60Fe30Al10 Amorphous Alloys”, Physica B, B320(1-4), 288-290 (2002) (Experimental,
Magn. Prop., 5)
[2002Hon] Hong, N.M., Dan, N.H., Phuc, N.X., “Large Unidirectional Anisotropy in Nd60Fe30Al10
Bulk Amorphous Alloys”, J. Magn. Magn. Mater, 242-245, 847-849 (2002) (Experimental,
Magn. Prop., 6)
[2002Jon] Jonen, S., Rechenberg, H.R., Campo, J., “Rare Earth Effects on the Magnetic Behavior of
R6Fe11-xAl3+x Compounds”, J. Magn. Magn. Mater., 242-245, 803-805 (2002) (Crys.
Structure, Experimental, Magn. Prop., 7)
[2002Kon] Kong, H.Z., Ding, J., Dong, Z.L., Wang, L., White, T., Li, Y., “Observation of Cluster in
Re60Fe30Al10 Alloys and the Associated Magnetic Properties”, J. Phys. D: Appl. Phys.,
D35(5), 423-429 (2002) (Experimental, Magn. Prop.)
[2002Lai] Lai, J.K.L., Shao, Y.Z., Shek, C.H., Lin, G.M., Lan, T., “Investigation on Bulk Nd-Fe-Al
Amorphous/nano-Crystalline Alloy”, J. Magn. Magn. Mater., 241, 73-80 (2002)
(Experimental, Magn. Prop., 16)
[2002Sat] Sato Turtelli, R., Triyono, D., Groessinger, R., Michor, H., Espina, J.H., Sinnecker, J.P.,
Sassik, H., Eckert, J., Kumar, G., Sun, Z.G., Fan, G.J., “Coercivity Machanism in
Nd60Fe30Al10 and Nd60Fe20Co10Al10 Alloys”, Phys. Rev. B: Condens. Matter, B66(5),
054441-1-054441-8 (2002) (Experimental, Magn. Prop., 18)
[2003Bra] Bracchi, A., Samwer, K., Schneider, S., Loeffler, J.F. “Random Anisotropy and
Domain-wall Pinning Process in the Magnetic Properties of Rapidly Quenched
Nd60Fe30Al10”, Appl. Phys. Lett., 82(5), 721-723 (2003) (Crys. Structure, Experimental,
Magn. Prop., 13)
[2003Kan] Kang, Y., Chen, N., Shen, J., “Atomistic Simulation of the Lattice Constats and Lattice
Vibrations in RT4Al8 (R = Nd, Sm; T = Cr, Mn, Cu, Fe)”, J. Alloys Compd., 352, 26-33
(2003) (Crys. Structure, 40)
[2003Kum] Kumar, G., Eckert, J., Loser, W., Roth, S., Schultz, L., “Effect of Al on Microstructure and
Magnetic Properties of Mould-Cast Nd60Fe40-xAlx Alloys”, Scr. Mater., 48, 321-325 (2003)
(Crys. Structure, Experimental, Magn. Prop., 18)
[2003Leb] Lebrun, N., “Al-Nd (Aluminum-Neodymium)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 30)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 58)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
Dissolves 0.5 at.% Nd at 632°C
[1990Kon]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
323
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
( Fe)
( Fe)
1538-1394
( Fe)
< 912
cI2
Im3m
W
a = 293.15
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
dissolves up to 45.0 at.% Al at 1310°C
[Mas2]
pure Fe at 25°C [Mas2]
0-18.8 at.% Al, HT [1958Tay]
0-19.0 at.% Al, HT [1961Lih]
0-18.7 at.% Al, 25°C [1999Dub]
( Fe)
1394-912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2, 1993Kat]
dissolves up to 1.2 at.% Al
( Nd)
1021-863
cI2
Im3m
W
a = 413 at 25°C [Mas2]
Dissolves ~12 at.% Al at 690°C
[1996Sac]
( Nd)
< 863
hP4
P63/mmc
La
a = 365.82
c = 1179.66
at 25°C [Mas2]
Dissolves ~2 at.% Al at 650°C
[1996Sac]
Fe4Al13
< 1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7 to107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
74.16-76.70 at.% Al [1986Gri]
sometimes called FeAl3 in the literature
at 76.0 at.% Al [1994Gri]
Fe2Al5< 1169
oC24
Cmcm
a = 765.59
b = 641.54
c = 421.84
at 71.5 at.% Al [1994Bur]
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [1993Kat]
1102-1232
cI16? a = 598.0 at 61 at.% Al [1993Kat]
FeAl
< 1310
cP2
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5-47.5 at.% Al [1961Lih]
36.2-50.0 at.% Al [1958Tay]
39.7-50.9 at.% Al [1997Kog] quenched
from 500°C in water
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
~24-~37 at.% Al [2001Ike]
23.1-35.0 at.% Al [1958Tay]
24.7-31.7 at.% Al [1961Lih]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
324
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [1993Kat]
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
metastable
85.7 at.% Al [1993Kat]
[1998Ali]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[1998Ali]
( Nd3Al11)
1235-917
tI10
I4/mmm
BaAl4
a = 433.8
c = 999.6
lattice parameters for NdAl4(h) [V-C2]
According to [2001Goe] the
transformation temperature decreases
from 934 to 917°C increasing the Nd
content. This phase has a small range of
composition (0.5 at.%) around the
theoretical composition
( Nd3Al11)
< 934
oI28
Immm
La3Al11
a = 435.9
b = 1292.4
c = 1001.7
[V-C2]
NdAl3< 1205
hP8
P63/mmc
Ni3Sn
a = 647.0
c = 460.3
[V-C2] after an annealing of 50 hours at
800°C
Nd(Al1-xFex)2NdAl2< 1460°C
cF24
Fm3m
MgCu2 a = 800.0
0 x 0.5 [1975Dwi]
0 x 0.3 [1991Gri2]
[V-C2] after 7 days annealing at 500°C
NdAl
< 940
oP16
Pbcm
DyAl
a = 594.0
b = 1172.8
c = 572.9
a = 594.2
b = 1173.4
c = 573.3
[V-C2]
[1993Bor]
Nd2Al
< 795
oP12
Pnma
Co2Si
a = 671.6
b = 523.5
c = 965.0
[V-C2]
Nd3Al
< 780
hP8
P63/mmc
Ni3Sn
a = 696.8 to 698.5
c = 541
[V-C2] and [1996Sac]
Nd2(Fe,Al)17 (h) ? stable at higher temperature [1991Gri2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
325
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
Nd2Fe17-xAlx (r)
< 1208
Nd2Fe17
hR57
R3m
Th2Zn17 a = 865.2
c = 1256.9
a = 889
c = 1290
a = 857 to 859
c = 1244 to 1248
0 x ? at 600°C [1991Gri2]
0 x 10.5 at 500°C [1970Viv]
at x = 2 [1989Wei]
at x = 8.5 [1989Wei]
at x = 0 [V-C2]
Nd5Fe17
780
hP228
P63/mcm
Nd5Fe17
a = 2021.4
c = 1232.9
[1991Lan]
* 1, NdFe4-xAl8+x tI26
I4/mmm
ThMn12
a = 881.3
c = 505.8
0 < x < 0.7 [1970Viv]
[1976Bus]
* 2, NdFe2Al10 oC52
Cmcm
YbFe2Al10
a = 900.6
b = 1020.6
c = 906.9
[1998Thi]
* 3,
Nd6Fe9Al(Fe1-xAlx)4
< 900
tI80
I4/mcm
Nd6Fe13Si
or it is ordered
variant of the
R6Fe11Ga3 type
a = 810.45
c = 2310.1
a = 814.72
c = 2307.5
a = 805.2
c = 2294
a = 809.8
c = 2294
a = 815.2
c = 2310
a = 812.8
c = 2311
0.15 x 1 [1991Gri2, 1995Bre]
at x = 0.25
at x = 0.5 [1992Hu]
at x = 0.25 [1995Bre]
at x = 0.45 [1995Bre]
at x = 0.5 [1998Gro]
at x = 0.5 [2000Wan]
* 4, Nd(Fe1-xAlx)2 ? 0.037 x 0.075 [1990Gri]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments/References
326
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
Fig
. 1:
A
l-F
e-N
d.
Rea
ctio
n s
chem
e
Fe-
Nd
Al-
Nd
Al-
Fe-
Nd
(δF
e)(γ
Fe)
, l
13
94
d1
l +
(γF
e) N
d2F
e 17
12
08
p1
L+
(γF
e)(α
δFe)
+N
d2F
e 17
?U1
l +
NdA
l 2 N
dA
l
94
0p2
(γF
e)(α
Fe)
,Nd2F
e 17
91
2d2
(βN
d)
(αN
d),
l
84
3d3
l+N
d2F
e 17
Nd5F
e 17
78
0p4
l (
αNd)
+ N
d5F
e 17
68
5e 3
l +
NdA
l N
d2A
l
79
5p3
l +
Nd2A
l N
d3A
l
78
0p5
l (
βNd)
+ N
d3A
l
69
0e 2
(βN
d)
(αN
d)+
Nd3A
l
65
0e 4
L(α
Fe)
+N
dA
l 2
?e 1
L+
(αF
e)N
dA
l 2+
Nd2F
e 17
?U2
L+
NdA
l 2+
Nd2F
e 17
τ 39
00
P1
L +
τ3 +
Nd2F
e 17
τ 47
50
P2
L+
Nd2F
e 17
τ 4+
Nd5F
e 17
?U4
L+
NdA
l 2τ 3
+ N
dA
l7
20
U3
Nd
Al 2
+τ 3
Nd
Al+
Nd2F
e 17
70
0U5
L+
NdA
l N
d2A
l+τ 3
67
5U7
τ 3+
Νd
Al
Nd2A
l+N
d2F
e 17
67
0U8
L+
(βN
d)
(αN
d)+
Nd3A
l?
U9
L+
Nd2A
lτ 3
+N
d3A
l6
25
U11
L +
τ4
τ 3 +
(αN
d)
64
5U10
L+
Nd5F
e 17
(αN
d)+
τ 46
80
U6
Lτ 3
+ (
αNd)
+ N
d3A
l6
00
E1
?
L+
NdA
l 2+
Nd2F
e 17
L+
(αF
e)+
Nd2F
e 17
L+
Nd2F
e 17+
τ 3L
+N
dA
l 2+
τ 3N
dA
l 2+
Nd2F
e 17+
τ 3
L+
NdA
l+τ 3
L+
Nd2A
l+τ 3
L+
(αN
d)+
Nd3A
l
τ 3+
NdA
l+N
d2F
e 17
L+
τ 4+
τ 3
L+
τ 4+
(αN
d)L
+N
d5F
e 17+
τ 4
NdA
l 2+
(αF
e)+
Nd2F
e 17
τ 3+
Nd2A
l+N
d3A
l
(αN
d)+
τ 3+
Nd3A
l
L+
τ 3+
(αN
d)
τ 3+
τ 4+
(αN
d)
τ 4+
(αN
d)+
Nd5F
e 17
τ 3+
τ 4+
Nd2F
e 17
τ 3+
Nd2A
l+N
d2F
e 17
NdA
l+N
d2A
l+N
d2F
e 17
Nd
Al 2
+N
dA
l+τ 3
NdA
l 2+
NdA
l+N
d2F
e 17
L+
Nd2F
e 17+
τ 4
L+
τ 3+
Nd3A
l
Nd2F
e 17+
τ 4+
Ni 5
Fe 17
Nd
Al+
Nd2A
l+τ 3
327
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
10
20
30
40
10 20 30 40
60
70
80
90
Nd 50.00Fe 0.00Al 50.00
Nd 0.00Fe 50.00Al 50.00
Al Data / Grid: at.%
Axes: at.%
Fe4Al13
Fe2Al5
FeAlNd2Fe17-xAlx
τ1
τ2
Nd3Al11
NdAl3
NdAl2FeAl2
(Al)Fig. 2: Al-Fe-Nd.
Isothermal section at
500°C
20
40
60
80
20 40 60 80
20
40
60
80
Nd Fe
Al Data / Grid: at.%
Axes: at.%
Nd3Al+τ3+(αNd)
Nd2Al+Nd3Al+τ3
τ4
Nd
2 Fe17-x A
lx (r)τ3
Nd3Al
Nd2Al
NdAl
NdAl2
Nd2Fe17-xAlx(r)+NdAl+Nd2Al
Nd2Fe17Nd5Fe17
(αNd)
?
Fig. 3: Al-Fe-Nd.
Isothermal section at
600°C from
[1991Gri2]
328
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Nd
10 20500
600
700
800
900
Nd 70.00Fe 30.00Al 0.00
Nd 70.00Fe 0.00Al 30.00Al, at.%
Tem
pera
ture
, °C
L
L+τ3 L+τ3+Nd2Al
L+τ 3+NdAl
L+NdAl
L+Nd2Al
L+Nd2Al+Nd3Al
τ3+Nd2Al+Nd3Al
τ3+(αNd)+Nd3Al
L+τ3+(αNd) L+τ3+Nd2Al
L+NdAl+Nd2Al
L+Nd5Fe17
L+Nd5Fe17+τ4
L+τ4
L+(αNd)+Nd5Fe17
L+(αNd)+τ4
(αNd)+τ3+τ4
(αNd)+Nd5Fe17+τ4
L+τ3+τ4
L+τ3+NdAl2
U6,680
U10,645 U11,625
E1,600
U7,675
U3,720
L+Nd2Fe17+Nd5Fe17
L+Nd2Fe17
(αNd)+Nd5Fe17
Fig. 4: Al-Fe-Nd.
Vertical section at 70
at.% Nd = constant
329
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
Aluminium – Iron – Nickel
Peter Budberg and Alan Prince,
updated by
Gabriele Cacciamani, Riccardo Ferro, Benjamin Grushko, Pierre Perrot, Rainer Schmid-Fetzer
Literature Data
The first extensive investigation of the Al-Fe-Ni ternary system was the determination of the liquidus
surface at <50 mass% Al ( 75 at.% Al). Since, a critical assessment of the system may be found in
[1980Riv] with minor amendments by [1988Ray] and an update by [1992Bud]. [1994Rag] presented
isothermal sections at 950 and 1050°C in the Al-rich part of the diagram (> 50 at.% Al), an isothermal
section at 1050°C in the Fe-rich part of the diagram (> 50 at.% Fe) and a vertical section along the
Ni3Al-Ni3Fe join. The first calculations of the whole diagram by the Calphad method has been carried out
by [1974Kau] at 1200, 1400, 1600 and 1700 K. The phase diagram calculated at 1200 K looks strongly like
the diagram proposed by [1940Bra1] which represents the structures obtained by a slow cooling method.
Microstructural observations of [1995Guh] after water quenching Fe30Ni20Al50 alloys following annealing
at 420, 620 and 820°C does not contradict phase equilibria proposed by [1980Riv]. Experimental work of
[1993Pov, 1994Gho, 1994Jia, 1999Dyb, 2000Dyb, 2002Bit] on phase equilibria together with the
apparition of quasicrystalline decagonal phases [1989Tsa, 1994Lem, 1996Yam, 1997Sai, 2002Hir,
2003Doe] adds to our knowledge of this ternary system and necessitates an updating of the earlier
assessments by [1980Riv] and [1992Bud]. More recent experimental work are summarized in Table 1. This
ternary system exhibits a continuous series of solid solutions between ,NiAl and ,FeAl (B2 structure, type
CsCl). This fact allows the system to be split into two: the Al-rich portion from 50 to 100 at.% Al and the
Fe-Ni rich region from 0 to 50 at.% Al. The solidus temperatures in the (50 at.% Al) solid solution has
been experimentally determined by [2002Bit].
The Al-rich region has been studied by [1934Fus, 1938Bra, 1940Bra1, 1942Phi, 1943Sch, 1947Ray,
1981Kha, 1982Kha, 1986Sei, 1993Pov, 2000Dyb]. Reviews have been published by [1943Mon, 1952Han,
1961Phi, 1976Mon, 1992Bud, 1994Rag].
The data on the possible constitution of liquidus surfaces in the Al-Fe3Al-Ni3Al field are given in [1934Fus,
2000Dyb]. According to [1938Bra], however, two ternary phases are formed in the composition field
mentioned above: 1(FeNiAl9) and 2(Fe3NiAl10). These data were confirmed by [1940Bra1]. The
conditions of the 1 formation were established by [1943Sch, 2000Dyb]; it crystallizes by a peritectic
reaction (P):
L + Fe4Al13 + NiAl3 1 at 809°C.
This temperature was confirmed by [1981Kha, 1982Kha, 1986Sei, 2000Dyb].
The data on the presence of two invariant transformations in the Al-rich alloys
(E2): L (Al) + 1 + NiAl3 and
(U2): L + Fe4Al13 (Al) + 1
previously obtained by [1942Phi] were also confirmed. These reactions take place at 640 and 650.2°C,
respectively [1943Sch] or at 638 [1942Phi, 1981Kha, 1982Kha, 1986Sei, 2000Dyb] and 649°C [1942Phi],
respectively.
The phase field boundaries in the Al-rich portion of the diagram at 620°C were constructed by [1943Sch]
and isothermal sections at 500 and 550°C by [1947Ray]. These data are in good agreement with each other.
[1938Bra, 1940Bra1] cooled homogenized and afterwards powdered alloys, which were then held at
different temperatures with 10 K min-1 in vacuum. The authors suggest that the section obtained probably
represents a 500°C isothermal.
The phase 1(FeNiAl9) has a homogeneity range from 4.42 to 11.11 at.% Fe and from 7.01 to 13.5 at.% Ni
at 620°C [1943Sch]. By precipitation from liquid Al-rich alloys, [1996Zho] obtains a 1 phase whose
chemical composition lies in the range FexNi2-xAl9 (1 x 1.6). The 1 phase is also easily observed by
reacting Fe-Ni alloys with liquid Al at 700°C [1999Dyb].
330
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
In the reviews [1952Han, 1961Phi] the previously obtained data were generalized though [1961Phi]
virtually followed [1942Phi]. According to [1976Mon], the reactions P, E2 and U2 occur at 809, 639 and
649°C, respectively. The solubility of Ni in Fe3Al is 1.4 to 1.9 at.% and that of Fe in Ni3Al, up to 0.5 at.%.
The FeNiAl9 compound ( 1) has been given a homogeneity range from 3.0 at.% Fe and 17 at.% Ni to 7.5
at.% Fe and 11.5 at.% Ni by [1976Mon].
Using precise investigation techniques, in particular electro-magnetic separation of phases in the
liquid-solid state after annealing at 1050, 950 and 750°C for 3 h, [1981Kha, 1982Kha] established the
position of tie lines between the equilibrium phases. Isothermal sections at 750, 950 and 1050°C were
constructed after prolonged exposures for 40, 15 and 3 d, respectively. These heat treatments allowed
establishment of the formation of a new ternary phase, FeNi3Al10, besides two previously known ( 1 and
2). This phase, according to [1981Kha, 1982Kha], exists in a narrow temperature range and decomposes
at slow cooling so that it has not been found by [1938Bra, 1940Bra1, 1947Ray] and others. The solubility,
at room temperature, of Fe in Ni2Al3 and NiAl3 is 2 and 4 at.%, respectively and that of Ni in FeAl2, Fe2Al5and Fe4Al13 at 1050°C is up to 2, 2 and 10 at.%, respectively [1982Kha].
Between 1050 and 950°C an invariant reaction L + 2 Fe4Al13 + Ni2Al3 takes place [1981Kha, 1982Kha].
The formation of ternary FeNiAl5 was found in a powder sample (composition Fe14.3Ni14.3Al71.4) annealed
at 720°C for 3 h and water quenched; it has a hexagonal structure of the Co2Al5 type [1990Ell]. It is known
that 2 is also isotypic to Co2Al5. According to [1990Ell], the position of homogeneity fields corresponding
to ternary phases may be displaced along the Al isoconcentration line (exactly along FexNi0.286-xAl0.714),
dependent on the heat treatment; during this displacement an Fe to Ni substitution takes place (or a reverse
process may occur). This fact may be explained by the ease of the electron exchange between analogous
metals. In the case of the alloy quenched from 720°C, the Fe:Ni ratio is equal to 1:1; it corresponds to the
FeNiAl5 alloy, so here the FeNiAl5 phase is assumed to lie within the homogeneity range of 2.
[1986Sei] used insufficiently prolonged exposures during annealing. 72 h to 200 h were applied to
homogenize the alloys at temperatures between 1200 and 600°C followed by annealing for 50 h at 1000,
800 and 600°C and water quenching. [1981Kha, 1982Kha] used 72 h at 1050°C, 360 h at 950°C and 960 h
at 750°C, and even then stated that equilibrium was not established at 750°C. This is the reason why the
field of the 2 existence was not confirmed by [1986Sei]. [1986Sei] did also find a two-phase region
NiAl+FeAl at 650, 750, 1000 and 1150°C, which is in contradiction to the results of [1938Bra, 1940Bra1,
1951Bra, 1952Bra], the lattice parameter studies of [1939Lip] and [1972Kot] and the work of [1984Hao].
[1972Kot] found 17 single phase alloys at 950°C with the lattice parameter increasing up to 25 at.% Ni and
then constant up to NiAl. [1984Hao] also shows an ordered CsCl type phase to exist between 1150 and
850°C from the Al-Fe to the Al-Ni side.
Alloys with compositions close to the Fe-Ni side were studied in detail by [1938Bra, 1940Bra1, 1949Bra,
1951Bra, 1952Bra]. The features of the crystallization and the phase constitution of these alloys were
investigated by DTA, X-ray diffraction and metallographic analysis in a temperature range of 750°C to
melting. The position of the phase boundaries in the alloys with < 50 at.% Al is strongly dependent on the
invariant four-phase equilibrium U1 and on the minimum point (point of tangency) of the liquidus and
solidus surfaces. The temperature of the reaction:
U1: L + ' +
was established to be 1380°C [1949Bra]. Taking into account some new data on the formation of the
'(Ni3Al) phase in the binary Al-Ni system [1987Hil, 1988Bre], it must be noted that this temperature could
not exceed 1365°C. A monovariant order-disorder transformation descends from higher Al contents to the
monovariant melting trough p1-e2 (see Fig. 3a). The dotted line belongs to the liquidus concentrations
corresponding to the solidus intersecting with the order-disorder transformation between and as a
second order transformation (see Fig. 14). Older publications [1942Dan, 1949Bra] introduced a transition
type reaction at 12.5 at.% Al and 67.5 at.% Fe [1949Bra] for the liquid with the equation:
L + + , 1350°C,
assuming that the two-phase field + extends up to the liquid, but this has been revised by more recent
experiments [1984Hao], Fig. 14. [1984Hao] applied diffusion couple techniques on samples prepared from
99.95% Fe, 99.95% Ni and 99.9% Al and annealed at temperatures between 850 and 1150°C to determine
the shape of the miscibility gap between and . The exact location of the order-disorder transformation
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to higher Al contents is unknown; in Fig. 3a it is assumed that it contacts directly with the same
transformation in the Al-Fe binary system.
The decomposition of the ( Fe, ) solid solution to a mixture of and on cooling was investigated by
[1940Kiu, 1941Kiu1, 1941Kiu2, 1941Kiu3, 1942Dan, 1949Bra, 1951Bra, 1952Bra, 1984Hao] in detail.
Using X-ray diffraction, [1941Kiu1, 1941Kiu2, 1941Kiu3] investigated both the position of a three-phase
field + + and possible transformations in the solid state in detail. Unfortunately, this field was
incorrectly projected on the composition plane (the phase rule was violated). The position of a three-phase
field + '+ at 1000°C was refined by [1986Bra]; the ' field at 1000°C stretches to 60.9 at.% Ni though
[1949Bra] has supposed that this field stretches to 68 at.% Ni at 1050 and 950°C. The two-phase equilibrium
+ ' was calculated by the cluster variation method with the tetrahedron approximation [1991Eno] and the
results compared with experimental determinations of [1949Bra, 1951Bra]. Experimental investigations of
the - ' and - ' equilibria in the Ni rich corner of the diagram were carried out by [1994Jia] at 1100 and
1300°C using diffusion couples and electron microprobe analysis.
The Ni3Al-FeNi3 section has been studied by [1987Mas] using 99.9 mass% Ni, 99.99 mass% Al and 99.9
mass% Fe, the samples being homogenized at 1050°C for 48 h. Metallographic, X-ray and diffusion couple
techniques have been applied to examine the phase boundaries at 75% Ni. Using neutron diffraction,
[1998Gom] investigated the L12 ordering in the Ni3Al-FeNi3 section at low temperatures.
Binary Systems
The binary boundary systems Al-Ni and Al-Fe are accepted from critical assessments of [2003Sal] and
[2003Pis], respectively. The Fe-Ni binary phase diagram is taken from [1982Kub].
Solid Phases
The crystallographic data of the Al-Fe-Ni phases and their temperature ranges of stability are listed in
Table 2. In general Fe and Ni are not appreciably dissolved in Al, but form solid solutions which extend
significantly into the ternary system.
The Al-Fe based bcc solid solution extends into the ternary and its Ni concentration increases with the
increase of the Al concentration. In the binary Al-Fe system it orders in by a second order transformation
which became first order by adding Ni.
phase (CsCl-type) forms a continuous range of solid solutions between Al-Fe, Al-Ni and toward Fe.
Along the NiAl-Fe direction a miscibility gap is formed between the ordered and disordered solid
solutions. Lattice parameters and hardness measurements in the field have been carried out by [2001Tan].
Site occupancies of Fe in NiAl were first investigated by [1994Dun] by using atom-probe field-ion
microscopy. Then an exhaustive study of lattice parameters, site occupancies and vacancy concentration,
point defects, density and hardness has been carried out by [1997Pik, 2002Pik] over a wide range of
compositions and temperatures in the -region. The triple defect structure was observed across the entire
phase field. In all Al-rich compositions constitutional vacancies were observed. Thermodynamic
predictions that the Fe anti-sites are more stable than the Ni anti-sites in the Al-poor compositions were
qualitatively confirmed. The lattice parameter as a function of composition is reported in Figs. 1a and 1b.
The fcc solid solution extends from the Fe-Ni subsystem to more than 20 at.% Al. With decreasing
temperature it orders in the ' structure (AuCu3 type) at about 75 at.% Ni and forms a continuous solid
solution with the isostructural Ni3Al [1986Bra, 1987Mas, 1998Gom]. Iron can occupy both Al and Ni
sublattices, 78% of Fe atoms occupy Al sublattice for the Fe concentration of 2.5 at.%, while only 54% for
the 9.3 at.% Fe compound [1977Nic]. Dissolution of Fe to at least 7 at.% does not influence the lattice
parameter of ' [1959Gua, 1984Och].
Site occupancies in Fe3Al and, in particular, the substitution of Fe by Ni (about 3 at.%) have been
investigated by neutron diffractometry [1998Sun].
The monoclinic Fe4Al13 phase dissolves up to 12.0 at.% Ni at 800°C and NiAl3 dissolves up to 2.5 at.% Fe
[1996Gru1], Ni2Al3 can dissolve about 2, 4 and 10 at.% Fe at room temperature, 850 and 1050°C,
respectively, Fe2Al5 and FeAl2 can dissolve up to 2 at.% Ni at elevated temperatures [1982Kha].
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No ternary phases were reported in the Al-poor region. In the Al-rich region three stable ternary phases were
revealed. The 1 (Ni,Fe)2Al9 phase isostructural to Co2Al9 is formed at almost constant 82 at.% Al between
4.4 to 11.1 at.% Fe [1943Sch, 1999Dyb, 2000Dyb]. The same phase extends from 9 to 14.5 at.% Fe when
1 precipitates from melt-spun samples [1996Zho].
The hexagonal 2 Fe3NiAl10 phase of the Co2Al5 type has been observed at 1050°C in the
Al70-72.5Fe18-24.5Ni10.5-4.5 composition range [1981Kha]; it has been structurally characterized by
[1990Ell].
Quasiperiodic structures to which higher dimensional crystallography is applicable were discovered in
Al-Fe-Ni alloys since 1989. A number of different decagonal diffraction patterns have been first observed
[1989Tsa] in Al-Fe-Ni alloys prepared by melt quenching. After that decagonal phases have been studied
by several authors [1989Tsa, 1993Tan, 1994Lem, 1996Gru1, 1997Sai, 2000Fre, 2001Hir, 2002Yok,
2003Doe]. The best known is the phase 3 (periodicity of about 0.4 nm), stable between 930 and 847°C in
a range of less than 1 at.% around the Al71Ni24Fe5 composition [1994Gru, 1994Lem, 1996Gru1, 2000Dro,
2003Doe]. It probably corresponds to an unidentified phase FeNi3Al10 previously observed by [1982Kha].
The diffraction patterns of the 3-phase are very similar to those of the Ni-rich decagonal phase found in the
more extensively studied Al-Co-Ni alloy system [1996Gru2]. It was argued by [1996Gru1] that the stable
ternary 3 phase is an extension of a metastable isostructural Al-Ni phase.
Two more metastable D-phases with slightly different diffraction properties were observed by [1993Tan,
1997Sai, 2001Qia] at higher Fe content. Structural models belonging to the space groups P10m2 and
P105/mmc (or P10/mmm, according to [1993Tan]) were found to approximate the HRTEM images of
quasicrystals at Fe30-xNixAl70 with 10 < x < 17 and 17 < x < 20, respectively [1997Sai]. Disorder in these
phases has been studied by X-ray (synchrotron) and neutron diffraction experiments [2000Fre]. [2001Hir]
found that large columnar clusters of atoms with a decagonal section of about 3.2 nm in diameter exist as a
basic structural unit.
It may be noticed that owing to the experimental and interpreting difficulties, also connected to the
dependence of the sample structures on the preparation procedures, the reported description of the Al-Fe-Ni
decagonal phases may be considered still incomplete but representative of a more complex situation.
Pseudobinary Systems
It may be supposed that a pseudobinary section exists in the system. It occurs between FeAl and NiAl which
possess isotypic structures. A series of continuous solid solutions is formed of the CsCl structure type; the
melting point of the alloys decreases monotonically from NiAl to FeAl. However, the tie lines L+ are
essentially perpendicular to that section, which renders it non-pseudobinary. A miscibility gap develops in
at lower temperatures [1986Sei]. These tie lines are again off-section and essentially in the NiAl-Fe
direction as described in more detail under Isothermal Sections.
Invariant Equilibria
The data on the invariant equilibria are given in Table 3 according to [1949Bra] (U1) and [1943Sch] (P, E2,
U2). The U1 temperature was corrected according to [1987Hil, 1988Bre]. The data on the eutectic
decomposition, E1, of the ternary decagonal phase 3 are accepted from [1996Gru1]. A partial reaction
scheme is given in Fig. 2.
Liquidus Surface
The projection of liquidus surfaces of portions of the ternary diagram investigated by [1949Bra] (0 to 50
at.% Al) and [1943Sch] (100 to 88 at.% Al), adapted to the accepted binaries, are given in Fig. 3a, and a
more detailed view of the Al-corner [1942Phi] in Fig. 3b. It should be noted that the position of the
minimum point of the peritectic/eutectic line, e2, at 50 at.% Fe must be above 1350°C, see Fig. 4, and below
the 1365°C of U1. It is assessed at 1360°C. The liquidus surface of is extremely flat in that range. In the
alloys with 85 to 50 at.% Al additional invariant transformations must occur in the range 850 to 1340°C
(besides the four-phase reactions already investigated) where the reactions p3, p4, p5, p6, p7, e3 and e4 of the
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corresponding binary systems enter the ternary. The U-type reaction suggested at ~840°C with a liquid at
about 82 at.% Al [1992Bud] cannot be accepted in view of the firmly established three-phase equilibrium
Fe4Al13 + Ni2Al3 + NiAl3 formed in the reaction E1 at 847°C [1996Gru1].
Isothermal Sections
Isothermal sections between 1350 and 750°C, Figs. 4 - 10, were constructed on the basis of the data obtained
by [1949Bra, 1951Bra, 1981Kha, 1982Kha, 1984Hao, 1986Bra, 1996Gru1]. The location of the
order-disorder transition between and at 1350°C in Fig. 4 is not known but must occur inside the
ternary since in the binary Al-Fe that transition ends at 1310°C. This line is shown dotted in Figs. 5 and 6.
At even lower temperature, Figs. 7 - 10, the peculiar horn-shape develops. This indicates the change from
the second order transition along a single line to the first order transition with a two-phase field + , that
exists only in the ternary. This miscibility gap, taken essentially from [1984Hao] is in qualitative agreement
with the data of [1941Kiu3]. The plotted phase boundaries of [1941Kiu3], however, do not show the
horn-shape with the necessary tricritical point and are therefore not reproduced.
The position of the three-phase field + + ' at 1050 and 950°C in Figs. 7 and 8 was refined based on the
data of [1986Bra] at 1000°C. The data obtained by diffusion couple technique at 1300 and 1100°C [1994Jia]
essentially agree with that, although they show a somewhat different curvature of the phase boundaries. The
'/ + ' and / + ' boundaries of [1994Jia] are curved towards higher Al-content. All sources agree on the
important distribution of Fe in the three phases, showing a decreasing Fe-content in the phase sequence
- '- [1949Bra, 1986Bra, 1994Jia].
The position of phase fields in the Al-rich alloys are given according to [1981Kha, 1982Kha, 1996Gru1].
At 1050 and 950°C, the 2 phase field can be seen; the decagonal phase 3, stable between 930 and 847°C
[1996Gru1], is given in Fig. 9 with other partial equilibria; at 750°C, the 1 phase already exists. The
isothermal section at 620°C of the Al-rich portion of the diagram is shown in Fig. 11 [1943Sch].
The general distribution of phase fields in the whole composition triangle is given in Fig. 12; the data were
obtained by cooling the alloys with a rate of 10°C h-1 from 900°C (for Al-rich alloys, from 600°C) in
[1938Bra, 1940Bra1, 1940Bra2]. Early calculations of isothermal sections for 927, 1127, 1327 and 1427°C
are given by [1974Kau], at that time without modeling the bcc ordering. The - ' phase boundaries have
been calculated in [1991Eno] by cluster variation method using tetrahedron approximation and the
phenomenological Lennard-Jones pair potentials. The results are in a fair agreement with the experimental
data from [1949Bra, 1951Bra].
Temperature – Composition Sections
Two vertical sections parallel to the Fe-NiAl section with some Ni-excess are shown in Figs. 13 and 14, and
the Fe-NiAl section in Fig. 15. The Ni-excess sections may be approximately considered as pseudobinary
sections. By contrast, Fig. 15 is absolutely not pseudobinary with the + tie lines virtually perpendicular
to the section. It is important to note that minute changes of the phase limits in the isothermal sections
correspond to drastic changes in these vertical sections. In this context, the agreement between the sections
reported by [1951Bra, 1984Hao] for Fig. 14 or [1951Bra, 1951Iva] may be considered to be fair. As an
example in Fig. 15, [1951Bra] reports a small three-phase field + + around 80 at.% Fe and 750-850°C,
whereas [1951Iva] reports a continuous single phase field connecting ( Fe) and ( Fe), as shown dashed
in Fig. 15. These alternatives are probably within the experimental error of the phase limit in the
corresponding isothermal sections. It is thus not considered helpful to reproduce the additional vertical
sections reported by [1951Bra] for the Al-excess sections or by [1952Bra] for the sections parallel to Al-Fe.
A similar reasoning applies to the vertical sections reported in the early work of [1933Koe, 1941Kiu3].
The vertical section Ni3Al-Fe3Al [1987Mas] displayed in Fig. 16 is also supported by the data of [1994Jia]
on the Fe-poor + ' equilibrium. The data of [1998Gom] indicate a lower / + ' boundary but are
unacceptably low for the Ni3Al limit.
The + miscibility gap is due to both chemical and magnetic ordering effects. It has been tried to separate
these effects in a Calphad-type calculation, suggesting that the (metastable) miscibility gap in the
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magnetically and chemically disordered state is at much lower temperature compared to the stable gap along
a vertical section Fe97.5Al2.5 - Ni49.5Al50.5 [1994Gho].
Thermodynamics
The temperature and the enthalpy of fusion of the decagonal phase Fe5Ni24Al71 prepared by inductively
melting the pure metals, water cooling, then annealing 300h at 880°C has been respectively determined in
967 ± 5°C and 13.0 ± 0.4 kJ·mol-1 of atoms [1999Hol]. The standard enthalpy of formation of the phase
at different compositions has been measured by Al solution calorimetry by [1993Zub] and, with very good
reproducibility, by [2001Bre]. Their results are reported in Table 4.
Notes on Materials Properties and Applications
Fe is one of the most important constituent of Ni-base superalloys because the B2-type of NiAl phase has a
high melting temperature, high thermal conductivity and high resistance to oxidation. The lack of high
temperature strength may be overcome by the use of Fe or other minor additions such as Ga or Mo
[2002Alb] and a systematic study of correlation between point defects and Fe precipitates has been
undertaken [1998Ko, 2002Alb], together with the influence of iron on physical, mechanical (grain size,
yield strength) and magnetic properties of NiAl [2002Ban, 2002Mun]. Indeed, these compounds would be
of higher practical interest if their attractive high temperature behavior could be combined with good room
temperature formability. This aim may be achieved by introducing a substantial amount of disorder in their
crystal lattice. Several techniques have been proposed like melt spinning, ion irradiation, mechanical
alloying [1991Kos, 1995Gaf, 2001Sur] or introduction of dopants such as carbon [2002Kim].
Nanostructured materials show significant kinetics of reordering even at 300°C. However, complete
reordering could not be achieved, even after long annealing time at 600°C [2002Joa]. Al-Fe-Ni alloys are
good precursors for the preparation of Fe-Ni powders with high surface area and interesting catalyst
properties [1981Kha]. Ternary alloys with nominal compositions Ni30Fe5Al65 and Ni15Fe10Al75 prepared
by mechanical alloying were used to obtain Fe-Ni Raney-type catalysts by leaching aluminium with an
alkaline aqueous solution [2000Zei].
New materials may be obtained through thermal explosion reaction as an alternative to combustion
synthesis. The order of reaction n and the activation energy E of thermal explosive reaction for
Fe30Ni50Al20 (in mass%) has been respectively measured as n = 0.37 and E = 152 kJ·mol–1 [2002He]. The
maximum reaction temperature is 657°C, higher than eutectic temperature between Al and NiAl3, so that
the thermal explosion consists of both liquid and solid state reactions.
Al-Fe-Ni alloys present a shape memory effect in the + field [1992Kai]. The control of the Ms
(Martensite start) temperature, difficult to achieve in Al-Ni alloys because of the very sensitive dependence
on the Al content, is, on the other hand, very easily achieved in the ternary two-phase alloy by manipulating
the composition of the phase through appropriate choice of annealing temperatures.
Miscellaneous
Crystallographic features of decagonal structures are presented in [1996Yam, 2002Hir] and formation rules
for Al-Fe-Ni quasicrystals were pointed out in [2001Qia]. A number of different decagonal diffraction
patterns have been first observed [1989Tsa] in Al-Fe-Ni alloys prepared by melt quenching in the
composition ranges from 9 to 16 at.% Ni, 9 to 21 at.% Fe, in good agreement with the composition range
Fe20-xNi10+xAl70 (0 x 10) more recently proposed by [1993Tan, 1997Sai]. However, more precise
investigations show the possible existence of at least 3 decagonal phases. Quasicrystals Fe20-xNi10+xAl70
were found by the convergent-beam electron diffraction (CBED) method to belong to the
noncentrosymmetric space group P10m2 for 0 x 7 [1993Tan, 1997Sai] and to the centrosymmetric
group P10/mmm for 7 x 10 [1993Tan] and to present periods along the tenfold axis which are multiple
of 0.4 nm [1997Yam]. It is probable that these structures correspond actually to the phases
D1, Fe14.5Ni13Al72.5 and D2, Fe9.83Ni19.34Al70.83 whose structure has been described by [2001Qia].
D1, Fe14.5Ni13Al72.5 is observed to coexist with 2, FeNiAl5. Decagonal phases reveal higher positron
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lifetime than crystalline compounds [1995Wue], which implies higher concentration of structural
vacancies. A characteristic feature of these structures, isotypic with decagonal phases encountered in
Al-Co-Ni and Al-Co-Cu systems [1994Gru] is that they consist of 2 nm clusters with pentagonal symmetry.
The superstructure is due to chemical ordering in the central part of the 2 nm clusters. Star-shaped and
butterfly-shaped tiles observed in quasicrystals are well understood from observations of [2002Yok].
Diffuse scattering from X-rays (synchrotron) and neutrons [2000Fre] shows disordered layers
perpendicular to the unique tenfold axis.
The diffusion experiments, carried out at 1002°C in the B2 ( NiAl) domain of the ternary system presents
anomalous behavior [1976Moy], the interactions among the various components being strongly
composition dependent. This is explained [1997Kai] by the fact that NiAl has a wide composition range and
exhibits two types of structural imperfections depending on the nature of deviation from stoichiometry. In
NiAl, iron was observed to substitute preferentially aluminium atoms whatever the Al/Ni ratio [1994Dun,
2002Ban]. The substitution (up to 10 at.%) of Al by Fe in NiAl decreases the lattice parameter and increases
the Young’s modulus [1991Mas]. More generally, the introduction of Fe increases the hardness of the Al
rich alloys and decreases the hardness in the Ni rich alloys [1997Pik, 2001Tan]. This softening is attributed
to the replacement of Ni anti-site defects with Fe defects on the Al sublattice. On the other hand, the site
preference of Ni in ordered iron aluminide has been determined using ALCHEMI technique (Atom
Location by Chaneling-Enhanced Microanalysis), first in the Fe50Ni5Al45 alloy [1997And], then in the
whole domain (40 to 52 at.% Al) [2002Pik]. Ni was found to occupy the Fe sites exclusively, displacing
Fe to Al anti-sites [2002Ban, 2002Pik]. The influence of Ni on the formation and growth characteristics of
Fe based aluminide diffusion layers has been modelled [1998Akd, 1999Mek] by mean of a quasichemical
method combined with an electronic theory in the pseudopotential approximation; the influence of Fe on
the lattice parameter and hardening of NiAl has been modelled [2002Liu] by first principle quantum
mechanical calculations. The site preference in various solid solutions (FexNi50-x/2Al50-x/2, FexNi50-xAl50
FexNi50Al50-x) have also been modelled [2002Boz] via Monte-Carlo simulation. A phenomenological
model for multicomponent diffusion in the (B2 ordered) phase was presented by [1999Hel] and calculated
diffusion paths were compared with experimental ones given by [1976Moy]. The OTL (ordering tie-line)
approach [2000Ama] confirms the preceding observations showing that, while Ni segregates preferentially
to the Fe sublattice in Al depleted FeAl, Fe segregates preferentially to the Al sublattice in Al depleted NiAl.
The presence of iron improves the fatigue behavior under cyclic accumulated strain [1991Har]. Fracture
thoughness and yield strength of ,NiAl and ,Fe20Ni45Al35 is improved by mechanical alloying with
additions of small amounts of Y2O3 which allows the achievement of fine grain sizes [1991Kos].
References
[1933Koe] Koester, W., “Iron-Nickel-Aluminium System” (in German), Arch. Eisenhuettenwes., 7(4),
257-262 (1933) (Equi. Diagram, Experimental, #, 8)
[1933Osa] Osawa, A., “On the Equilibrium Diagram of Iron-Aluminium System”, The 309th Rep. Res.
Inst. Iron, Steel and Other Metals, 803-823 (1933). (Equi. Diagram, Crys. Structure,
Experimental, 16)
[1934Fus] Fuss, V., “Aluminum-Nickel-Iron” (in German), in “Metallography of Aluminium and its
Alloys”, Berlin, 140-141 (1934) (Equi. Diagram, Review, 1)
[1938Bra] Bradley, A.J., Taylor, A., “An X-Ray Study of the Iron-Nickel-Aluminium Ternary
Equilibrium Diagram”, Proc. Roy. Soc. (London) A, A166, 353-375 (1938) (Equi. Diagram,
Experimental, #, 3)
[1939Lip] Lipson, H., Taylor, A., “Defect Lattices in Some Ternary Alloys”, Proc. Roy. Soc., 173,
232-237 (1939) (Equi. Diagram, Crys. Structure, Experimental, 7)
[1940Bra1] Bradley, A.J., Taylor, A., “An X-Ray Investigation of the Aluminium Rich
Iron-Nickel-Aluminium Alloys after Slow Cooling”, J. Inst. Met., 66, 53-63 (1940) (Equi.
Diagram, Experimental, #, 14)
[1940Bra2] Bradley, A.J., Bragg, W.L., Sykes, C., “Researches into the Structure of Alloys”, J. Iron
Steel Inst., London, 80, 63-156 (1940) (Equi. Diagram, Experimental, Crys. Structure, #, 22)
336
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[1940Kiu] Kiuti, S., “On the Mechanism of a New Transformation and Some Associated New
Reactions in the Iron-Nickel-Aluminium System”, Rep. Aeronaut. Res. Inst. / Imp. Univ.
(Tokyo), 15(17), 601-720 (1940) (Equi. Diagram, Experimental, #, 25)
[1941Kiu1] Kiuti, S., “On the Nature of a Satellite in the X-Ray Pattern of -Crystals, and the
Differentiation of a New Phase ' by the Surface-Recrystallization Method in Certain
Ternary Alloys (I). Part 1. The Iron-Nickel-Aluminium System”, Rep. Aeronaut. Res. Inst.
/ Imp. Univ. (Tokyo), 16(4), 167-204 (1941) (Equi. Diagram, Crys. Structure, #, 16)
[1941Kiu2] Kiuti, S., “An X-Ray Study of the Mechanism of the Splitting Phenomenon of -Crystals in
the Interiors of Some Ternary Alloys (I). Part 1. The Iron-Nickel-Aluminium System”, Rep.
Aeronaut. Res. Ins. / Imp. Univ, (Tokyo), 16(6), 271-298 (1941) (Equi. Diagram, Crys.
Structure, Experimental, #, 12)
[1941Kiu3] Kiuti, S., “An X-Ray Investigation on the Ternary Equilibrium in the
Iron-Nickel-Aluminium System”, Sci. Rep. Tohoku Imp. Univ., 29, 742-794 (1941) (Equi.
Diagram, Crys. Structure, Experimental, #, 30)
[1942Dan] Dannoehl, W., “The Iron-Nickel-Aluminium Phase Diagram” (in German), Arch.
Eisenhuettenwes., 15(7), 321-330 (1942) (Equi. Diagram, #, 33)
[1942Phi] Phillips, H.W., “The Constitution of the Aluminium Rich Alloys of the
Aluminium-Nickel-Iron and Aluminium-Nickel-Silicon Systems”, J. Inst. Met., 68, 27-46
(1942) (Equi. Diagram, Experimental, #, 15)
[1943Mon] Mondolfo, L.F., “Al-Ni-Fe (Aluminum-Nickel-Iron)”, in “Metallography of Aluminium
Alloys”, John Wiley and Sons, Inc., New York, Chapman and Hall, Limited, London, 93-95
(1943) (Equi. Diagram, Review, #, 0)
[1943Sch] Schrader, A., Hanemann, H., “The Aluminium-Rich Region of the System
Aluminium-Iron- Nickel”, (in German), Aluminium, 25(10), 339-342 (1943) (Equi.
Diagram, Experimental, #, 5)
[1947Ray] Raynor, G.V., Pfeil, P.C.L., “The Constitution of the Aluminium-Rich
Aluminium-Iron-Nickel Alloys”, J. Inst. Met., 73(6), 397-419 (1947) (Equi. Diagram,
Experimental, #, 15)
[1949Bra] Bradley, A.J., “Microscopical Studies on the Iron-Nickel- Aluminium System. Part I. +
Alloys and Isothermal Section of the Phase Equilibrium Diagram”, J. Iron Steel Inst.,
(London), 163(1), 19-30 (1949) (Equi. Diagram, Experimental, #, 19)
[1951Bra] Bradley, A.J., “Microscopical Studies on the Iron-Nickel- Aluminium System. Part II. The
Breakdown of Body-Centered Cubic Lattice”, J. Iron Steel Inst., (London), 168(3), 233-244
(1951) (Equi. Diagram, Crys. Structure, Experimental, #, 18)
[1951Iva] Ivanov, O.S., “Main features of the Phase Equilibrium in High-coercive Fe-Ni-Al Alloys”
(in Russian), Dokl. Akad. Nauk SSSR, 78, 1157 (1951) (Equi. Diagram, Experimental, 7)
[1952Bra] Bradley, A.J., “Microscopical Studies on the Iron-Nickel-Aluminium System. Part III.
Transformations of the and ' Phases”, J. Iron Steel Inst., (London), 171(1), 41-47 (1952)
(Equi. Diagram, Experimental, #, 25)
[1952Han] Hanemann, H., “Aluminum-Iron-Nickel” (in German), in “Ternary Alloys of Aluminium”,
Haneman, H., Schrader, A. (Eds.), Vol. 3., Verlag Stahleisen M.B.H. Düsseldorf, 105-109
(1952) (Equi. Diagram, Review, #, 4)
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids 6, 16-37 (1958) (Crys. Structure,
Experimental, 49)
[1959Gua] Guard, R.W., Westbrook, J.H., “Alloying Behavior of Ni3Al ( ') Phase”, Trans. Metall.
Soc. AIME, 215, 807-814 (1959) (Equi. Diagram, Experimental, 27)
[1961Lih] Lihl, F., Ebel, H., “X-ray Examination of the Constitution of Iron-Rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenwes., 32, 483-487 (1961) (Crys.
Structure, Experimental, 12)
[1961Phi] Phillips, H.W.L., “Aluminum-Iron-Nickel”, in “Equilibrium Diagrams of Aluminium Alloy
Systems”, The Alumin. Develop. Assoc., London, 89-90 (1961) (Equi. Diagram, Review, #)
337
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[1965Wal] Walford, L.K., “The Structure of the Intermetallic Phase FeAl6”, Acta Crystallogr., 18,
287-291 (1965) (Crys. Structure, Experimental, 12).
[1972Kot] Kotov, A.P., Zelenin, L.P., Bronfin, B.M., Sidorenko F.A., Gel'd, P.V., “Structure and
Magnetic Properties of Mutual Solid Solutions of Fe and Ni Monoaluminides” (in Russian),
Fiz. Met. Metalloved., 33(3), 602-606 (1972) (Crys. Structure, Magn. Prop.,
Experimental, 11)
[1973Cor] Corby, R.N., Black, P.J. “The Structure of FeAl2 by Anomalous Dispersion Methods”, Acta
Crystallogr., Sect. B: Struct. Crystallogr. Crys. Chem., B29, 2669-2677 (1973) (Crys.
Structure, Experimental, 32).
[1974Kau] Kaufman, L., Nesor, H., “Calculation of superalloy phase diagrams. Part II”, Met. Trans.
(J. of Metals, AIME), 5(7), 1623-1629 (1974) (Equi. Diagram, Calculation, #, 20)
[1976Mon] Mondolfo, L.F., Aluminium Alloys: Structure and Properties, Butterworth, London-Boston,
532-533 (1976) (Equi. Diagram, Review, #, 10)
[1976Moy] Moyer, T.D., Dayananda, M.A., “Diffusion in Fe-Ni-Al alloys”, Metall. Trans. A, 7A(7),
1035-1040 (1976) (Equi. Diagram, Diffusion, Experimental, #, 13)
[1977Nic] Nicholls, J.R., Rawlings, R.D., “A Mössbauer Effect Study of Ni3Al with Iron Additions”,
Acta Metall., 25, 187-194 (1977) (Crys. Structure, Moessbauer, 16)
[1977Sim] Simensen C.J., Vellasamy R, “Determination of Phases Present in Cast Material of an
Al-0.5 wt.% Fe-0.2 wt.% Si Alloy”, Z. Metallkd., 68, 428-431 (1977) (Crys. Structure,
Experimental, 10)
[1980Riv] Rivlin, V.G., Raynor, G.V., “Phase Equilibria in Iron Ternary Alloys. Part 2: Critical
Evaluation of Constitution of Aluminium-Iron-Nickel System”, Int. Met. Rev., 25(3), 79-93
(1980) (Equi. Diagram, Review, #, *, 38)
[1981Kha] Khaidar, M., “Equilibrium of Phases and Intermetallic Compounds of the Ni-Fe-Al System:
Characterization of the Catalysts Deriving from These Compounds” (in French), Tezisy,
Dokl. Grenobl. Univ., 1-71 (1981) (Equi. Diagram, Crys. Structure, #, 67)
[1982Kha] Khaidar, M., Allibert, C.H., Driole, J., “Phase Equilibria of the Fe-Ni-Al System for
Al-Content above 50 at.% and Crystal Structures of Some Ternary Phases”, Z. Metallkd.,
73(7), 433-438 (1982) (Equi. Diagram, Crys. Structure, #, *, 17)
[1982Kub] Kubaschewski, O., Iron Binary Phase Diagrams, Springer Verlag, Berlin, Verlag
Stahleisen, Düsseldorf, 5-9 (1982) (Equi. Diagram, Review, #, 26)
[1984Hao] Hao, S.M., Takayama, T., Ishida, K., Nishizawa, T., “Miscibility Gap in Fe-Ni-Al and
Fe-Ni-Al-Co Systems”, Metall. Trans. A, 15A, 1819-1828 (1984) (Equi. Diagram,
Experimental, #, *, 18)
[1984Och] Ochiai, S., Mishima, Y., Suzuki, T., “Lattice Parameter Data of Ni ( ), Ni3Al ( ') and Ni3Ga
( ') Solid Solutions”, Bull. Res. Lab. Precis. Machin. Electron., Tokyo Inst. Technol., 53,
15-28 (1984) (Crys. Structure, Experimental, 66)
[1984She] Shechtman D., Blech, I., Gratias, D., Cahn, J., “Metallic Phases with Long-Range
Orientational Order and no Translational Symmetry”, Phys. Rev. Lett., 53, 1951-1954
(1984) (Crys. Structure, Experimental, 12)
[1986Bra] Bramfitt, B.L., Michael, J.R., “AEM Microanalysis of Phase Equilibria in Ni3Al
Intermetallic Alloys Containing Iron”, Mater. Res. Soc. Symp. Proc., 62, 201-208 (1986)
(Equi. Diagram, Experimental, #, *, 20)
[1986Fun] Fung, K.K., Yang, C.Y., Zhou, Y.Q., Zhao, J.G., Zhan, W.S., Shen, B.G., ”Icosahedrally
Related Decagonal Quasicrystal in Rapidly Cooled Al-14 at.% Fe Alloy”, Phys. Rev. Lett.
56, 2060-2063 (1986) (Crys. Structure, Experimental, 12)
[1986Sei] Seitzhanov, S.V., “Phase Equilibria in the Aluminium-Nickel-Titanium (Iron) Systems and
the Development of Alloy Catalysators Based on These Systems” (in Russian), Diss. Thesis,
Moscow, Aviation Technology Institute, 1-20 (1986) (Equi. Diagram, Experimental, #, 8)
[1987Hil] Hilpert, K., Kobertz, D., Venugopal, V., Miller, M., Gerads, H., Bremmer, F.J., Nickel, H.,
“Phase Diagram Studies on the Al-Ni System”, Z. Naturforsch. A, 42A, 1327-1332 (1987)
(Equi. Diagram, Experimental, #, 17)
338
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[1987Mas] Masahashi, N., Kawazoe, H., Takasagi, T., Izumi, O., “Phase Relations in the Section
Ni3Al-Ni3Fe of the Al-Fe-Ni System”, Z. Metallkd., 78(11), 788-794 (1987) (Equi.
Diagram, Experimental, #, 18)
[1988Bre] Bremer, F.J., Beyss, M., Karthaus, E.K., Hellwig, A., Schober, T., Welter J.M., Wenzel, H.,
“Experimental Analysis of the Ni-Al Phase Diagram”, J. Cryst. Growth, 87, 185-192 (1988)
(Equi. Diagram, Experimental, #, 16)
[1988Ray] Raynor, G.V., Rivlin, V.G., “Phase Equilibria in Iron Ternary Alloys”, Inst. Metals,
London, 107-121 (1988) (Equi. Diagram, Review, #, 32)
[1989Ell] Ellner, M., Kek, S., Predel, B., “Ni3Al4 - A Phase with Ordered Vacancies Isotypic to
Ni3Ga4”, J. Less-Common Met., 154(1), 207-215 (1989) (Experimental, Crys. Structure, 26)
[1989Tsa] Tsai, An-P., Inoue, A., Masumoto, T., “New Decagonal Al-Ni-Fe and Al-Ni-Co Alloys
Prepared by Liquid Quenching”, Mater. Trans., JIM, 30(2), 150-154 (1989) (Crys.
Structure, Experimental, 21)
[1990Ell] Ellner, M., Röhrer, T., “On the Structure of the Ternary Phase FeNiAl5” (in German), Z.
Metallkd., 81(11), 847-849 (1990) (Equi. Diagram, Crys. Structure, *, #, 23)
[1991Eno] Enomoto, M., Harada, H., Yamazaki, M., “Calculation of `/ Equilibrium Phase
Compositions in Nickel-Base Superalloys by Cluster Variation Method”, Calphad, 15(2),
143-158 (1991) (Assessment, Calculation, Equi. Diagram, #, 34)
[1991Har] Hartfield-Wuensch, S.E., Gibala, R., “Cyclic Deformation of B2 Aluminides”, Mater. Res.
Soc. Symp. Proc.: High-Temp. Order. Intermet. Alloys IV, 213, 575-580 (1991) (Crys.
Structure, Experimental, Mechan. Prop., 12)
[1991Kim] Kim, Y.D., Wayman, C.M., “Transformation and Deformation Behavior of Thermoelastic
Martensite Ni-Al Alloys Produced by Powder Metallurgy Method” (in Korean), J. Korean
Inst. Met. Mater., 29(9), 960-966 (1991) (Mechan. Prop., Experimental, 15)
[1991Kos] Kostrubanic, J., Koss, D.A., Locci, I.E., Nathal, M., “On Improving the Fracture Toughness
of a NiAl-Based Alloy by Mechanical Alloying”, MRS Symp. Proc.: High-Temp. Order.
Intermet. Alloys IV, 213, 679-684 (1991) (Experimental, Phys. Prop., 17)
[1991Mas] Maslenkov, S.B., Filin, S.A., Abramov, V.O., “Effect of Structural State and Alloying of
Transition Metals on the Degree of Hardening of Ternary Solid Solutions Based on Nickel
Monoaluminide”, Russ. Metall., (1), 115-118 (1991) translated from Izv. Akad. Nauk SSSR,
Met., (1), 111-115 (1991) (Crys. Structure, Experimental, Mechan. Prop., 10)
[1991Pat] Patrick, D.K., Chang, K.-M., Miracle, D.B., Lipsitt, H.A., “Burgers vector Transition in
Fe-Al-Ni Alloys”, Mater. Res. Soc. Symp. Proc.: High-Temp. Order. Intermet. Alloys IV,
213, 267-272 (1991) (Mechan. Prop., Experimental, 10)
[1991Yav] Yavari, A.R., Baro, M.D., Fillion, G., Surinach, S., Gialanella, S., Clavaguera-Mora, M.T.,
Desre, P., Cahn, R.W., “L12 Ordering in Disordered NiAlFe Alloys”, Mater. Res. Soc.
Symp. Proc.: High-Temp. Order. Intermet. Alloys IV, 213, 81-86 (1991) (Crys. Structure,
Magn. Prop., Experimental, 7)
[1992Bud] Budberg, P., Prince, A., “Aluminium - Iron - Nickel”, MSIT Ternary Evaluation Program,
in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services
GmbH, Stuttgart; Document ID: 10.10205.1.20 (1992) (Crys. Structure, Equi. Diagram,
Assessment, 32)
[1992Kai] Kainuma, R., Ishida, K., Nishizawa, T., “Thermoelastic Martensite and Shape Memory
Effect in B2 Base Ni-Al-Fe Alloy with Enhanced Ductility”, Metall. Trans. A, 23A(4),
1147-1153 (1992) (Mechan. Prop., Experimental, 24)
[1992Mur] Murakami, Y., Otsuka, K., Hanada, S., Watanabe, S., “Crystallography of Stress-Induced
B2->7R Martensitic Transformation in a Ni-37.0 at.%Al Alloy”, Mater. Trans., JIM, 33(3),
282-288 (1992) (Crys. Structure, Experimental, 25)
[1993Kat] Kattner, U.R. and Burton, B.P., “Al-Fe (Aluminum-Iron)“, in “Phase Diagrams of Binary
Iron Alloys”, Okamoto, H. (Ed), ASM International, Materials Park, OH 44073-0002, 12-28
(1993) (Equi. Diagram, Review, 99)
339
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[1993Kha] Khadkikar, P.S., Locci, I.E., Vedula, K., Michal, G.M., “Transformation to Ni5Al3 in a
63.0 at.% Ni-Al Alloy”, Metall. Trans. A, 24A(1), 83-94 (1993) (Equi. Diagram, Crys.
Structure, Experimental, 28)
[1993Pov] Povarova, K.B., Filin, S.A., Maslenkov, S.B., “Phase Equilibria in the Ni-Al-Me (Me = Co,
Fe, Mn, Cu) Systems in Vicinity of -Phase at 900 and 1100°C”, Russ. Metall. (Engl.
Transl.), (1), 156-169 (1993), translated from : Izv. Akad. Nauk SSSR, Met., (1), 191-205
(1993). (Crys. Structure, Experimental, Equi. Diagram, 19)
[1993Tan] Tanaka, M., Tsuda, K., Terauchi, M., Fujiwara, A., Tsai, A., Inoue, A., “Electron
Diffraction and Electron Microscope Study on Decagonal Qusicrystals on Al-Ni-Fe
Alloys”, J. Non-Cryst. Solids, 153-154, 98-102 (1993) (Crys. Structure, Experimental, 7)
[1993Zub] Zubkov, A.A., Emel’yanenko, L.P., Ul’yanov, V.I., “Enthalpy of Formation of -Phase in
Iron-Alloyed Nickel-Aluminum System”, Russ. Metall. (Engl. Transl.), (3), 35-38 (1993),
translated from Izv. Akad. Nauk SSSR, Met., (3), 39-42 (1993) (Experimental, Thermodyn.,
17)
[1994Bur] Burkhardt, U., Grin, J., Ellner, M., Peters, K., Structure Refinement of the Iron-Aluminum
Phase with the Approximate Composition F2Al5”, Acta Crystallogr., Sect. B: Struct.
Crystallogr. Crys. Chem., B50, 313-316 (1994) (Crys. Structure, Experimental, 9)
[1994Dun] Duncan, A.J., Kaufman, M.J., Liu, C.T., Miller, M.K., “Site Occupation of Iron in
Intermetallic NiAl”, Appl. Surface Sci., 76-77(1-4), 155-159 (1994) (Crys. Structure,
Experimental, 17)
[1994Gho] Ghosh, G., Olson, G.B., Kinkus, T.J., Fine, M.E., “Phase Separation in Fe-Ni-Al and
Fe-Ni-Al-Cr Alloys”, “Solid Solid Phas. Transform.” Proc. Int. Conf. Solid-Solid Phase
Transform. Inorg. Mater., 359-364 (1994) (Calculation, Thermodyn., Experimental, #, 13)
[1994Gri] Grin, J., Burkhardt, U., Ellner, M., Peters, K., “Refinement of the F4Al13 Structure and its
Relationship to Quasihomological Homeotypical Structures”, Z. Kristallogr., 209, 479-487
(1994) (Crys. Structure, Experimental, 39)
[1994Gru] Grushko, B., Urban, K., “A Comparative Study of Decagonal Quasicrystalline Phase”,
Philos. Mag. B, 70B(5), 1063-1075 (1994) (Crys. Structure, Experimental, 26)
[1994Jia] Jia, C.C., Ishida, K., Nishizawa, T., “Partition of Alloying Elements Between (A1), `
(L12) and (B2) Phases in Ni-Al Base Systems”, Metall. Mater. Trans. A, 25A, 473-485
(1994) (Crys. Structure, Experimental, Equi. Diagram, #, 25)
[1994Lem] Lemmerz, U., Grushko, B., Freiburg, C., Jansen, M., “Study of Decagonal Quasicrystalline
Phase Formation in the Al-Ni-Fe Alloy System”, Philos. Mag. Lett., 69(3), 141-146 (1994)
(Crys. Structure, Experimental, 9)
[1994Rag] Raghavan, V., “The Al-Fe-Ni System”, J. Phase Equilib., 15(4), 411-413 (1994) (Equi.
Diagram, Review, 14)
[1995Ell] Ellner, M., “Polymorphic Phase Transformation of Fe4Al13 Causing Multiple Twinning
with Decagonal Pseudosymmetry”, Acta Crystallogr., Sect. B: Struct. Crystallogr. Crys.
Chem., B51, 31-36 (1995) (Crys. Structure, Experimental, 28)
[1995Gaf] Gaffet, E., “Structural Investigation of Mechanicall Alloyed (NiAl)1-x(M)x (M = Fe, Zr)
Nanocrystalline and Amorphous Phases”, NanoStruct. Mater., 5(4), 393-409 (1995) (Crys.
Structure, Mechan. Prop., Experimental, 58)
[1995Guh] Guha, S., Baker, I., Munroe, P.R., “The Microstructures of Multiphase Ni-20Al-30Fe and
its Constituent Phases”, Mater. Charact., 34, 181-188 (1995) (Experimental, Equi.
Diagram, #, 11)
[1995Wue] Wuerschum, R., Troev, T., Grushko, B., “Structural Free Volumes and Systematics of
Positron Lifetimes in Quasicrystalline Decagonal and Adjacent Crystalline Phases of
Al-Ni-Co, Al-Cu-Co, and Al-Ni-Fe Alloys”, Phys. Rev. B, 52B(9), 6411-6416 (1995) (Crys.
Structure, Experimental, Equi. Diagram, 37)
[1996Gru1] Grushko, B., Lemmerz, U., Fischer, K., Freiburg, C., “The Low-Temperature Instability of
the Decagonal Phase in Al-Fe-Ni”, Phys. Status Solidi A, 155A, 17-30 (1996)
(Experimental, Equi. Diagram, 29)
340
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[1996Gru2] Grushko, B., Holland-Moritz, D., “High-Ni Al-Ni-Co Decagonal Phase”, Scr. Mater.,
35(10), 1141-1146 (1996) (Experimental, Crys. Structure, 19)
[1996Pau] Paufler, P., Faber, J., Zahn, G., “X-Ray Single Crystal Diffraction Investigation on
Ni1+xAl1-x”, Acta Crystallogr., Sect. A : Found. Crystallogr., A52, C319 (1996) (Crys.
Structure, Experimental, Abstract, 3)
[1996Vik] Viklund, P., Häußermann, U., Lidin, S., “NiAl3: a Structure Type of its Own?”, Acta
Crystallogr., Sect. A: Found. Crystallogr., A52, C321 (1996) (Crys. Structure,
Experimental, Abstract, 0)
[1996Yam] Yamamoto, A., “Crystallography of Quasiperiodic Crystals”, Acta Crystallogr., Sect. A:
Found. Crystallogr., A52, 509-560 (1996) (Calculation, Crys. Structure, Review, 211)
[1996Zho] Zhongtao, Z., Yinyan, L., Qihua, Z., Zhengxin, L., Ruzhang, M., “Mössbauer Study of
Precipitates in Rapidly Solidified Al-Fe-Ni Alloys”, Z. Metallkd., 87(1), 40-44 (1996)
(Experimental, Moessbauer, Phase Configurations, 12)
[1997And] Anderson, I.M., “Alchemi Study of Site Distributions of 3d-Transition Metals in
B2-Ordered Iron Aluminides”, Acta Mater., 45(9), 3897-3909 (1997) (Calculation, Crys.
Structure, Experimental, Theory, 26)
[1997Bou] Bouche, K., Barbier, F., Coulet, A., “Phase Formation During Dissolution of Nickel in
Liquid Aluminium”, Z. Metallkd., 88(6), 446-451 (1997) (Thermodyn., Experimental, 15)
[1997Kai] Kainuma, R., Ikenoya, H., Ohnuma, I., Ishida, K., “Pseudo-Interface Formation and
Diffusion Behaviour in the B2 Phase Region of NiAl-Base Diffusion Couples”, Def. Diffus.
Forum, 143-147, 425-430 (1997) (Crys. Structure, Experimental, Equi. Diagram, Phys.
Prop., 10)
[1997Pik] Pike, L.M., Chang, Y.A., Liu, C.T., “Solid-Solution Hardening and Softering by Fe
Additions to NiAl”, Intermetallics, 5, 601-608 (1997) (Crys. Structure, Mechan. Prop.,
Experimental, 18)
[1997Poh] Pohla, C., Ryder, P.L., “Crystalline and Quasicrystalline Phases in Rapidly Solidified Al-Ni
Alloys”, Acta Mater., 45, 2155-2166 (1997) (Crys. Structure, Experimental, 48)
[1997Pot] Potapov, P.L., Song, S.Y., Udovenko, V.A., Prokoshkin, S.D., “X-ray Study of Phase
Transformations in Martensitic Ni-Al Alloys”, Metall. Mater. Trans. A, 28A, 1133-1142
(1997) (Crys. Structure, Experimental, 40)
[1997Sai] Saiton, K., Tsuda, K., Tanaka, M., “Structural Models for Decagonal Quasicrystals with
Pentagonal Atom-Cluster Columns”, Philos. Mag. A, 76A(1), 135-150 (1997) (Crys.
Structure, Experimental, 14)
[1997Yam] Yamamoto, A., Weber, S., “Superstructure and Color Symmetry in Quasicrystals”, Phys.
Rev. Lett., 79(5), 861-864 (1997) (Crys. Structure, Experimental, 20)
[1998Akd] Akdeniz, M.V., Mekhrabon, A.O., “The Effect of Substitutional Impurities on the Evolution
of Fe-Al Diffusion Layer”, Acta Mater., 46(4), 1185-1192 (1998) (Calculation,
Thermodyn., 55)
[1998Ali] Aliravci, C.A., Pekgueleryuez, M.O., “Calculation of Phase Diagrams for the Metastable
Al-Fe Phases Forming in Direct-chill (DC)-cast Aluminium Alloy Ingots”, Calphad, 22,
147-155 (1998) (Calculation, Equi. Diagram, #, 20)
[1998Gom] Goman’kov, V.I., Tret’yakova, S.M., Monastyrskaya, E.V., Fykin, L.E., “Structural
Diagrams of Quasi Binary Alloys Ni3Fe-Ni3Al, Ni3Mn-Ni3Al, and Ni3Mn-Ni3Ga”, Russ.
Metall., (6), 125-131 (1998), translated from Izv. Akad. Nauk SSSR, Met., (6), 104-108
(1998) (Experimental, Equi. Diagram, #, 15)
[1998Ko] Ko, H.-S., Park, H.-S., Hong, K.-T., Lee, K.-S., Kaufman, M.J., “The Effects of the Point
Defects on Precipitation in NiAlFe Alloys”, Scr. Mater., 39(9), 1267-1272 (1998)
(Experimental, Equi. Diagram, 12)
[1998Rav] Ravelo, R., Aguilar, J., Baskes, M., Angelo, J.E., Fultz, B., Holian, B.L., “Free Energy and
Vibrational Entropy Difference between Ordered and Disordered Ni3Al”, Phys. Rev. B,
57B(2), 862-869 (1998) (Thermodyn., Theory, Calculation, 43)
341
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[1998Sun] Sun, Z.Q., Yang, W.Y., Shen, L.Z., Huang, Y.D., Zhang, B.S., Yang, J.L., “Neutron
Diffraction Study on Site Occupation of Substitution Elements at Sub Lattices in Fe-Al
Intermetallics”, Mater. Sci. Eng. A, 258A, 69-74 (1998) (Crys. Structure, Experimental,
Magn. Prop., Mechan. Prop., 19)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-rich Fe-Al
Alloys”,Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 15)
[1999Dyb] Dybkov, V.I., “Physicochemical and Structural Investigations of Materials. Phase
Formation at an Interface Beetween Aluminium and an Iron-Nickel Alloy”, Powder Metall.
Met. Ceram., 38(11-12), 590-596 (1999) (Experimental, Mechan. Prop., Equi.
Diagram, #, 10)
[1999Hel] Helander, T., Agren, J., “Diffusion in the B2-B.C.C. Phase of the Al-Fe-Ni System -
Application of a Phenomenological Model”, Acta Mater., 47(11), 3291-3300 (1999)
(Assessment, Calculation, Thermodyn., Diffusion, #, 20)
[1999Hol] Holland-Moritz, D., Lu, I.-R., Wilde, G., Schroers, J., Grushko, B., “Melting Entropy of
Al-Based Quasicrystals”, J. Non-Cryst. Solids, 250-252, 829-832 (1999) (Experimental,
Thermodyn., 17)
[1999Mek] Mekhrabov, A.O., Akdeniz, M.V., “Effect of Ternary Alloying Elements Addition on
Atomic Ordering Characteristics of Fe-Al Intermetallics”, Acta Mater., 47(7), 2067-2075
(1999) (Calculation, Theory, Thermodyn., 63)
[2000Ama] Amancherla, S., Banerjee, R., Banerjee, S., Fraser, H. L., “Ordering in Ternary B2 Alloys”,
Inter. J. Ref. Met. Hard Mater., 18(4-5), 245-252 (2000) (Calculation, Experimental, Magn.
Prop., Equi. Diagram, Thermodyn., 23)
[2000Dro] Drobek, T., Heckl, W.M., “Scanning Probe Microscopy Studies of the Surface of Decagonal
Quasicrystals in Ambient Conditions”, Mater. Sci. Eng. A, 294A-296A, 878-881 (2000)
(Crys. Structure, Experimental, 16)
[2000Dyb] Dybkov, V.I., “Interaction of Iron-Nickel Alloys with Liquid Aluminium Part II. Formation
of Intermetallics”, J. Mater. Sci., 35, 1729-1736 (2000) (Experimental, Equi. Diagram, #, 9)
[2000Fre] Frey, F., “Disorder Diffuse Scattering of Decagonal Quasicrystals”, Mater. Sci. Eng. A,
294A-296A, 178-185 (2000) (Crys. Structure, Experimental, 15)
[2000Zei] Zeifert, B.H., Salmones, J., Hernandez, J.A., Reynoso, R., Nava, N., Reguera, E.,
Cabanas-Moreno, J.G., Aguilar-Rios, G., “X-Ray Diffraction and Moessbauer
Characterization of Raney Fe-Ni Catalysts”, J. Radioanal. Nucl. Chem., 245(3), 637-639
(2000) (Crys. Structure, Moessbauer, 10)
[2001Bre] Breuer, J., Gruen, A., Sommer, F., Mittemeijer, E.J., “Enthalpy of Formation of B2-Fe1-xAlxand B2-(Ni,Fe)1-xAlx”, Metall. Mater. Trans. B, 32B, 913-918 (2001) (Experimental,
Thermodyn., 18)
[2001Hir] Hiraga, K., Ohsuna, T, “The Structure of an Al-Ni-Fe Decagonal Quasicrystal Studied by
High-Angle Annular Detector Dark-Field Transmission Electron Microscopy”, Mater.
Trans., JIM, 42, 894-896 (2001) (Crys. Structure, Experimental, Equi. Diagram, 31)
[2001Ike] Ikeda, O., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
BCC Phases in the Fe-rich Portion of the Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Equi. Diagram, Experimental, Mechan. Prop., 18)
[2001Qia] Qiang, J.-B., Wang, D.-H., Bao, C.-M., Wang, Y.-M., Xu, W.-P., Song, M.-L., Dong, Ch.,
“Formation Rule for Al-Based Ternary Quasi-Crystals: Example of Al-Ni-Fe Decagonal
Phase”, J. Mater. Res., 16(9), 2653-2660 (2001) (Crys. Structure, Experimental, Equi.
Diagram, 31)
[2001Sav] Savin, O.V., Stepanova, N.N., Akshentsev, Yu.N., Rodionov, D.P., “Ordering Kinetics in
Ternary Ni3Al-X Alloys”, Scr. Mater., 45(8), 883-888 (2001) (Crys. Structure, Electr.
Prop., Experimental, Kinetics, 18)
[2001Sur] Suryanarayana, C., “Mechanical Alloying and Milling”, Prog. Mater. Sci., 46(1-2), 1-184
(2001) (Crys. Structure, Experimental, Kinetics, Equi. Diagram, Review, Thermodyn., 932)
342
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[2001Tan] Tan, Y., Shinoda, T., Mishima, Y., Suzuki, T., “Stoichiometry Splitting of Beta Phase in
Ni-Al-Mn, Ni-Al-Co and Ni-Al-Fe Ternary Systems”, Mater. Trans., JIM, 42(3), 464-470
(2001) (Crys. Structure, Experimental, Mechan. Prop., Equi. Diagram, 16)
[2002Alb] Albiter, A., Bedolla, E., Perez, R., “Microstructure Characterization of the NiAl
Intermetallic Compound with Fe, Ga and Mo Additions Obtained by Mechanical Alloying”,
Mater. Sci. Eng. A, 328A, 80-86 (2002) (Crys. Structure, Mechan. Prop., Experimental, 14)
[2002Ban] BanerJee, R., Amancherla, S., Banerjee, S., Fraser, H.L., “Modeling of Site Occupancies in
B2 FeAl And NiAl Alloys with Ternary Additions”, Acta Mater., 50, 633-641 (2002)
(Calculation, Crys. Structure, Experimental, Equi. Diagram, 21)
[2002Bit] Bitterlich, H., Loeser, W., Schultz, L., “Reassessment of Al-Ni and Ni-Fe-Al Solidus
Temperatures”, J. Phase Equilib., 23(4), 301-304 (2002) (Experimental, Equi. Diagram, 18)
[2002Boz] Bozzolo, G. H., Khalil, J., Noebe, R. D., “Modeling of the Site Preference in Ternary
B2-Ordered Ni-Al-Fe Alloys”, Comput. Mater. Sci., 24(4), 457-480 (2002) (Calculation,
Crys. Structure, 22)
[2002He] He, X., Han, J., Zhang, X., “Kinetic Parametres of the Thermal Explosion Reaction of
Ni-Al-Fe System”, Key Eng. Mater., 217, 51-54 (2002) (Experimental, Kinetics, 7)
[2002Hir] Hiraga, K., “The Structure of Quasicrystals Studied by Atomic-Scale Observations of
Transmission Electron Microscopy”, Adv. Imag. Electr. Phys., 122, 1-86 (2002) (Review,
Crys. Structure, 85)
[2002Joa] Joardar, J., Pabi, S.K., Fecht, H.-J., Murty, B.C., “Stability of Nanocrystalline Disordered
NiAl Synthesized by Mechanical Alloying”, Philos. Mag. Lett., 82(9), 469-475 (2002)
(Experimental, Kinetics, 16)
[2002Kim] Kim, S.H., Kim, M.C., Lee, J.H., Oh, M.H., Wee, D.M., “Microstructure Control in
Two-Phase (B2 + L12) Ni-Al-Fe Alloys by Addition of Carbon”, Mater. Sci. Eng. A,
329A-331A, 668-674 (2002) (Experimental, Equi. Diagram, Mechan. Prop., 20)
[2002Liu] Liu, C.T., Fu, C.L., Pike, L.M., Easton, D.S., “Magnetism-Induced Solid Solution Effects
in Intermetallic”, Acta Mater., 50, 3203-3210 (2002) (Calculation, Crys. Structure,
Experimental, Mechan. Prop., 21)
[2002Mun] Munroe, P.R., George, M., Baker, I., Kennedy, F.E., “Microstructure, Mechanical
Properties and Wear of Ni-Al-Fe Alloys”, Mater. Sci. Eng. A, 325A, 1-8 (2002)
(Experimental, Mechan. Prop., Equi. Diagram, 35)
[2002Pik] Pike, L.M., Anderson, I.M., Liu, C.T., Chang, Y.A., “Site Occupancies, Point Defect
Concentrations, and Solid Solution Hardening in B2 (Ni, Fe)Al”, Acta Mater., 50(15),
3859-3879 (2002) (Calculation, Crys. Structure, Experimental, Mechan. Prop., 38)
[2002Yok] Yokosawa, T., Saitoh, K., Tanaka, M., Tsai, A.P., “Structural Variations in Local Areas of
an Al70Ni15Fe15 Decagonal Quasicrystal and the Interpretation by the 1-nm Column-Pair
Scheme”, J. Alloys Compd., 342, 169-173 (2002) (Crys. Structure, Experimental, 10)
[2003Doe] Doeblinger, M., Wittmann, R., Grushko, B., “Initial Stages of the Decomposition of the
Decagonal Phase in the System Al-Ni-Fe”, J. Alloys Compd., 360, 162-167 (2003) (Crys.
Structure, Experimental, 17)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, 58)
[2003Sal] Saltykov, P., Cornish, L., Cacciamani, G., “Al-Ni (Aluminium-Nickel)”, MSIT Binary
Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science
International Services GmbH, Stuttgart; to be published, (2003) (Equi. Diagram, Review,
164)
343
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
Table 1: Recent Investigations of the Al-Fe-Ni System
Reference Experimental Technique Temperature/ Composition/ Phase Range
Studied
[1989Tsa] New decagonal phases prepared by liquid
quenching
9 to 21 at.% Fe, 9 to 16 at.% Ni,
[1990Ell] Crystal structure FeNiAl5
[1991Har] Texture measurements, cyclic deformation Fe60Al40 and Fe20Ni50Al30
[1991Kos] Fracture toughness, grain size effects,
strain-stress measurements
Fe20Ni45Al35
[1991Pat] Transition in Burgers’ vector (FexNi1-x)60Al40 (0 x 1)
[1991Mas] Crystal structure, Hardness, Young’s
modulus
FexNi50Al50-x (0 x 10)
[1991Yav] Magnetization of ' alloys obtained by cold
working or melt spinning
10 to 13 at.% Fe, 16 to 17.4 at.% Al
[1992Kai] Shape memory effect, stress-strain curves,
Ms temperature
Fe57Ni25Al18, 1000-1300°C
[1993Pov] Phase equilibria, Electron microprobe
analysis, X-ray analysis
> 50 at.% Al, 900-1100°C
[1993Zub] Enthalpies of formation, enthalpies of
dilution in liquid Al
0 to 10 at.% Fe, 40 to 50 at.% Ni, 800°C
[1994Dun] Crystal structure, atom probe field-ion
microscope
Fe0.3Ni50Al49.7 and Fe2.2Ni47.8Al50
[1994Gho] Spinodal decomposition by transmission
electron microscopy, field-ion microscopy
Fe-23.3 mass% Ni-9.4 mass% Al, water
quenched from 1300°C
[1994Jia] Equilibria - ' and - ', diffusion couples,
electron microprobe analysis
< 6 mass% Fe, < 22 mass% Al,
1100-1300°C
[1994Lem] Stability of the decagonal phase 23 to 24.6 at.% Ni, 4.3 to 5.3 at.% Fe,
800 to 940°C ( 3 phase)
[1995Gaf] Mechanical alloying, crystal structure NiAl-Fe join, room temperature
[1995Wue] Structural vacancies, positron lifetimes
measurements
< 25 at.% Fe, 20-25 at.% Ni
[1996Gru1] Decagonal phase, Stability Fe5Ni24Al71, inductive melting then
annealing 340h at 880°C ( 3 phase)
[1996Zho] Crystal structure, Mössbauer FexNi2-xAl9 (1 x 1.6) ( 1 phase)
[1997Pik] Lattice parameters, bulk density, hardness
measurements
0 to 12 at.% Fe, 40 to 52 at.% Al
water quenched from 1000°C
[1997Sai] Decagonal phases, Crystal Structure,
Convergent-beam electron diffraction
Fe30-xNixAl70 (10 x 17) (D1 phase)
[1998Gom] Neutron diffraction, Order-disorder
equilibrium
FeNi3-Ni3Al join, 500-1000°C
[1998Sun] Crystal structure, neutron diffraction study Fe72Ni3Al25
[1999Dyb] Interface Al-intermetallic layers by electron
probe microanalysis
Reaction between liquid Al and Fe-Ni alloys
at 700°C
344
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
[1999Hol] DTA investigation, Melting point and
enthalpy of fusion of quasicrystals
Fe5Ni24Al71 quenched from the melt then
annealed 300h at 880°C ( 3 phase)
[2000Dro] Scanning electron microscopy, atomic
force microscopy
Fe5Ni23.5Al71.5 quenched from the melt,
then annealed 51 h at 900°C ( 3 phase)
[2000Dyb] Liquidus surfaces, phase field in the solid
state
> 60 mass% Al, < 800°C
[2000Fre] Diffuse scattering of X-rays and neutrons in
decagonal phase
Fe5Ni23.5Al71.5 ( 3 phase)
[2001Bre] Enthalpies measurements, differential
solution calorimetry
FexAl1-x and FexNiyAlz (x = 0-0.6, y =
0-0.55, z = 0.35-0.50), 800°C
[2001Hir] Crystal structure, atomic scale observation
by scanning transmission electron
microscopy
4.7 at.% Fe, 23.7 at.% Ni,
[2001Sav] Crystal structure, Order-disorder transition,
electrical resistivity
Fe8Ni71Al21, 1000-1850°C
[2001Tan] Crystal parameters and hardness measured
in the domain
< 60 at.% Al, powder homogenized 1h at
850°C
[2002Bit] Solidus determination, high temperature
differential thermal analysis
NixAl100-x (45 < x < 47) and FeyNi50-yAl50
(0 < y < 50), 1259-1681°C
[2002Joa] Nanostructured alloy, kinetics of reordering Fe20Ni40Al40, 300-600°C
[2002Mun] Microstructure, tensile and compressive
strength, hardness and wear tests
Fe-NiAl join (0 to 44 at.% Fe), 500-900°C
[2002Pik] Hardness, Vacancy concentration, Atomic
site occupancy in the domain, ALCHEMI
technique
40 to 52 at.% Al, samples quenched from
700 and 1000°C
[2001Qia] Decagonal phases, crystal structures Fe14.5Ni13Al72.5 and Fe12Ni17.5Al70.5 (D1
and D2 phases)
[2002Yok] Crystal structure of decagonal phase,
high-angle annular dark-field scanning
transmission electron microscope
Fe15Ni15Al70, prepared with a single roller
melt-spinning apparatus (D1 phase)
Reference Experimental Technique Temperature/ Composition/ Phase Range
Studied
345
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
Table 2: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 dissolves 0.03 at.% Fe at 652°C and
0.025 at.% Ni at 640°C [L-B]
, Fe1-x-yNixAly
( Fe)
1394-912
(Ni)
< 1455
cF4
Fm3m
Cu
a = 352.40
a = 364.67
at x = 0, 0 y 0.013
at y = 0, 0 x 1
at x + y = 1, 0 y 0.02
at x = 0, y = 0 and 915°C [V-C2, Mas2]
at x = 1, y = 0 and 20°C [V-C2, Mas2]
(at y = 0 and 20°C a vs x is not linear and
has a maximum for x 0.4)
, Fe1-x-yNixAly
( Fe)
1538-1394
( Fe)
<912
cI2
Fm3m
W
a = 286.65
a = 293.22
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
at x = 0, 0 y 0.045
at y = 0, 0 x 0.055 ( Fe)
at y = 0, 0 x 0.035 ( Fe)
at x = 0, y = 0 and 25°C [V-C2]
at x = 0, y = 0 and 1394°C [V-C2]
at x = 0, 0 y 0.019, 20°C [1958Tay]
at x = 0, 0 y 0.019, 20°C [1961Lih]
at x = 0, 0 y 0.010, 20°C [1999Dub]
, (Fe1-xNix)1+yAl1-y
FeAl
< 1310
NiAl
< 1638
cP2
Pm3m
CsCl a = 290.90
a = 290.17
a = 289.77
a = 289.66
a = 289.53
a = 288.7
a = 288.0
at x = 0, 0.10 y 0.54 (FeAl)
at x = 1, 0.16 y 0.38 (NiAl)
at x = 0, y = 0 (50 at.%Al)
at x = 0, y = 0.124 (43.8 at.%Al)
at x = 0, y = 0.182 (40.9 at.%Al)
at x = 0, y = 0.234 (38.3 at.%Al)
x = 0, y = 0.276 (36.2 at.%Al) [1958Tay]
at x = 1, y = 0 (50 at.% Al)
at x = 1, y = 0.08 (46 at.%Al) [1996Pau]
(see also Figs. 1a and 1b)
Fe4Al13
< 1157
mC102
C2/m
Fe4Al13
a = 1549.2(2)
b = 807.8(2)
c = 1247.1(1)
= 107.69(1)°
a = 1543.7
b = 810.9
c = 1243.0
= 107,66°
74.5-76.6 at.% Al at 0 at.% Ni [2003Pis]
at 76.0 at.% Al [1994Gri]
[1982Kha] at 10 at.% Ni
dissolves
12 at.% Ni at 800°C [1996Gru1]
10 at.% Ni at 950°C [1982Kha]
6 at.% Ni at 1050°C [1982Kha]
Fe2Al5< 1169
oC24
Cmcm
Fe2Al5 a = 765.59
b = 641.54
c = 421.84
70-73 at.% Al at 0 at.% Ni [1993Kat]
at 71.5 at.% Al [1994Bur]
dissolves 2 at.% Ni at 1050°C [1982Kha,
1993Pov]
346
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
66-66.9 at.% Al at 0 at.% Ni [1993Kat]
at 66.9 at.% Al [1973Cor]
dissolves 2.5 at.% Ni at 1050°C
[1982Kha]
1102 - 1232
cI16? a = 578.0 at 61 at.% Al [1933Osa]
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.98
a = 579.30 to 578.86
a = 579.98
a = 579.30 to 578.92
~24 - ~37 at.% Al in Al-Fe [2001Ike]
Extends less than 10 at.% Ni into the
ternary [1940Bra2]
at 24.35 at.% Al [1998Sun]
23.1-35.0 at.% Al [1958Tay]
at 25 at.% Al and 3 at.% Ni
neutron diffr. [1998Sun]
24.7-31.7 at.% Al [1961Lih]
O-Fe4Al13 oC~50
Cmmm
Fe4Al13
a = 2377.1
b = 775.10
c = 403.36
Metastable (?)
Described by the authors in terms of the
Bmmm group. It was suggested that
multiple twinning of this structure
exhibits decagonal pseudo-symmetry
[1995Ell]
Fe2Al9 mP22
P21/a
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
Metastable [1977Sim]
FeAl6 oC28
Cmc21
MnAl6
a = 646.4
b = 744.0
c = 877.9
Metastable [1965Wal]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[1998Ali]
I(Al-Fe) Icosahedral, Metastable [1984She]
',(Ni3Al)
< 1372
(FeNi3)
< 517
cP4
Pm3m
AuCu3
a = 358.9
a = 356.32
a = 357.92
a = 355.25
73 to 76 at.% Ni at 0 at.% Fe [Mas2]
dissolves up to 15 at.% Fe [1986Bra,
1993Pov]
63-85 at.% Ni at 0 at.% Al and 350°C
[1982Kub]
complete solid solution with FeNi3 at
T<500°C [1987Mas]
at 75 at.% Ni, 0 at.% Fe [1993Kha]
disordered [1998Rav]
ordered [1998Rav]
at 75 at.% Ni, 0 at.% Al, 20°C [L-B]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
347
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
Ni3Al4< 580
cI112
Ia3d
Ni3Ga4
a = 1140.8 [1989Ell, V-C]
Ni2Al3< 1138
hP5
P3m1
Ni2Al3 a = 402.8
c = 489.1
36.8 to 40.5 at.% Ni at 0at.% Fe [Mas2]
[1997Bou, V-C]
dissolves 2 at.% Fe at 20°C
and 10 at.% Fe at 1050°C [1982Kha]
NiAl3< 856
oP16
Pnma
NiAl3
a = 661.3
b = 736.7
c = 481.1
[1996Vik]
dissolves 4 at.% Fe [1982Kha]
Ni2Al hP3
P3m1
CdI2
a = 407
b = 499
Metastable [1993Kha]
NixAl1-x martensite tP4
P4/mmm
AuCu
m**
a = 383.0
c = 320.5
a = 379.5
c = 325.6
a = 375.1
c = 330.7
a = 379.9 to 380.4
c = 322.6 to 323.3
a = 371.7 to 376.8
c = 335.3 to 339.9
a = 418
b = 271
c = 1448
= 93.4°
Metastable 0.60 < x < 0.68
[1993Kha]
at 62.5 at.% Ni [1991Kim]
at 66.0 at.% Ni [1991Kim]
at 64 at.% Ni [1997Pot]
at 65 at.% Ni [1997Pot]
[1992Mur]
Ni2Al9 mP22
P21/a
Co2Al9
a = 868.5
b = 623.2
c = 618.5
= 96.50°
Metastable [1997Poh]
FeNi tP4
P4/mmm
CuAu
a = 358.23
c = 358.22
Metastable(?) [L-B]
Fe3Ni c** a = 357.5 Metastable(?) [L-B]
D1, Fe14.5Ni13Al72.5 P10m2 aD = 713.4
cD = 818
Metastable in the ternary at
Al70Ni10-17Fe20-13 [1997Sai, 2001Qia]
Metastable in the Al-Fe binary [1986Fun]
D2,
Fe9.83Ni19.34Al70.83
P10/mmm
or P105mc
aD = 712
cD = 409
Metastable in the ternary at
Al70Ni17-20Fe13-10 [1997Sai, 2001Qia]
* 1, FeNiAl9forms between 850
and 750°C
mP22
P21/a
Co2Al9
a = 859.8
b = 627.1
c = 620.7
= 94.66°
at Al82Ni11.7Fe6.3 [1982Kha]
7.3 to 12.7 at.% Ni, 10.4 to 4.7at.% Fe at
620°C [1943Sch], confirmed by
[1999Dyb, 2000Dyb]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
348
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
Table 3: Invariant Equilibria
Table 4: Thermodynamic Data
* 2, FeNi3Al10
~850 < T < 1110
hP28
P63/mmc
Co2Al5
a = 770.3
c = 766.8
[1990Ell] at FeNiAl5Al70-72.5Fe18-24.5Ni10.5-4.5 at 1050°C
[1981Kha]
* 3, Fe5Ni24Al71
847 < T < 930
aD 378
cD 411
aD = 373.3
cD = 407.3
Decagonal phase with small solubility
range [1994Lem, 1996Gru].
Diameter of the decagonal section ~3200
pm [2001Hir]
Metastable in Al-Ni binary system
at 24-30 at.% Ni [1997Poh]
Reaction T [°C] Type Phase Composition (at.%)
Al Fe Ni
L + ' + ~1365 U1 L 23 4 73
3 Fe4Al13 + Ni2Al3 +
NiAl3
847 E1 3
Fe4Al13
Ni2Al3NiAl3
~71
~75
~61
75
~5
~15
~2
~2
~24
~10
~37
~23
L + Fe4Al13+ NiAl3 1 809 P L 87.06 2.11 10.83
L + Fe4Al13 (Al) + ( 1) 650 U2 L 98.42 0.795 0.786
L (Al) + NiAl3 + 1 638 E2 L 96.72 0.105 3.175
Reaction or
Transformation
Temperature
[°C]
Quantity per Reaction
[J, mole, K]
Comments
xFe( ) + yNi( ) + zAl(liq)
FexNiyAlz( )
800 fH = –42780 ± 280
fH = –48730 ± 220
fH = –54420 ± 240
fH = –60860 ± 230
fH = –65740 ± 270
fH = –39870 ± 230
fH = –45740 ± 050
fH = –51920 ± 140
fH = –58070 ± 110
fH = –63110 ± 060
fH = –65380 ± 100
fH = –30920 ± 240
fH = –35460 ± 310
fH = –51520 ± 290
x = 0.42, y = 0.08, z = 0.50
x = 0.34, y = 0.16, z = 0.50
x = 0.25, y = 0.25, z = 0.50
x = 0.16, y = 0.34, z = 0.50
x = 0.08, y = 0.42, z = 0.50
x = 0.46, y = 0.09, z = 0.45
x = 0.37, y = 0.18, z = 0.45
x = 0.275, y = 0.275, z = 0.45
x = 0.18, y = 0.37, z = 0.45
x = 0.09, y = 0.46, z = 0.45
x = 0.0, y = 0.55, z = 0.45
x = 0.59, y = 0.06, z = 0.35
x = 0.53, y = 0.12, z = 0.35
x = 0.145, y = 0.505, z = 0.35
Al solution calorimetry [2001Bre]
xFe( ) + yNi( ) + zAl(liq)
FexNiyAlz( )
25 fH = –58000 ± 3000
fH = –56800 ± 2300
fH = –54100 ± 2100
fH = –48400 ± 2400
x = 0.0, y = 0.50, z = 0.50
x = 0.02, y = 0.50, z = 0.48
x = 0.05, y = 0.50, z = 0.45
x = 0.10, y = 0.40, z = 0.50
Al solution calorimetry [1993Zub]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
349
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
291
286
287
288
289
290
0 6010 20 30 40 50
FeAl
NiAl
50 at.% Al
40 at.% Al
Latticeparameter(pm)
Ni, at.%
Fig. 1a: Al-Fe-Ni.
Lattice parameter of
-phase, (Fe,Ni)Al as
a function of
composition at
constant Al contents
[2002Pik]
291
286
287
288
289
290
40 5242 44 46 48 50
Latticeparameter(pm)
Al, at.%
0
1/4
1
4
�
Fig. 1b: Al-Fe-Ni.
Lattice parameter of
-phase, (Fe,Ni)Al as
a function of
composition at
constant Fe:Ni ratio
(0 - for NiAl, - for
FeAl) [2002Pik]
350
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
Fig
. 2:
Al-
Fe-
Ni.
Par
tial
rea
ctio
n s
chem
e
Al-
Fe
Fe-
Ni
Al-
Ni
Al-
Fe-
Ni
l +
αδ
γ1
513
p1
l +
βε
12
32
p3
L +
γ´
γ +
βca
.13
65
U1
l +
γγ´
13
72
p2
Lβ
+ γ
ca.1
360
e 2
lε
+ F
e 2A
l 5
11
65
e 3
l +
Fe 2
Al 5
Fe 4
Al 13
11
60
p4
l +
Fe 2
Al 5
FeA
l 2
11
56
p5
εβ
+ F
eAl 2
11
02
e 4
l (
Al)
+ F
e 4A
l 13
65
5e 5
lγ´
+ β
13
69
e 1
l +
β N
i 2A
l 3
11
38
p6
l +
Ni 2
Al 3
NiA
l 3
85
6p7
Ni 3
Al
+ β
Ni 5
Al 3
72
3p8
β +
Ni 2
Al 3
Ni 3
Al 4
70
2p9
l (
Al)
+ N
iAl 3
64
4e 6
D1
Fe 4
Al 13+
Ni 2
Al 3
+N
iAl 3
84
7E1
L+
Fe 4
Al 13+
NiA
l 3τ 1
80
9P
L +
Fe 4
Al 13
(A
l) +
τ1
65
0U2
L (
Al)
+ N
iAl 3
+ τ1
63
8E2
γ +
γ´ +
β
L+
τ 1+
Fe 4
Al 13
L+
NiA
l 3+
τ 1
L+
(Al)
+τ 1
(Al)
+N
iAl 3
+τ 1
Fe 4
Al 13+
(Al)
+τ 1
Fe 4
Al 13+
NiA
l 3+
τ 1
L+
Fe 4
Al 13+
NiA
l 3
Fe 4
Al 13+
Ni 2
Al 3
+N
iAl 3
αδ
β
351
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
γ
β
αδ
p1
p2
e1
U1
1400
1400
1400
1450
1450
1450
1500
155016001350
e2
order-disordertransformation
γ'
PFe4Al13NiAl3
(Al)
E2
e6e5
τ1
Fe 3.50Ni 0.00Al 96.50
Fe 0.00Ni 3.50Al 96.50
Al Data / Grid: at.%
Axes: at.%
τ1
e6
U2
Fe4Al13
NiAl3
(Al)
E2
e5 656
654652
650
646
648
658
720
700
680
660
710
690
675
665655
Fig. 3a: Al-Fe-Ni.
Partial liquidus
surface [1949Bra,
1943Sch]
Fig. 3b: Al-Fe-Ni.
Partial liquidus
projection of
Al-corner
352
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
L
L+β
β
γ
β+γγ´
β+γ´
γ´+γ
αδ
αδ+β+γαδ+γ
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
L
β
L+β
β+γ
γ
γ´β+γ´
γ´+γ
αδ
Fig. 5: Al-Fe-Ni.
Isothermal section at
1250°C [1949Bra].
The dotted
order-disorder line is
added
Fig. 4: Al-Fe-Ni.
Isothermal section at
1350°C [1949Bra].
Note that
order-disorder limit
between + is not
shown and must occur
inside the ternary
353
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Al–Fe–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
β
β+γ
γ
β+γ´γ´
γ´+γ
αδ+β+γ
β+γ+γ´
αδ
αδ+γ
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
αδ
γ
αδ+β
αδ+γ+β
β+γ
β
γ+γ'
γ'β+γ'
β+γ+γ'
L
τ2
FeAl2
Fe4Al13Fe2Al5
Ni2Al3
Fig. 6: Al-Fe-Ni.
Isothermal section at
1150°C [1949Bra]
below 50 at.% Al
Fig. 7: Al-Fe-Ni.
Isothermal section at
1150°C [1949Bra]
below 50 at.% Al
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Al–Fe–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
β
γ
αδβ+γαδ+β γ+γ'
γ'
β+γ'
Ni2Al3
L
Fe4Al13
Fe2Al5
FeAl2
τ2
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
β
αδ
αδ+β
β+γ
γ
γ´
γ+γ´
β+γ´
Ni2Al3
NiAl3Fe4Al13
τ2 τ3
L
Fig. 8: Al-Fe-Ni.
Isothermal section at
950°C, Al-rich
[1982Kho], Al-poor
[1951Bra, 1984Hao]
Fig. 9: Al-Fe-Ni.
Partial isothermal
section of Al-Fe-Ni at
850°C [1951Bra,
1996Gru1]
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Al–Fe–Ni
20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
αδαδ+β
β
β+γβ+γ+γ'
γ+γ'
γ'
β+γ'
L
NiAl3Fe4Al13
τ1
γ
?
10
20
10 20
80
90
Fe 30.00Ni 0.00Al 70.00
Fe 0.00Ni 30.00Al 70.00
Al Data / Grid: at.%
Axes: at.%
Fe4Al13NiAl3
τ1
(Al)+τ1
Fe4Al13+NiAl3+τ1
(Al)+NiAl3 +τ
1
(Al)+Fe 4Al13+τ1
(Al)
Fig. 10: Al-Fe-Ni.
Partial isothermal
section at 750°C:
Al-rich [1982Kho],
Al-poor [1951Bra]
Fig. 11: Al-Fe-Ni.
Partial isothermal
section at 620°C
[1943Sch]
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20
40
60
80
20 40 60 80
20
40
60
80
Fe Ni
Al Data / Grid: at.%
Axes: at.%
γ
γ+γ'
αδ
αδ+β
β+γ
Fe3Al
β
Ni2Al3
NiAl3
τ1
Fe2Al5
FeAl2 τ2
Fe4Al13
αδ+γ
90 80 70 60 50 40 30 20 100
250
500
750
1000
1250
1500
1750
2000
Fe 95.00Ni 0.00Al 5.00
Fe 0.00Ni 47.50Al 52.50Fe, at.%
Tem
pera
ture
, °C
L
β
αδ+β
L+αδ L+β
αδ
Fig. 12: Al-Fe-Ni.
Solid phases in alloys
cooled at 10 K/h
[1938Bra, 1940Bra1,
1940Bra2]
Fig. 13: Al-Fe-Ni.
Vertical section
parallel to Fe-NiAl,
Fe95Al5-Ni47.5Al52.5
[1951Bra]
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Al–Fe–Ni
90 80 70 60 50 40 30 20 100
250
500
750
1000
1250
1500
1750
2000
Fe 97.50Ni 0.00Al 2.50
Fe 0.00Ni 48.75Al 51.25Fe, at.%
Tem
pera
ture
, °C
L
αδ β
L+αδ L+β
αδ+β
magnetic transition
90 80 70 60 50 40 30 20 10500
750
1000
1250
1500
1750
Fe Fe 0.00Ni 50.00Al 50.00Fe, at.%
Tem
pera
ture
, °C
β
L L+β
L+αδ+β
γ
L+αδ
αδ
γ+αδ
αδ
αδ+β
magnetic transition
Fig. 14: Al-Fe-Ni.
Vertical section
parallel to Fe-NiAl,
Fe97.5Al2.5 -
Ni48.75Al51.25
[1984Hao]
Fig. 15: Al-Fe-Ni.
Vertical section
Fe-NiAl [1951Bra,
1951Iva]
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Al–Fe–Ni
20 100
250
500
750
1000
1250
1500
Fe 25.00Ni 75.00Al 0.00
Fe 0.00Ni 75.00Al 25.00Fe, at.%
Tem
pera
ture
, °C
γ'(ordered)
γ+γ'
γ(disordered)
L1430°C
Fig. 16: Al-Fe-Ni.
Vertical section
Ni3Al-FeNi3[1987Mas]. The tiny
L+ '+ around
1369°C close to
Ni3Al is not shown
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Al–Fe–Si
Aluminium – Iron – Silicon
Gautam Ghosh
Literature Data
The system contains many technologically important alloys, such as foil and sheet products for food
packaging, capacitors, lithographic printing sheets, magnetic alloys for transformer. Furthermore, iron and
silicon, originating from bauxite ore and anode material, are present in nearly all industrial Al-alloys.
Metallurgical grade silicon also contains, among others, aluminum and iron as impurities. Due to these
reasons, there are numerous experimental studies on the phase equilibria of the ternary system, the results
of which have been reviewed from time to time [1934Fue, 1937Ser, 1943Mon, 1950Gme, 1952Han,
1959Phi, 1968Dri, 1981Riv, 1981Wat, 1985Riv, 1987Pri, 1988Ray, 1992Gho, 1992Zak, 1994Rag,
2002Rag]. The system is characterized by a large number of ternary phases, both stable and metastable, and
at least nineteen ternary invariant reactions during solidification which impart difficulties in establishing the
phase equilibria of the system. The difficulties are further augmented by the effects of metastability,
impurity elements, incomplete reactions, undercooling, and many solid-state reactions which are not well
understood.
Earlier works by [1923Dix, 1923Han, 1923Wet, 1924Fus, 1934Roe, 1941Pan] were mostly on the
observation of microstructures of dilute Al-alloys. [1951Ran] determined the phase boundaries of the
Al-corner at 475°C by diffusional anneal technique. Due to extensive results [1927Gwy, 1933Nis, 1936Jae,
1937Ura, 1943Phi, 1951Hol, 1951Now, 1967Mun, 1987Gri1, 1987Ste], the phase equilibria of the
Al-corner are well established.
The first comprehensive study of phase equilibria of the entire system was performed by [1940Tak]. They
used electrolytic iron, pure aluminium and metallic silicon (unspecified purity). Over 150 ternary alloys
were prepared using master alloys of selected compositions in an arc furnace, under hydrogen atmosphere
with NaCl as flux on the molten surface of the alloys, followed by cooling at a rate of 2 to 3 K per 5 to 10
sec. In some cases, in order to confirm and identify solid-state reactions, the cooling curves were
supplemented by heating runs. [1940Tak] employed metallography, thermal, X-ray, magnetic and
dilatometric analyses to establish the phase equilibria. They reported six ternary phases, and all form by
peritectic reactions. They also presented an extensive set of several vertical sections from 500°C up to the
liquidus temperature. Based on these results, [1981Riv] constructed a probable isothermal section at 600°C.
The Fe-corner was extensively studied by [1968Lih] up to 50 at.% Al and 35 at.% Si by DTA,
thermo-magnetometry, microhardness and X-ray diffraction. The phase equilibria involving ordered and
disordered phases in Fe-rich alloys were determined by [1982Miy] and [1986Miy] in the temperature range
of 450 to 700°C using transmission electron microscopy.
Recent investigations of the Al-corner, for alloys up to 14 at.% Si and 35 at.% Fe, are due to [1987Gri1] and
[1987Ste]. They used thermal analysis, X-ray diffraction and electron probe microanalysis to establish the
liquidus surface, and isothermal sections at 570 and 600°C. These results were slightly modified by
[1987Pri] to make them consistent with the thermodynamic rules of phase diagram construction.
[1981Zar] reported ten ternary phases, and an isothermal section at 600°C. [2001Kre] determined a partial
isothermal section at 550°C. About 100 alloys, containing up to 50 at.% Fe and 50 at.% Si, were used. The
phase equilibria were established by extensive use of X-ray diffraction, EDS analysis of the phases, and
optical metallography.
Thermodynamic datasets of the ternary system were assessed by [1994Ang, 1998Kol, 1999Liu].
Binary Systems
The Al-Si binary phase diagram is accepted from [2003Luk]; the Al-Fe binary phase diagram is accepted
from [2003Pis]; and the Fe-Si binary phase diagram is accepted from [1982Kub]. In the Al-Fe system, it
has been reported that Fe4Al13 melts congruently at 1152°C [1986Len] which confirms earlier finding by
[1960Lee].
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Al–Fe–Si
Solid Phases
As far as the binary intermediate phases are concerned, only those appearing in the equilibrium phase
diagrams are considered here. For example, direct chill-cast of commercially pure Al-alloys are reported to
contain Al-Fe intermediate phases that are not present in the equilibrium phase diagram [1977Sim,
1982Wes, 1985Don2, 1986Liu1, 1986Liu2, 1987Cha, 1987Skj1, 1987Skj2, 1987Ste, 1988Cha, 1988Liu2].
Therefore, they are not considered in constructing the ternary phase diagrams.
At 550°C, the solubility of Fe and Si in (Al) is less than 1 at.% [2001Kre], and that of Fe and Al in (Si) is
extremely small.
The Fe4Al13 phase is reported to dissolve 0.8 mass% Si [1955Arm], 0.2 mass% Si [1967Sun], 1.0 mass%
Si [1984Don], 2.9 mass% Si [1987Skj1], up to 6.0 mass% Si at 600°C [1987Ste], and 4 at.% Si at 550°C
[2001Kre]. This is associated with an increase in the a-lattice parameter and a decrease in the b-lattice
parameter; whereas no significant changes in the c-lattice parameter and were detected [1987Ste]. The
composition dependence of a- and b-lattice parameters in Fe4Al13 is expressed by [1987Ste] as
a (in pm) = 1505.0+1.14 WFe-0.41 WSi
b (in pm) = 862.8-1.41 WFe-1.3 WSi
where WFe and WSi are the mass% of Fe and Si, respectively. A detailed crystallographic analysis of the
Fe4Al13 phase, by means of convergent beam electron diffraction and high resolution electron microscopy,
has been performed by [1987Skj3]. Lattice images revealed that the Fe4Al13 crystals are divided into tiny
domains (few thousand pm) which are separated by lattice displacements such as stacking faults [1987Skj2,
1987Skj3].
At 550°C, FeAl2 dissolves about 1 at.% Si, and Fe2Al5 dissolves about 2 at.% Si [2001Kre].
Initial studies showed that the FeSi2(h) phase dissolves up to about 0.5 mass% Al [1961Sab, 1965Sab,
1965Skr, 1968Sab1, 1968Sab2] which is accompanied by a small increase in both the a- and c-lattice
parameters. However, later it was found that FeSi2 dissolves up to 10 at.% Al [1994Ang, 1995Gue3]. The
FeSi phase also dissolves substantial amount of Al [1996Szy, 1998Dit], and at 550°C it is about 10 at.%
with Al substituting Si [2001Kre]. The ambient temperature lattice parameters of FeSi, FeSi2(h) and
FeSi2(r) as functions of Al-content were reported by [1996Szy]:
For FeSi: a (in pm) = 448.1+5.4xAl
For FeSi2(h): a (in pm) = 269.1+17.9xAl
c (in pm) = 515.7+30.2xAl
For FeSi2(r): a (in pm) = 986.6+7.3xAl
b (in pm) = 778.7+10.3xAl
c (in pm) = 782.1+27.6xAl
where xAl is the atomic fraction of Al.
The Fe3Al and Fe3Si phases form a continuous solid solution. The lattice parameter of the alloys along
Fe3Al-Fe3Si and Fe73Al27-Fe73Si27 sections and also for the commercial SENDUST and ALSIFER 32
alloys were determined systematically and accurately by [1979Cow]. The composition dependence of the
lattice parameter can be expressed as:
Along the Fe3Al-Fe3Si section
a (in pm) = 565.54+12.846 W+1.896 W2-0.7245 W3 = 565.54+12.776 C+1.9522 C2-0.7094 C3
where W = mass fraction of Fe3Al and C = mole fraction of Fe3Al.
Along the Fe73Al27-Fe73Si27 section
a (in pm) = 564.462+11.964 W +5.3929 W2-2.5 W3 = 564.462+11.915 C +5.3183 C2-2.321 C3
where W = mass fraction of Fe73Al27 and C = mole fraction of Fe73Al27.
[1979Cow] attributed a small, but consistent deviations from the linear dependence on composition, along
both sections, to the incomplete ordering as Al is replaced by Si. [1979Bur] also reported limited lattice
parameter data along Fe3Al-Fe3Si section which are in reasonable agreement with those of [1979Cow], but
[1979Bur] assumed a linear dependence of lattice parameter on composition (see also [1977Nic1],
[1977Nic2]). [1968Lih] reported lattice parameters of ternary alloys up to 30 at.% Si and 47 at.% Al at 20,
500, 600 and 900°C. [1946Sel] also measured the lattice parameter of ternary alloys up to 18 mass% Si and
13 mass% Al. The lattice parameter of Fe3(Al,Si) containing about 10 mass% Al and 5 mass% Si is reported
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Al–Fe–Si
to be 570 ± 3 pm [1978Xu]. The lattice parameter of an Fe-5.5 mass% Al-9.7 mass% Si alloy is reported to
be 568.4 pm after water quenching and 568.54 pm after annealing for 24 h at 600°C.
The complexity of phase equilibria of the Al-Fe-Si system is primarily due to the occurrence of many
ternary phases, and the associated metallurgical reactions during solidification and during heat treatments.
While some of these ternary phases are stable, many are metastable. In recent years, detailed
crystallographic characterization of the stable phases have been performed; however, the current
crystallographic data of many metastable ternary phases are far from being complete. The difficulties of
complete crystallographic characterization of these phases are due to (i) the occurrence of several phases
over a relatively narrow composition range in the Al-corner, (ii) the complex crystal structure along with
the presence of high density of planar defects in ternary phases, (iii) the order-disorder reactions in the
Fe-corner, (iv) many invariant reactions which under normal experimental conditions (both during
solidification and during heat treatments) do not undergo completion, and (v) the effect of heterogeneous
nucleation on the phase selection during solidification. In the past seven decades a large number of ternary
phases in the Al-Fe-Si system have been reported. A chronological survey of these ternary phases is given
in Table 1, where it may be noted that some of the results are still controversial.
Nine ternary phases are accepted for the construction of phase diagrams. These are labeled as 1 to 10.
Among these, [1940Tak] reported six ternary phases, four of which ( 2, 4, 5, and 6) could be identified
without much difficulty. Their investigation was mainly based on thermal analysis and microstructural
examination, supplemented by limited X-ray diffraction. Single crystal structure determinations have been
carried out for 1 [1996Yan], 3, [1989Ger2], 4, [1969Pan, 1995Gue1], 6, [1994Rom], 7, [1995Gue2]
and 10, [1989Ger1]. The details of the crystal structures and lattice parameters of the solid phases are listed
in Table 2. The composition ranges of the equilibrium ternary phases reported by different authors are
plotted in Fig. 1. It may be noted that while most of the composition ranges are isolated from each other,
there are overlapping composition ranges among 2, 3 and 10 phases.
The 1-phase has monoclinic structure, and its composition has been corrected from Fe3Al3Si2 to Fe3Al2Si3[1996Yan]. [2001Kre] established that the previously reported 1 and 9 [1992Gho] are actually the same
phase. The 1-phase corresponds to the K1-phase of [1940Tak] and the E-phase of [1981Zar], and 9
corresponds to the D-phase of [1981Zar]. [2001Kre] also confirmed triclinic structure [1996Yan] of 1/ 9.
At 550°C, 1/ 9 coexists with Fe2Al5, Fe4Al13, 2, FeSi, 2, 3, 7, 10, and possibly 8 [2001Kre].
[1981Zar] represented the homogeneity range of 2-phase (the K-phase) as Fe22Al52-63Si15-26, which most
likely corresponds to the K3-phase of [1940Tak]. [2001Kre] represented its homogeneity range as
Fe(Al1-xSix)7, with 0.2 x 0.33. As seen in Table 2, three crystal structures of 2 have been reported.
[2001Kre] indexed the X-ray diffraction pattern of 2 using the monoclinic unit cell proposed by
[1967Mun]. At 550°C, 2 coexists with Fe4Al13, 1/ 9, 3, 4, 5, 6 and 7 [2001Kre].
The 3-phase corresponds to the K2-phase of [1940Tak] and the G-phase of [1981Zar], and it has negligible
homogeneity range [2001Kre]. The composition of 3 is represented as FeAl2Si [1981Zar], but EDS
analysis of [2001Kre] gave Fe25Al56±1Si19±1, or Fe(Al1-xSix)3, with x = 0.25. On the other hand,
[1989Ger2] reported its composition as Fe(Al1-xSix)3, with x=0.33 based on XRD analysis. [2001Kre]
suggested that it is impossible to detect such a small difference in Al/Si-ratio based on XRD analysis. Its
structure has been confirmed to be orthorhombic [1974Mur, 1981Zar, 1989Ger2, 2001Kre]; however, there
is a scatter in the lattice parameter values. At 550°C, 3 coexists with Fe4Al13, 1/ 9, 2 and 10 [2001Kre].
The 4-phase corresponds to the K4-phase of [1940Tak] and the A-phase of [1981Zar]. It is single phase at
the composition Fe(Al0.6Si0.4)5 [2001Kre]. The tetragonal structure of the 4 phase was first reported by
[1936Jae], and subsequently confirmed by several others [1950Phr, 1969Pan, 1974Mur, 2001Kre]. At
550°C, 4 coexists with (Si), 2, 6 and 7 [2001Kre].
The 5-phase corresponds to the K5-phase of [1940Tak] and the M-phase of [1981Zar]. Often, it is also
designated as -AlFeSi. Its stoichiometry may be described as Fe46(Al0.875Si0.125)200-x, with x = 7
[2001Kre]. The hexagonal structure of the 5 phase was first reported by [1953Rob], and subsequently
confirmed by [1967Mun, 1975Bar, 1977Cor, 1977Hoi, 1987Gri2, 1997Vyb, 2001Kre]. Earlier studies
[1950Phr, 1952Arm, 1955Arm, 1967Coo] reported a cubic structure of 5, but it was attributed to traces
( 0.3 mass%) of dissolved transition metals such as Mn or Cu that might have stabilized the cubic symmetry
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Al–Fe–Si
at the expense of the hexagonal structure [1967Sun, 1967Mun]. At 550°C, 5 coexists with (Al), Fe4Al13,
2, and 6 [2001Kre].
The 6-phase corresponds to the K6-phase of [1940Tak] and the L-phase of [1981Zar]. Often, it is also
designated as -AlFeSi. Its stoichiometry is FeAl4.5Si. Despite numerous studies, the crystal structure of 6
is still controversial. While the X-ray diffraction studies reported its structure to be monoclinic [1950Phr,
1954Spi, 1955Obi, 1975Bar, 1994Mur, 1994Rom, 1996Mur, 1997Vyb, 2001Kre], convergent beam
electron diffraction studies found that 6 is orthorhombic [1993Car, 2000Zhe]. In fact, [2000Zhe] did not
find any monoclinic phase in their electron microscopic investigation. They concluded that the
misinterpretation of X-ray diffraction data indexed by a monoclinic cell may be due to intergrowth of
different phases, and a high density of planar defects. At 550°C, 6 coexists with (Al), (Si), 2, 4 and 5
[2001Kre].
[1951Pra1] correlated the formation of 5 and 6 with the electron-to-atom ratio. [1979Mor] analyzed the
composition of the intermetallic phases by electron microprobe technique and grouped them into two
categories based on the size and Fe/Si ratios which can be matched with the 5 and 6 phases. However,
[1979Mor] reported 'indeterminate' particles having intermediate size and Fe/Si ratios between 2.75 and
2.25. [1977Igl] postulated that the 5 phase is metastable and can replace the 6 phase at cooling rates
greater than 200 K/min. [1985Suz] and [1987Nag] reported Mössbauer spectra of the 5 and 6 phases, the
former gave a relatively complex spectrum, and the latter gave a simpler one.
The 7-phase corresponds to the B-phase of [1981Zar], and it has negligible homogeneity range [2001Kre].
Based on the EDS data, the stoichiometry of 7 is Fe25Al45Si30, or Fe(Al1-xSix)3, with x = 0.4 [2001Kre].
On the other hand, based on XRD data [1995Gue2] proposed the stoichiometry of 7 as Fe2Al3Si3, or
Fe(Al1-xSix)3, with x = 0.5, which reflects a discrepancy in Al/Si-ratio. Nevertheless, the monoclinic
structure of 7 reported by [1995Gue2] was also confirmed by [2001Kre]. The observation of Fe5Al8Si7[1994Ang] most likely corresponds to 7 [2001Kre], based on the assumption of a composition shift similar
to 1, even though [1994Ang] did not report its crystal structure. At 550°C, 7 coexists with (Si), 1/ 9, 2,
4 and 8 [2001Kre].
The 8-phase corresponds to the C-phase of [1981Zar]. Its stoichiometry may range from Fe(Al1-xSix)2,
with x = 0.5 [1981Zar] to Fe(Al1-xSix)2, with x = 0.67 [1996Yan]. It has orthorhombic structure [1996Yan,
2001Kre]. The observation of Fe5Al5Si6 [1994Ang] most likely corresponds to 8 [2001Kre], based on the
assumption of a composition shift similar to 1, even though [1994Ang] did not report its crystal structure.
The 10-phase corresponds to the F-phase of [1981Zar] with stoichiometry Fe25Al60Si15. [1981Zar]
reported that its structure in as-cast alloy is different from annealed condition, which was later confirmed
by [1987Ste]. The hexagonal structure of 10 is prototypical of either Co2Al5 or Mn3Al10. [1989Ger1]
reported Mn3Al10-type structure of 10 annealed at 600°C, while [2001Kre] reported the same structure in
as-cast alloy. At 550°C, 10 coexists with Fe4Al13, 1/ 9 and 3 [2001Kre].
Recent investigations of precipitates in commercial Al alloys, by means of TEM/STEM, EDAX, and high
resolution electron microscopy, have revealed a wide variety of precipitate crystal structures, lattice
parameters and compositions [1982Wes, 1984Don, 1985Don1, 1985Don2, 1985Gri, 1985Liu, 1986Liu1,
1986Liu2, 1987Cha, 1987Czi, 1987Skj1, 1987Ste, 1987Tur, 1988Ben2, 1988Cha] which can not be
grouped together (for details see Table 1). In this assessment, these phases are considered to be metastable.
In the absence of detailed crystallographic data, a classification of these metastable phases based on the
crystal system is proposed in Table 3. [1987Nag] and [1987Tur] found that the compositions of the
intermediate phases and the phase transformations that take place during high temperature annealing depend
on the Fe/Si ratio of the alloy. [1986Liu2] reported three different kinds of precipitates, in dilute Al-Fe-Si
alloys, formation of which is reported to be a function of Fe/Si ratio, alloy purity, solidification rate and heat
treatment. These factors probably explain the occurrence of so many ternary phases as reported by different
authors. The principles governing the substitution of Al by Si in the ternary intermediate phases have been
described by [1989Tib].
The composition ranges of the metastable phases are plotted in Fig. 2. Compared to the equilibrium ternary
phases, the scenario here is much more complex. Virtually all metastable phases have overlapping
composition range between 25 to 35 mass% Fe and 0 to 11 mass% Si. Besides crystalline metastable phases,
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Al–Fe–Si
the formation of amorphous phases in a number of Al-Fe-Si alloys has also been reported [1986Dun,
1987Ben, 1988Ben1].
Order-Disorder Phase Transitions
There have been extensive studies of order-disorder transitions of Fe-rich ternary alloys, both
experimentally and theoretically. Mutual solid solubility between Fe3Al and Fe3Si is well-established. The
solid solubility and the magnetic behavior of Fe3(Al, Si) was correlated with electron-atom ratio [1977Nic1]
and [1977Nic2]. The existence of the ordered phases 1 (Fe3Al and Fe3Si which have D03 or BiF3 type
order) and 2 (FeAl and FeSi which have B2 or CsCl type order) along the Fe3Al-Fe3Si section was studied
[1969Pol, 1973Kat] by means of high temperature X-ray diffraction and recording the disappearance of D03
superlattice {111} and {200} reflections as a function of temperature and composition. [1946Sel] measured
the lattice parameter of alloys up to 13 mass% Al and 18 mass% Si and observed an inflection point in the
lattice parameter vs composition curve which was attributed to the ordering reaction and the formation of
Fe3(Al,Si) having D03 superstructure. This was further supported by specific heat measurements as a
function of Si/Al ratio by [1951Sat], who found the reaction is accompanied by a small change in Gibbs
energy suggestive of a second-order reaction. However, with the addition of Si in Fe3Al the ordering
energies increase monotonically [1973Kat]. The order-disorder transitions along Fe3Al-Fe3Si was further
studied by transmission electron microscopy (TEM) [1982Cha] and by magnetic method [1986Tak].
However, there is still some controversy regarding the sequence of ordering transitions along this section.
Previous studies by [1969Pol] and [1973Kat] indicate that the sequence of ordering reaction (on cooling) is
always ( Fe) 2 1 along Fe3Al-Fe3Si section. However, recent studies by [1982Cha] and [1986Tak]
indicate that substitution of more than 50% of the Al atoms by Si atoms ( Fe) transforms directly into D03
structure. [1984Mat] studied two kinds of processes of ordering with phase separation, 2 ( Fe+ 1) and
1 ( Fe+ 1), in an Fe-6Fe-9Si (at.%) alloy using X-ray diffraction and transmission electron microscopy.
Single phase 1 and 2 structures were retained by quenching the alloy from 700 and 900°C, respectively.
The results of [1969Pol] and [1973Kat] indicate that addition of Si in Fe3Al increases the 1 2 transition
temperature while that of 2 ( Fe) increases with up to about 12.5 at.% Si beyond which it levels off. The
initial increase in ordering temperatures is consistent with the observation of [1977Nic1], and also
confirmed by [1987For]. A recent study of magnetic measurements [1986Tak] indicate that the ( Fe) 2
and 2 1 transition temperatures vary non-monotonically with increasing Si-content as shown in Fig. 3.
Minor adjustments have been made in Fig. 3 to comply with the accepted Al-Fe binary phase diagram, and
also by taking into account the results of [1982Cha] that the ( Fe) 1 ordering temperature of
Fe3(Al0.392Si0.608) is greater than 1050°C. Even though the effect of Si on the ordering induced phase
separation around Fe3Al has not been investigated in detail, it is important to note that [1996Mor] observed
( Fe)+ 1 microstructure in an Fe-17Al-1Si(at.%) alloy in the temperature range of 400 to 600°C. It is
expected that the topology of the phase boundaries involving ordered ( 1, 2) and disordered phases ( Fe)
near Fe3Al will follow the general features of phase diagrams associated with multicritical points [1982All].
Due to these reasons, several amendments are proposed in Fig. 3, shown by dotted lines, in the vicinity of
Fe3Al.
Even though, in general the nucleation and growth of 1 domain in 2 domain is easier than in ( Fe) matrix,
the direct ( Fe) 1 transformation in certain composition range has been attributed to the lowering of
atomic potential energy when Al atoms are substituted by Si atoms. This causes the formation of different
types of anti-phase boundaries and the corresponding changes in dislocation configuration leads to double
dissociation of superlattice dislocations [1982Cha]. Depending on the composition of the alloy, nucleation
of the ordered phases can also take place directly from the melt. TEM and Mössbauer spectroscopy study
[1983Gle] of an Fe-5.4Al-9.6Si(mass%) alloy revealed that the B2 type of ordering takes place directly
from the melt which subsequently undergoes D03 ordering. Also, [1969Pol] observed that the D03
superlattice reflections persist up to the melting point in an alloy of Fe3Al+12 at.% Si. A similar conclusion
was also made by [1954Gar] who investigated the order-disorder transition, after quenching from different
temperatures, in an Fe-9.7Si-5.5Al(mass%) alloy. By rapid quenching an Fe-5.4 mass% Al-9.6 mass% Si
alloy, [1983Gle] observed that excess vacancies are introduced which occupy ordered sublattice positions,
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giving rise to a new crystallographic superstructure of the D03-type. Such type of vacancy-induced long
range ordering, from one crystal structure to another, has also been observed at other composition
[1988Liu1].
Mössbauer spectroscopy study of Fe73Al11Si16 (ALSIFER27) and Fe68Al22Si10 (ALSIFER32), by
[1977Suw], revealed that excess diamagnetic atoms preferentially occupy particular D03 lattice sites which
is not observed from X-ray diffraction. They argued that powder methods used in X-ray diffraction may not
represent the ordering reactions in the bulk materials. Also, Mössbauer study of Fe3Al1-xSix, for 0 x 1,
indicates that 'order-annealing' treatment is accompanied by a separation of Fe3Al and Fe3Si types of local
surroundings [1983Sch]. However, this has only weak influence on the physical properties and the
predominant factor being the composition of the sample. [1987Dob] determined the atom locations in
Fe3-xAlxSi alloys with x=0.1, 0.2 and 0.3 having D03 structure, where Al atoms are confirmed to occupy the
Fe-sites.
[1996Mor] studied the kinetics of ordering and phase separation in an Fe-17 at.% Al-1 at.% Si alloy in the
temperature range of 400 to 600°C, where they monitored the evolution of + 1 microstructure. They found
that partial substitution of Al by Si improves microstructural stability against coarsening, most probably due
to decrease diffusivity and a reduction in misfit strain.
A theoretical study of ordering process in Fe0.5(Al1-xSix)0.5 [1999Mek] predicts an increase in
order-disorder temperature. Furthermore, they predicted that Si preferentially substitute Fe in
Fe0.5(Al1-xSix)0.5.
Pseudobinary Systems
[1931Fus] and [1934Fue] proposed a pseudobinary section Si-Fe4Al13 with a peritectic reaction
L + Fe4Al13 Fe2Al6Si3 at about 920°C and a eutectic reaction between (Si) and Fe2Al6Si3 at 850°C and
32 mass% Si. However, later works failed to confirm the presence of such a pseudobinary section and
consequently it is disregarded.
Invariant Equilibria
At least nineteen invariant equilibria, in the solidification range of Al-Fe-Si alloys, have been reported
which are listed in Table 4. The assessed compositions of the liquid phase, after [1927Gwy, 1936Jae,
1937Ura, 1940Tak, 1951Now, 1960Spe], for the ternary invariant reactions are listed in Table 4. [1940Tak]
proposed nineteen ternary invariant reactions for the solidification of the Al-Fe-Si alloys. However, they
reported that some of these reactions take place in a very narrow range of temperature, thus, difficult to
resolve by thermal analysis. For example, [1940Tak] proposed the following two reactions:
L + 2 + FeAl2 at 1120°C
L + FeAl2 2 + Fe2Al5 at 1115°C.
These two reactions could not be distinguished clearly and a temperature interval of 5°C was assumed
[1940Tak]. Also, they reported that it was difficult to distinguish FeAl2 from Fe2Al5 by etching. Instead of
the above two reactions, the following invariant reaction is assumed in the present evaluation:
L + 2 + Fe2Al5 at 1120°C.
Ignoring the solubility of Si in FeAl2 and Fe2Al5, thermodynamic calculations [1998Kol, 1999Liu] give
following three reactions:
+ Fe2Al5 FeAl2, L (degenerate binary reaction)
L + 2 + FeAl2 at 1125°C [1998Kol], at 1127°C [1999Liu]
L + FeAl2 2 + Fe2Al5 at 1062°C [1998Kol], at 1073°C [1999Liu].
Among these, the first reaction was not explicitly mentioned by the authors. Since the solubility of Si in
FeAl2 and Fe2Al5 phases are not considered in thermodynamic modelling, the temperature of the
three-phase equilibrium + Fe2Al5 + FeAl2 in the ternary is connected with the Si-content of by a
"generalized Raoult's law". In the Al-Fe system, the eutectic temperature of L + Fe2Al5 is very closely
above the temperature of + Fe2Al5 FeAl2. For the three-phase equilibria going down from these
temperatures into the ternary a "generalized Raoult's law" is valid, due to which the two three-phase
equilibria meet and form the above mentioned four-phase equilibrium. This meeting happens very near to
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the binary Al-Fe system. The amount of liquid participating in the four-phase equilibrium roughly
corresponds to the ratio of Si-solubility in and liquid phases.
[1981Riv] did not consider the participation of the L 2 + Fe2Si binary invariant reaction in the
solidification process of the ternary alloys. Also, they did not consider Fe2Si to be a primary crystallization
product in the ternary regime. To alleviate these drawbacks, an invariant reaction with highest temperature
must be assumed near the Fe-Si side. It is labelled as U1, and assumed to take place around 1150°C
[1992Gho]:
L + Fe2Si 2 + FeSi
In fact, the likelihood of U1 is also predicted in recent thermodynamic assessments of [1998Kol, 1999Liu].
Thermodynamic modeling also confirmed the existence of following invariant reactions: P1, U3, U4, U5, P2,
U7, U8, P5, U10, U11, U12 and E1.
It should be noted that Fig. 4 represents only a partial reaction scheme. It considers participation of six
ternary phases, 1, 2, 4, 5, 6 and 7, during solidification. The composition domain of liquid alloy where
3 is the primary crystallization product should be close to that of 2, but the available thermal analysis data
[1940Tak] are insufficient to differentiate them. The reaction scheme does not account for the experimental
observation of several three-phase fields, such as 2+ 5+ 6 at 600°C [1987Ste] and at 550°C [2001Kre],
2+ 4+ 6 at 550°C [2001Kre], 2+ 4+ 7 at 550°C [2001Kre]. These may originate from the invariant
reactions L + 2 5 + 6 around 650°C [1952Arm, 1967Mun], L + 2 + 4 6 around 700°C [1927Gwy,
1940Tak], and L + 7 3 + 4, respectively. However, to account for all experimentally observed
three-phase fields at 600 [1992Gho] and 550°C [2001Kre], including those involving 8 and 10, it is
necessary to introduce too many speculative invariant reactions. Therefore, no attempt was made to propose
a complete reaction scheme. Nevertheless, further careful experiments are needed to establish the invariant
reactions during solidification and also in the solid state.
Liquidus Surface
Figure 5 shows the liquidus surface of the Al-corner calculated by the dataset of [1999Liu], which
reproduces well those of [1927Gwy, 1943Phi, 1946Phi1]. The general form of the liquidus surface has been
confirmed by other investigators [1933Nis, 1936Jae, 1937Ura, 1951Now, 1967Mun, 1987Gri1, 1988Zak].
Nevertheless, some disagreement exists over the temperature contours. [1967Mun] reported that the cooling
rate is an important factor. On the other hand, [1967Sun] using a variety of cooling rates confirmed the data
of [1927Gwy] and [1943Phi] and proposed that the nucleation is the decisive factor. [1977Igl] claimed a
marked sensitivity of cooling rate not only on the temperature arrest, but also on the final product. In this
assessment, the data of [1927Gwy] and [1943Phi] are considered to be representative of normal equilibrium
condition and more complete compared to those reported by others [1933Nis, 1937Ura, 1951Now].
Figure 6 shows the liquidus surface of the whole Al-Fe-Si system [1940Tak], depicting the melting grooves
separating 15 different areas of primary crystallization. Since the invariant reaction U1 has not been
experimentally confirmed, part of the univariant lines formed by the 2, FeSi and Fe2Si crystallization
surfaces have been shown dashed. Nevertheless, the U1 reaction complies with all the binary invariant
reactions and experimental ternary phase diagrams. The calculated liquidus surfaces [1998Kol, 1999Liu]
look similar, except in the Al-corner where they differ by several at.% in composition and up to 30°C in
temperature compared to that of [1940Tak].
Approximate isotherms at 50°C interval are superimposed in Fig. 6. In both Al-Fe and Fe-Si binary systems,
depending on the alloy composition, either ( Fe) or 2 may be the primary crystallization product. In the
ternary system, as an approximation, the composition domains of ( Fe) and 2 as primary crystallization
products are delineated by the linear extrapolation between the composition limits of two binary edges. This
is shown by a dashed line in Fig. 6. In the Fe-Si system, 1 is the primary crystallization product during
solidification of alloys containing 27.5 to 32 at.% Si. However, the extension of this composition range into
the ternary system is not known. In the a comprehensive study of liquidus surface of the Al-corner, up to 70
mass% Fe, by [1937Ura] agrees reasonably well with the results of [1940Tak]. The liquidus temperatures
of [1936Jae] are few tens of degrees higher than [1940Tak], and could be due to inadequate experimental
arrangements.
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Isothermal Sections
Figure 7 shows the isothermal section at 1000°C [1981Riv], drawn from the polythermal sections of
[1940Tak]. At 1000°C, only one ternary phase, 1, is stable which is also expected from the reaction scheme
in Fig. 4. Also, in Fig. 7, the boundary between ( Fe) and 2 is shown by a dashed line which is a linear
interpolation between the composition limits of two binary edges. The extension of the binary intermediate
phases into the ternary regime is given as approximate only. Figure 8 shows the isothermal section of the
Al-corner at 640°C [1959Phi]. [1987Ste] reported the phase equilibria in a set of commercial Al-based alloy
after heat treating the as-cast samples for one month between 570 and 600°C. The heat treated state was
referred to as “quasi-equilibrium” condition [1987Ste]. The phase equilibria of the Al-corner at 600°C is
shown in Fig. 9, after [1987Pri] who amended the isothermal section reported by [1987Gri1] and [1987Ste].
It is to be noted that the (Al)+ 6 and (Al)+ 6+(Si) phase fields were derived from the measurements on
samples annealed at 570°C. So the existence of these phase fields is consistent with the reaction scheme in
Fig. 4, giving the temperature for E1 as 573°C. Also, [1987Ste] reported that three ternary compounds
-FeAlSi ( 5), -FeAlSi ( 6) and -FeAlSi ( 2), the details of which are given in Table 2, crystallize from
the liquid. This is also consistent with the proposed reaction scheme in Fig. 4. During heat treatment of the
as-cast samples, the Fe4Al13, 5 and (Si) phases react to form 6 phase, but this reaction does not go to
completion [1987Ste].
Figure 10 shows the assessed isothermal section at 600°C. The Fe-corner involving the ordered phases is
taken from [1986Miy], but at certain composition ranges the ordered phase regions are still doubtful, and
they are shown as dashed. The isothermal section at 600°C reported by [1981Zar] has undergone several
amendments. Previously reported [1992Gho] 1 and 9 phases are treated as one phase [2001Kre]. The
composition of 8 is accepted from [1996Yan]. Figure 11 shows the partial isothermal section at 550°C
[2001Kre]. Even though temperature difference is only 50°C, there are important differences between Figs.
10 and 11. For example, Fig. 10 shows the presence of (Al)+(Si)+ 4 phase field which is not accounted for
by the reaction scheme, while Fig. 11 shows the presence of (Al)+(Si)+ 6 phase field which is consistent
with the reaction scheme in Fig. 4. Figure 10 shows the presence of 10+Fe2Al5+Fe4Al13 phase field, while
Fig. 11 shows the presence of 1/ 9+Fe2Al5+Fe4Al13 phase field. In Fig. 11, several phase boundaries
involving 8 are uncertain. [2001Kre] reported that the tie-triangles involving 8 will depend on its
composition, which was not determined. As a results, some of the phase boundaries in 8 are shown dotted.
Figure 12 shows the partial isothermal section at 500°C proposed by [1984Don] in which the phase
boundaries have shifted to the right, compared to [1943Phi, 1946Phi1, 1946Phi2], in order to account for
the observation of various phases as well as the amount of Si in solid solution in the (Al) matrix in
industrially pure Al.
Figures 13, 14, 15, 16 show the isothermal sections of the Fe-corner at 700, 650, 550 and 450°C,
respectively, after [1986Miy] who studied ternary alloys, containing up to 40 at.% solute atoms (Al+Si), by
means of transmission electron microscopy. These figures depict the states of different kinds of order in
ternary Fe-rich alloys as a function of composition and temperature. [1986Miy] reported two types of phase
separation 1(D03)+ 2(B2) and ( Fe)+ 1(D03) in the ternary alloys connecting Fe-10 to 14 at.% Si with
Fe-20 to 25 at.% Al and also near Fe-30 at.% Si alloy. The morphology of the <100> modulated structure
in Fe-Si and Al-Fe-Si alloys differs from that of the Al-Fe system [1986Miy]. X-ray diffraction data and
TEM observations of [1971Gle] concerning various order-disorder reaction in the ternary alloys
qualitatively agree with those of [1986Miy]
Temperature – Composition Sections
Figures 17, 18 and 19 show polythermal sections of the ternary system at 0.7 mass% Fe [1949Cru, 1959Phi],
at 4.0 mass% Fe [1959Phi] and at 8.0 mass% Si [1959Phi], respectively. There are no published data for the
solidus projection of the entire system, even though a number of polythermal projections are available
[1927Gwy, 1932Nis, 1933Nis, 1940Tak, 1946Phi1]. The solidus projection of the Fe-corner was reported
[1968Lih], but their results differ substantially along the Al-Fe binary edge, so they are not accepted here.
Since Al-rich solid solutions can dissolve only about 0.052 mass% Fe, the solidus of the Al-corner
[1961Phi] of the Al-Fe-Si system is shown in Fig. 20 on an enlarged scale.
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Thermodynamics
Thermodynamic properties of ternary alloys have been investigated a number of times by measuring the
heat of formation of solid alloys [1937Koe, 1937Oel], activity measurements in liquid alloys [1969Bed,
1970Mit, 1973Nag, 1973Per, 1980Sud, 1984Ber, 1985Cao, 1989Bon], and the standard heat of formation
of ternary intermetallics [1997Vyb, 2000Li1, 2000Li2]. The energetics of chemical ordering in the ternary
system has been described by [1991Fuk] and [1994Koz]. Besides, thermodynamic modeling of the ternary
system has also been carried out by the CALculation of PHase Diagram (CALPHAD) method [1994Ang,
1995Gue3, 1998Kol, 1999Liu], where the Gibbs energies of the relevant phases are described by simple
analytical functions.
[1969Bed] determined the activity coefficients at several constant mole fraction ratios (xSi/xFe) at 1627°C.
The Al activities in the temperature range of 800 to 1100°C were reported by [1973Nag], and at 900°C by
[1973Per]. [1980Sud] reported Al activity in an Fe-1 mass% Al-1 mass% Si alloy at 1485 and 1546°C.
Further experiments were carried out by [1984Ber] and [1989Bon]. The latter authors measured the
chemical potential of Al in alloys containing up to 11.8 at.% Fe and 23.7 at.% Si by the concentration cell
method in the temperature range of 577 to 1027°C. The activities of Al show a negative deviation from ideal
behavior. The results of [1984Ber] also show a similar trend.
The heat of mixing of solid alloys was measured by pouring liquid Al-Si alloy and liquid Fe into a water
calorimeter [1937Koe,1937Oel]. However, the state of equilibrium in these experiments is uncertain
[1999Liu]. The standard heat of formation of ternary intermetallics, except 7, has been determined by
solution calorimetry by [1997Vyb], [2000Li1] and [2000Li2]. [1997Vyb] used 99.99% Al, 99.9% Fe and
99.99% Si to prepare single phase 5 and 6 samples by annealing cast ingots either at 550°C ( 5) or at
600°C ( 6) for 1 month. They used an aluminum bath at 1070°C for solution calorimetry. Li et al [2000Li1,
2000Li2] used 99.99% Al, 99.999% Fe and 99.999% Si, and prepared ingots by levitation melting followed
by annealing, the conditions of which were varied to obtain single phase alloys of 5, 10, 1 and 9
[2000Li1], and 6, 2, 3, 8 and 4 [2000Li2]. Unlike [1997Vyb], Li et al used an aluminum bath at a lower
temperature of 800°C for solution calorimetry. There are differences between the results of [1997Vyb] and
[2000Li1, 2000Li2]. For example, [1997Vyb] reported that the standard heat of formation of 5
(Fe19.2Al71.2Si9.6) and 6 (Fe15.4Al69.2Si15.4) are –34.3±2 and –24.5±2 kJ/atom, respectively. The
corresponding values reported by Li et al are –24.44±1.39 kJ/mol for 5 at Fe18Al72Si10 [2000Li1] and
–20.209±0.926 kJ/mol for 6 at Fe15Al70Si15 [2000Li2]. Even though the 5 and 6 compositions of
[1997Vyb] and [2000Li1, 2000Li2] are not identical, large differences in heat of formation are unexpected.
Apparently, Li et al [2000Li1, 2000Li2] were unaware of the results of [1997Vyb], and they did not discuss
this discrepancy. Nevertheless, it is not clear if a higher bath temperature (causing oxidation) and relatively
impure starting materials used by [1997Vyb] compared to Li et al have contributed to more negative heat
of formation.
[1994Ang] determined the enthalpy of fusion of FeAl3Si2 ( 4) and Fe5Al8Si7 ( 7).
[1949Cru] reported calculated solubility isotherms of Fe and Si in solid (Al). They suggested the formation
of a ternary compound Fe2Al7Si which is close to the 5 phase at low Si content. On the other hand their
calculation seems to suggest the ternary phase FeAl5Si which is close to the 6 phase [1981Riv]. Calculation
of the liquidus surface from a purely thermodynamic approach [1946Phi2] seems to produce good result
near the binary edges. However, their approach can neither predict the composition of the precipitating
phase nor calculate the solidus curves.
[1994Ang] employed the CALPHAD technique and calculated two vertical sections corresponding to
xAl/xSi=3/1 and at xSi=0.85. [1995Gue3] calculated two partial isothermal sections at 600 and 900°C, and a
vertical section at xSi=0.78 by the CALPHAD method. They considered only two ternary phases: FeAl3Si2( 4) and Fe2Al9Si2 ( 6).
[1991Fuk, 1994Koz] performed a theoretical analysis of phase separation involving Fe, 2 and 1 phases.
The free energy of ternary alloys is evaluated statistically using a pair-wise interaction up to second nearest
neighbor. Both chemical and magnetic interactions based on Bragg-Williams-Gorsky model were used. The
calculated phase diagrams are found to be consistent with the experimental ones.
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[1998Kol] and [1999Liu] carried out detailed thermodynamic assessments of the ternary system by the
CALPHAD method. According to our classification, [1998Kol] considered six ternary phases 1, 2, 3, 4,
5 and 6, whereas [1999Liu] considered seven ternary phases: 1, 2, 3, 4, 5, 6, and 7, called 1, , 23,
, , , , respectively. [1999Liu] argued that 2 and 3 have very similar Fe contents, and wondered, if they
are the same phase with a small homogeneity range. This view was also accepted by [2002Rag]. However,
as summarized in Table 2, 2 and 3 have different crystal structures. [1999Liu] computed the liquidus
surface, isothermal sections at 600 and 1000°C, and vertical sections at 1.3, 2, 5, 10% Fe and 2% Si (mass).
Notes on Materials Properties and Applications
[1951Oga1, 1951Oga2, 1983Sch] reported the ferromagnetic behavior of Fe3Al-Fe3Si alloys. [1968Aru1,
1968Aru2, 1970Aru] reported that the occupation of ordered sites by all three Al, Fe and Si atoms
accompanied with a minimum in electrical resistivity at Fe75Al18Si7 and Fe6(Al,Si). [1996Szy] reported
that dissolved Al in FeSi2(r) increases its magnetic susceptibility, and both FeSi and FeSi2(r) exhibit Van
Vleck paramagnetism even at very low temperature (up to 4.2 K). [1996Fri] and [1998Dit] studied the
metal-insulator transition in Al doped FeSi. [1998Dit] reported lattice constant, thermoelectric effect, Hall
effect, electrical conductivity, magnetic susceptibility, specific heat and magnetoresistance in FeSi1-xAlx,
with 0 x 0.08. All these properties confirm a metal to insulator transition of FeSi, which is otherwise
a Kondo insulator. [1999Oht] has reported that doping of FeSi2(r) with 3 at.% Al improves its
thermoelectric figure of merit. The magnetic properties of ternary alloys have been discussed in detail by
[1986Tak] and [1988Dor].
[1993Sch] investigated the plastic deformation of single-crystal Al20Fe75Si5 alloy as a function of
temperature. The critical resolved shear stress exhibits a non-monotonic behavior with a maximum around
530°C. The non-monotonic behavior was correlated with the temperature-dependent dislocation mobility
rather than a decrease in D03 long-range order parameter. [1996Cho, 2001Cho] reported the microstructure,
hardness and tensile properties of Al-5Fe-16Si(mass%) alloy, processed by powder metallurgy up to 520°C.
[1948Jen] demonstrated a relationship between the constitutional diagram and the susceptibility to cracking
of the Al-Fe-Si alloys. A key factor in determining the corrosion behavior of Al-rich alloys is the Fe/Si ratio.
Low Fe/Si ratio in ternary alloys exhibit better corrosion resistance in both industrial and marine
environment [2000Bha].
Miscellaneous
In recent years, the solidification of Al-rich ternary alloys has been investigated rather extensively
[1983Per, 1991Don, 1991Lan, 1995Bel, 1995Gue3, 1996All, 1997All, 1997Sto, 1997Can, 1999Cho,
1999Tay, 2000Dut, 2001Hsu, 2001Sha, 2002Mer]. [1983Per] discussed the effect of metastable liquid
miscibility gaps, metastable eutectic and metastable peritectic on the rapid solidification processing and
alloy design. Addition of up to 0.11 mass% Si in a Al-0.5 mass% Si alloy is reported to favor the formation
of the metastable phase FeAl6 [1978Suz].
[1995Bel] proposed a non-equilibrium solidification method to analyze the cast microstructure of ternary
alloys. This method utilizes equilibrium phase diagram, but assumes that the peritectic reactions are
suppressed and the eutectic reactions occur according to the equilibrium phase diagram. Cantor and
co-workers [1996All, 1997All, 1997Can] have discussed the role of heterogeneous nucleation on the phase
selection and solidification.
[1997Sto] studied the effect of cooling rate and solidification velocity on the microstructure selection of
Al-3.5 mass% Fe-(1 to 8.5) mass% Si alloys by wedge chill casting and Bridgman directional solidification
techniques. In the latter case, the front growth velocity was in the range of 0.01 to 2 mm/s under a
temperature gradient of 15°C/mm. Also, at front velocities greater than 1 mm/s, the primary intermetallics
were suppressed. The results of Al-3.5 mass%Fe-8.5 mass% Si were summarized in terms of a kinetically
based solidification microstructure selection diagram. [1999Tay] applied Scheil equation to predict the
defect-onset (porosity) during solidification of Al-rich alloys as a function of Fe and Si contents. They found
that a defect-free casting can be obtained if the solidification proceeds directly to the invariant reaction E1
(L 6+(Al)+(Si)), whereas poor casting may result when the solidification proceeds via the (Al)- 6 eutectic
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valley. The critical Fe-content at which the porosity is minimized is a function of Si-content in the alloy.
[2001Sha] also carried out Bridgman directional solidification of a model 6xxx alloy (Al-0.3 mass% Fe-0.6
mass% Si-0.8 mass% Mg), and obtained solidification front velocity in the range of 5 to 120 mm/min. They
observed two ternary phases, -FeAlSi ( 5) and -FeAlSi ( 6), of which the latter is metastable. At low front
velocity, such as 30 to 60 mm/min, -FeAlSi dominate the microstructure, while at high front velocity, such
as 120 mm/min, -FeAlSi dominates the phase selection.
Figure 21 shows the surface of secondary crystallization of the Al-corner after [1943Phi]. It should be noted
that the data relate to slowly-cooled alloys in a non-equilibrium state.
Since both the Al-Fe and Fe-Si binary systems form -loops, a ternary -loop is expected. [1931Wev]
reported the coordinates of the phase boundaries of the ternary -loop which are listed in Table 5.
[1960Voz] reported the effect of impurities on the solid solubility of Al alloys by means of electrical
resistivity. [1972Ere] studied the dissolution kinetics of Fe in Al-Si melts at 700, 750 and 800°C, the
kinetics of which was correlated with the formation of various intermediate phases.
[2000Sri] reported synthesis of bulk ternary intermetallics using elemental powder mixture by
self-propagating high temperature synthesis. They used cold compacted powder mixtures that were heated
to 650°C in a vacuum furnace. Both stable ( 2, 5 and 6) and metastable phases were obtained in this
process. They also reported hardness of the intermetallics.
[1998Akd] proposed that the value of activity coefficient of Al in -(Fe,Al,Si) alloys has a strong influence
on the formation and growth kinetics of interfacial diffusion layer. [1999Oht] has discussed the sintering
mechanism of Al-Fe-Si alloys, particularly the role of liquid phase, in the context of fabricating an Al-doped
FeSi2(r) phase. [2001Jha] has discussed the diffusion path of Al in ternary bcc alloys.
References
[1923Dix] Dix Jr., E.H., “Observations on the Occurrence of Iron- and Silicon in Aluminium”, Trans.
AIME, 69, 957-971 (1923) (Experimental, 12)
[1923Han] Hanson, D., Gayler, M.L.V., “The Heat-treatment and Mechanical Properties of Alloys of
Aluminium with Small Percentages of Copper”, J. Inst. Met., 29, 491-506 (1923)
(Experimental, 1)
[1923Wet] Wetzel, E., “Advances in Aluminium Research” (in German), Die Metallboerse, 13,
737-738 (1923) (Equi. Diagram, Experimental, 6)
[1924Fus] Fuss, V., “On the Constitution of Ternary Al Alloys” (in German), Z. Metallkd., 16, 24-25
(1924) (Experimental, 3)
[1927Gwy] Gwyer, A.G.C., Phillips, H.W.L., “The Ternary System: Aluminium-Silicon-Iron” in „The
Constitution of Alloys with Silicon and Iron“, J. Inst. Met., 38, 44-83 (1927) (Equi.
Diagram, Experimental, #, *, 9)
[1928Dix] Dix, Jr., E.H., Heath, Jr., A.C., “Equilibrium Relations in Aluminium-Silicon and
Aluminium-Iron-Silicon Alloys of High Purity”, Trans. AIME, Inst. Met. Div., 164-197
(1928) (Equi. Diagram, Experimental, #, *, 39)
[1931Fin] Fink, W.L., Van Horn, K.R., “Constituents of Aluminium-Iron-Silicon Alloys”, Trans.
AIME, Inst. Met. Div., 383-394 (1931) (Equi. Diagram, Experimental, #, *, 12)
[1931Fus] Fuss, V., “The Constitution of Aluminium-rich Al-Fe-Si Alloys” (in German), Z. Metallkd.,
23, 231-236 (1931) (Equi. Diagram, Experimental, 6)
[1931Wev] Wever, F., Heinzel, A., “Two Examples of Ternary Iron Systems with Closed -Loop” (in
German), Mitt. K.-W.-Inst. Eisenforschung, 13, 193-197 (1931) (Equi. Diagram,
Experimental, #, *, 14)
[1932Nis] Nishimura, H., “An Investigation of Al-rich Al-Fe-Si Alloys” (in Japanese), Tetsu to
Hagane, 18, 849-860 (1932) (Equi. Diagram, Experimental, #, *, 40)
[1933Nis] Nishimura, H., “Investigation of Ternary Aluminium Alloy Systems: Al-rich Al-Fe-Si
System”, Mem. Coll. Eng. Kyoto Univ., 7, 285-303 (1933) (Equi. Diagram, Experimental, #,
*, 13)
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[1934Fue] Fuess, V., “Aluminium-Iron-Silicon” (in German), in “Metallography of Aluminium and its
Alloys”, Berlin, 109-117 (1934) (Equi. Diagram, Experimental, 6)
[1934Roe] Roehrig, H., Kopernick, E., “On Spherically Precipitated Aluminium-Iron-Silicon Eutectic
in Pure Aluminium” (in German), Metallwirtschaft, 13, 591-593 (1934) (Experimental, 2)
[1935Bos] Bosshard, M., “Diffusional Research as a Means for the Simple Micrographic Detection of
Compound Formation between Alloy Constituents in Ternary and Multicomponent
Systems” (in German), Aluminium, 17, 477-481 (1935) (Experimental, 1)
[1936Jae] Jaeniche, W., “On the System Aluminium-Iron-Silicon” (in German), Alum. Arch., (5), 1-21
(1936) (Crys. Structure, Equi. Diagram, Experimental, #, *, 28)
[1937Koe] Koerber, F., Oelsen, W., Lichtenberg, H., “On the Thermochemistry of Alloys. II. Direct
Determination of the Heat of Formation of Ternary Alloys of the System
Iron-Nickel-Aluminium-Silicon, as well as Certain Alloys of the Copper - Manganese -
Aluminium System” (in German), Mitt. K.-W.-Inst. Eisenforschung, 19, 131-159 (1937)
(Experimental, Thermodyn., 50)
[1937Oel] Oelsen, W., “The Heats of Formation of Binary and Ternary Alloys and Their Importance
in Metallurgical Reactions” (in German), Z. Electrochem., 43, 530-535 (1937)
(Experimental, Thermodyn., 15)
[1937Ser] Sergeev, L.N., Rimmer, B.I, “Constitution of the System Aluminium-Iron-Silicon” (in
Russian), Metallurgia, (9/10), 112-125 (1937) (Crys. Structure, Equi. Diagram, Review)
[1937Ura] Urasov, G.G., Shashin, A.V., “Constitution of the (Ternary) Aluminium Alloys with Silicon
and Iron” (in Russian), Metallurgia, (4), 27-41 (1937) (Equi. Diagram, Experimental)
[1940Tak] Takeda, H.P., Mutuzaki, K., “The Equilibrium Diagram of the Iron-Aluminium-Silicon
System” (in Japanese), Tetsu to Hagane, 26, 335-361 (1940) (Equi. Diagram, Experimental,
#, *, 27)
[1941Pan] Panseri, C., Guastalla, B., “Investigations on the Permanent Modification of Eutectic
Aluminium-Silicon Alloys. I.-Influence of Titanium Additions as the third Components”,
Allumino, 10(5), 202-227 (1941) (Equi. Diagram, Experimental, Review, 161)
[1943Mon] Mondolfo, L.F., “Aluminum-Iron-Silicon”, in “Metallography of Aluminum Alloys”, John
Wiley & Sons, Inc., New York, 95-97 (1943) (Equi. Diagram, Review, #, 27)
[1943Phi] Phillips, H.W.L., Varley, P.C., “Constitution of Alloys of Aluminium with Magnesium,
Silicon and Iron”, J. Inst. Met., 69, 317-350 (1943) (Equi. Diagram, Experimental, #, *, 11)
[1946Phi1] Phillips, H.W.L., “The Constitution of Alloys of Aluminium with Magnesium, Silicon and
Iron”, J. Inst. Met., 72, 151-227 (1946) (Equi. Diagram, Experimental, #, *, 86)
[1946Phi2] Phillips, H.W.L., “The Application of Some Thermodynamic Principles to the Liquidus
Surfaces of Alloys of Aluminium with Magnesium, Silicon and Iron”, J. Inst. Met., 72,
229-242 (1946) (Theory, Thermodyn., #, *, 21)
[1946Sel] Selisski, Ya.P., “The Lattice Spacing of Solid Solutions of Fe, Si and Al Rich in Fe” (in
Russian), Zh. Fiz. Khim., 20, 597-604 (1946) (Crys. Structure, Experimental, *, 15)
[1948Jen] Jennings, P.H., Pumphrey, W.L., “A Consideration of the Constitution of
Aluminium-Iron-Silicon Alloys and Its Relation to Cracking Above the Solidus”, J. Inst.
Met., 74, 249-258 (1948) (Experimental, 14)
[1949Cru] Crussard, C., Aubertin, F., “Study of Thermo-electric and Thermodynamic Properties of
Aluminium-Base Alloys Containing Mg, Si, Fe or Ti” (in French), Rev. Metall., 46, 661-675
(1949) (Equi. Diagram, Experimental, #, *, 12)
[1950Gme] Gmelins Handbook of Inorganic Chemistry, “Aluminium-Iron-Silicon Alloys. The Al-Fe-Si
Phase Diagram” (in German), A(8), System No. 35, Verlag Chemie GmbH, Weinheim,
1334-1370 (1950) (Equi. Diagram, Review, #, *, 15)
[1950Phr] Phragmen, G., “On the Phase Occurring in Alloys of Aluminium with Copper, Magnesium,
Manganese, Iron and Silicon”, J. Inst. Met., 77, 489-552 (1950) (Equi. Diagram,
Experimental, #, *, 67)
371
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1951Hol] Holik, L., Nowotny, H., Thury, W., “Investigation of the Microstructure in the Al-Corner of
the System Aluminium-Iron-Silicon” (in German), Berg- u. Huettenmn. Monatsh. Hochsch.
Leoben, 96, 181-184 (1951) (Equi. Diagram, Experimental, #, *, 12)
[1951Now] Nowotny, H., Komerek, K., Kromer, J., “An Investigation of the Ternary System:
Aluminium-Iron-Silicon” (in German), Berg- u. Huettenmn. Monatsh. Hochsch. Loeben, 96,
161-169 (1951) (Crys. Structure, Equi. Diagram, Experimental, *, 31)
[1951Oga1] Ogawa, S., Matsuzaki, Y., “Study of the Supperlattices in Ternary Iron-Aluminium-Silicon
Alloys by X-rays”, Nippon Kinzoku Gakkaishi, 15, 242-244 (1951) (Crys. Structure,
Experimental, *, 9)
[1951Oga2] Ogawa, S., Matsuzaki, Y., “Study on the Superlattice of Ternary Alloys by X-rays”, Sci.
Rep. Res. Inst. Tohoku Univ., 3A, 50-54 (1951) (Crys. Structure, Experimental, *, 9)
[1951Pra1] Pratt, J.N., Raynor, G.V., “Intermetallic Compounds in Ternary Aluminium-rich Alloys
Containing Transitional Metals”, Proc. Roy. Soc. A, A205, 103-118 (1951) (Theory, 14)
[1951Pra2] Pratt, J.N., Raynor, G.V., “The Intermetallic Compounds in the Alloys of Aluminium and
Silicon with Chromium, Manganese, Iron, Cobalt and Nickel”, J. Inst. Met., 79, 211-232
(1951) (Crys. Structure, Equi. Diagram, Experimental, #, *, 32)
[1951Ran] Ransley, C.E., “Determination of Phase Boundaries in Solid Alloy Systems by a Diffusion
Technique”, Nature, 167, 814 (1951) (Experimental, 1)
[1951Sat] Sato, H., Yamamoto, H., “The Behaviours of Fe-Al, Fe-Si and Fe-Al-Si Alloys Considered
from the Standpoint of Ferromagnetic Supperlattice”, J. Phys. Soc. Jpn., 6, 65-66 (1951)
(Experimental, *, 2)
[1952Arm] Armand, M., “On the Phases in the Ternary System Aluminium-Iron-Silicon” (in French),
Comt. Rend. Acad. Sci. Paris, 235, 1506-1508 (1952) (Crys. Structure, Experimental, *, 9)
[1952Han] Hanemann, H., Schrader, A., Ternary Alloys of Aluminium (in German), Verlag: Stahleisen,
Duesseldorf, 109-115 (1952) (Equi. Diagram, Review, #, 12)
[1953Rob] Robson, K., Black, P.J., “An X-ray Examination of an -(Al-Fe-Si) Ternary Compound”,
Philos. Mag., 44, 1392-1397 (1953) (Crys. Structure, Experimental, *, 10)
[1954Gar] Garrod, R.I., Hogan, L.M., “The Superlattice in Sendust”, Acta Metall., 2, 887-888 (1954)
(Crys. Structure, Experimental, *, 5)
[1954Spi] Spiegelberg, A.P.W., Danielsson, S.L.A., Astroem, H., “The Crystal Structure of Some
Phases Occurring in Alloys of Aluminium, Iron and Silicon and Their Relationship to other
Phases”, Acta Crystallogr., 7, 634 (1954) (Crys. Structure, Experimental, *, 4)
[1955Arm] Armand, M., “Liquation and Equilibrium Diagram: Applications to the Diagram of
Aluminium-Iron-Silicon Alloys” (in French), Congress International de l'Aluminium, Paris,
1954, Revue de l'Aluminium, 1, 305-327 (1955) (Crys. Structure, Experimental, *, 9)
[1955Bla] Black, P.J., “Brillouin Zones of Some Intermetallic Compounds”, Philos. Mag., 46, 401-409
(1955) (Crys. Structure, Experimental, *, 23)
[1955Obi] Obinata, I., Komatsu, N., “On the Phases Occuring in Alloys of Aluminium with Iron and
Silicon” (in Japanese), Nippon Kinzoku Gakkaishi, 19, 197-201 (1955) (Crys. Structure,
Experimental, 30)
[1956Spe] Sperry, P.R., “The Intermetallic Phases in 2024 Aluminum Alloys”, Trans. ASM, 48,
904-918 (1956) (Experimental, 11)
[1959Phi] Phillips, H.W.L., Annoted Equilibrium Diagrams of Some Al Alloy Systems, Monograph,
Inst. of Met., London, (25), 57-65 (1959) (Equi. Diagram, Review, #, *, 18)
[1960Lee] Lee, J.R., “Liquidus-Solidus Relations in the System Iron-Aluminum”, J. Iron Steel Inst.
Met., 194, 222-224 (1960) (Equi. Diagram, Experimental, 5)
[1960Spe] Spengler, H., “The Importance of Research on Eutectics and its Application to Ternary
Eutectic Aluminium Alloys” (in German), Metall, 14, 201-206 (1960) (Experimental)
[1960Voz] Vozdvizhenskiy, V.M., “The Effect on the Saturation of Solid Solution in Some Al Alloys”
(in Russian), Izv. Vyss. Uchebn. Zaved., Tsvetn. Metall., (5), 116-120 (1960) (Equi.
Diagram, Experimental, 19)
372
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1961Phi] Phillips, H.W.L., “Al-Fe-Si”, in “Equilibrium Diagrams of Aluminium Alloy Systems”, The
Aluminium Develop. Assoc., London, 91-96 (1961) (Equi. Diagram, Experimental, #, *)
[1961Sab] Sabirzyanev, A.V., Shumilov, M.A., Gel´d, P.V. Ozhogikhina, G.V., “Solubility of Al in
-Leoboite”, Phys. Met. Metallogr., 12(5), 81-87 (1961), translated from Fiz. Met.
Metalloved., 12, 714-721 (1961) (Crys. Structure, Experimental, 14)
[1964Lai] Lainer, D.A., Kurakin, A.K., “Mechanism of the Influence of Silicon in Aluminium on the
Reaction Diffusion of Iron”, Phys. Met. Metallogr., 18, 134-137 (1964), translated from Fiz.
Met. Metalloved., 18, 145-148 (1964) (Crys. Structure, Experimental, 13)
[1965Sab] Sabirzyanev, A.V., Shumilov, M.A., “The Solubility of Al and P in Constituents of High-Si
Ferrosilicon” (in Russian), Tr. Ural'sk Politekh. Inst., 144, 35-40 (1965) (Experimental, 14)
[1965Skr] Skripova, E.A., Letun, G.M., “The Solubility of Al in -Leboite” (in Russian), Tr. Ural'sk
Politekh. Inst., 144, 67-70 (1965) (Crys. Structure, Experimental, 4)
[1967Coo] Cooper, M., “The Crystal Structure of the Ternary Alloys S-AlFeSi”, Acta Crystallogr., 23,
1106-1107 (1967) (Crys. Structure, Experimental, *, 5)
[1967Mun] Munson, D., “A Clarification of the Phases Occuring in Aluminium-Rich
Aluminium-Iron-Silicon Alloys with Particular Reference to the Ternary Phase -AlFeSi”,
J. Inst . Met., 95, 217-219 (1967) (Crys. Structure, Equi. Diagram, Experimental, *, 12)
[1967Sun] Sun, C.Y., Mondolfo, L.F., “A Clarification of the Phases Occuring in Al-Rich Al-Fe-Si
Alloys”, J. Inst. Met., 95, 384 (1967) (Crys. Structure, Experimental, *, 2)
[1968Aru1] Arutyunyan, S.V., Selissky, Ya.P., “The Question of Superstructure in Fe-Si-Al Alloys” (in
Russian), Izv. Akad. Nauk. Arm. SSR, Fizika, 3, 8-11 (1968) (Crys. Structure,
Experimental, 5)
[1968Aru2] Arutyunyan, S.V., “Some Features of Atomic Ordering in Ternary Fe-Si-Al Alloys” (in
Russian), Izv. Akad. Nauk Arm. SSR, Fizika, 3, 294-297 (1968) (Crys. Structure,
Experimental, 2)
[1968Dri] Drits, M.E., Kadaner, E.S., Turkina, N.I., “The System Al-Fe-Si” (in Russian), in
“Diagrammy Sostoyaniya Metallich. Sistem”, Nauka, Moscow, XIV, 109 (1968) (Equi.
Diagram, Review, 1)
[1968Lih] Lihl, F., Burger, R., Sturm, F., Ebel, H., “Constitution of Fe-rich Ternary Al-Fe-Si Alloys”,
Arch. Eisenhuettenwes., 39, 877-880 (1968) (Equi. Diagram, Experimental, *, 22)
[1968Sab1] Sabirzyanev, A.V., Gel´d, V.P., “Some Features of the Peritectoid Transformation in
-Leboite (FeSi2) Alloys Alloyed with Al, Ca and P” (in Russian), Tr. Ural'sk Politekh.
Inst., 167, 75-80 (1968) (Experimental, 6)
[1968Sab2] Sabirzyanev, A.V., Gel´d, V.P., “Nature of Solid Solutions of Aluminium and Phosphorus
in Iron Monosilicide” (in Russian), Izv. Vyss. Uchebn. Zaved., Chern. Metall., 11, 21-26
(1968) (Experimental, 3)
[1969Bed] Bedon., P., Ansara, I., Desre, P., “Isothermal Sections at 1900 K of the
Silver-Aluminium-Iron-Silicon and Silver-Aluminium-Nickel-Silicon Metallic Systems;
Activity of Aluminium in Molten Aluminium-Iron-Silver-Silicon and
Aluminium-Nickel-Silver Alloys” (in French), Mem. Sci. Rev. Metall., 66, 907-913 (1969)
(Experimental, Thermodyn., 5)
[1969Pan] Panday, P.K., Schubert, K., “Structure Studies in Some Alloys T-B3-B4 (T = Mn, Fe, Co, Ir,
Ni, Pd; B4 = Si, Ge)” (in German), J. Less-Common Met., 18, 175-202 (1969) (Crys.
Structure, Experimental, *, 32)
[1969Pol] Polishchuk, V.E., Selissky, YA.P., “High-Temperature Study of the Structure and Electrical
Properties of the Fe-Si-Al System” (in Russian), Ukrain. Fiz. Zhur., 14, 1722-1724 (1969)
(Equi. Diagram, Experimental, #, *, 9)
[1970Aru] Arutyunyan, S.V., “Transition from Atomic Ordering to Disordering in Fe3(Al,Si) Alloys
Related to the Formation of the K-Effect” (in Russian), Izv. Akad. Nauk Arm. SSR, Ser. Tekh.
Nauk, 32, 36-42 (1970) (Experimental, 4)
373
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1970Mit] Mitani, H., Nagai, H., Ohtani, T., “Dry Refining of Aluminium. IV. Activity Measurements
of the Ternary Liquid Al-Fe-Si System by the EMF Method” (in Japanese), Nippon Kinzoku
Gakkaishi, 34, 165-170 (1970) (Experimental, Thermodyn., 16)
[1971Gle] Glezer, A.M., Molotilov, B.V., Polishchuk, V.Ye., Selissky, Ya.P., “X-ray and Electron
Microscopic Analysis of the Fine Structure of Ordering High-Fe-Al-Si Alloys”, Phys. Met.
Metallogr., 32(4), 39-47 (1971) (Experimental, 19)
[1972Ere] Eremenko, V.N., Natanzon, Ya.V., Ryabov, V.R., Dzykovich, I.Ya., “Interaction of Al-Si
Melts with Steel” (in Russian), Liteinoe Proizvod., (2), 21-22 (1972) (Experimental)
[1973Kat] Katsnel´son, A.A., Polishchuk, V.Ye., “Energy Characteristics of Atomic Ordering in
Alloys of Iron with Aluminium and Silicon”, Phys. Met. Metallogr., 36(2), 86-90 (1972)
(Equi. Diagram, Experimental, #, *, 10)
[1973Kow] Kowatschewa, R., Dafinowa, R., Kamenowa, Z., Momtschilov, E., “Metallographic
Determination of Intermetallic Compounds in Aluminium Alloys”, Metallography, 10,
131-143 (1973) (Crys. Structure, Experimental, 9)
[1973Nag] Nagai, H., Mitani, H., “Activity Measurements of the Ternary Liquid Al-Si-Fe System by
the EMF Method”, Tran. Jpn. Inst. Met., 14, 130-134 (1973) (Experimental, Thermodyn., 9)
[1973Per] Perkins, J., Desre, P., “Determination of Activities in the Al-Fe-Si System by a EMF
Method” (in French), Rev. Int. Hautes Temp. Refract., 10, 79-84 (1973) (Experimental,
Thermodyn., 13)
[1974Mur] Murav´eve, A.A., German, N.V., Zarechnyuk, O.S., Gladyshevskii, E.I., “Ternary
Compounds of the Fe-Al-Si System” (in Russian), Proc. 2nd All-Union Conf. on Crys.
Chem. Intermet. Compounds, L'vov, October, 35-36 (1974) (Crys. Structure, Experimental,
*)
[1975Bar] Barlock, J.G., Mondolfo, L.F., “Structure of Some Aluminum-Iron-Magnesium-Silicon
Alloys”, Z. Metallkd., 66, 605-611 (1975) (Crys. Structure, Equi. Diagram, Experimental, *,
7)
[1977Cor] Corby, R.N., Black, P.J., “The Structure of -AlFeSi by Anomalous Dispersion Method”,
Acta Crystallogr. B: Struct. Crystallogr. Crys. Chem., 33B, 3468-3475 (1977) (Crys.
Structure, Experimental, *, 18)
[1977Hoi] Hoeier, R., Lohne, O., Moertvedt, S.T., “AlFeSi-Particles in an Al-Mg-Si-Fe Alloy”, Scand.
J. Metall., 6, 36-37 (1977) (Crys. Structure, Experimental, *, 3)
[1977Igl] Iglessis, J., Frantz, C., Gantois, M., “Conditions for the Formation of the Iron Phases in
Commercial Purity Aluminium-Silicon Alloys” (in French), Mem. Sci. Rev. Metall., 74,
237-242 (1977) (Experimental, *, 14)
[1977Nic1] Niculescu, V., Raj, K., Burch, T., Budnick, J.J., “Hyperfine Interactions and Structural
Disorder of Fe2Si1-xAlx Alloys”, J. Phys. F, Met. Phys., 7, L73-76 (1977) (Experimental, 7)
[1977Nic2] Niculescu, V., Budnick, J.J., “Limits of Solubility, Magnetic Properties and Electron
Concentration in Fe3-xTxSi System”, Solid State Commun., 24, 631-634 (1977) (Theory, 17)
[1977Sim] Simensen, C.J., Vellasamy, R., “Determination of Phases Present in Cast Material of an
Al-0.5 wt.% Fe-0.2 wt.% Si Alloy”, Z. Metallkd., 68, 428-431 (1977) (Crys. Structure,
Experimental, 10)
[1977Suw] Suwalski, J., Kisynska, K., Piekoszewski, J., “Distribution of Fe Atoms in Ordered
Fe1-x(Al,Si)x”, Proc. Int. Conf. Mössbauer Spectroscopy, Barb, D., Tarina, D. (Eds.),
Docum. Office, Central Inst. Phys., Bucharest, Romania, 125-126 (1977) (Theory, 2)
[1978Suz] Suzuki, H., Kanno, M., Tanabe, H., Itoi, K., “The Effect of Si or Mg Addition on the
Metastable to Stable Phase Changes in an Al-0.5% Fe Alloy” (in Japanese), J. Jpn. Inst.
Light Met., 28, 558-565 (1978) (Crys. Structure, Experimental, 7)
[1978Xu] Xu, W.-C., Su, X.-J., “An Investigation on the Structure of Fe-Si-Al Alloy” (in Chinese),
Acta Phys. Sin., 27, 576-582 (1978) (Crys. Structure, Experimental, *, 9)
[1979Bur] Burch, T.J., Raj, K., Jena, P., Budnick, J.I., Niculescu, V., Muir, W.B., “Hyperfine-Field
Distribution in Fe3Si1-xAlx Alloys and a Theoretical Interpretation”, Phys. Rev. B: Solid
State, 19B, 2933-2938 (1979) (Experimental, Theory, 17)
374
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1979Cow] Cowdery, J.S., Kayser, F.X., “Lattice Parameters of Ferromagnetic D03-Structured
Iron-Aluminium-Silicon Alloys”, Mater. Res. Bull., 14, 91-99 (1979) (Crys. Structure,
Experimental, *, 24)
[1979Mor] Mora, R., “The Determination of the Al-Fe-Si Phase in Homogenized Aluminium Alloy
6063” (in Spanish), Rev. Metall., 15, 91-95 (1979) (Crys. Structure, Experimental, *, 15)
[1980Sud] Sudavsova, V.S., Batalin, G.I., “Aluminium Activity in Liquid Iron Alloys” (in Russian),
Ukrain. Khim. Zhur., 46, 268-270 (1980) (Experimental, Thermodyn., 8)
[1981Riv] Rivlin, V.G., Raynor, G.V., “Phase Equilibria in Iron Ternary Alloys 4: Critical Evaluation
of Constitution of Aluminium-Iron-Silicon System”, Int. Met. Rev., 26, 133-152 (1981)
(Equi. Diagram, Review, #, *, 56)
[1981Wat] Watanabe, H., Sato, E., “Phase Diagram in Aluminium Alloys” (in Japanese), J. Jpn. Inst.
Light Met., 31, 64-79 (1981) (Equi. Diagram, Review, #, *, 22)
[1981Zar] Zarechnyuk, O.S., German, N.V., Yanson, T.I., Rykhal, R.M., Murav'eva, A.A., “Some
Phase Diagrams of Aluminium with Transition Metals, Rare Earth Metals and Silicon” (in
Russian), in “Fazovje Ravnovesija v Metallicheskych Splavach”, Nauka, Moscow, 69-71
(1981) (Crys. Structure, Equi. Diagram, Experimental, #, *, 5)
[1982All] Allen, S.M., Cahn, J.W., “Phase Diagram Features Associated with Multicritical Points in
Alloy Systems”, Bull. Alloy Phase Diagrams, 3(3), 287-295 (1982) (Theory, 25)
[1982Cha] Chang, Y.J., “An Electron Microscopic Investigation of Order-Disorder Transformation in
a Fe-Si-Al (SENDUST) Alloy and its Dislocation Configurations”, Acta Metall., 30,
1185-1192 (1982) (Crys. Structure, Experimental, 17)
[1982Kub] Kubaschewski, O., “Iron-Aluminium”, “Iron-Silicon”, in “Iron-Binary Phase Diagrams”,
Springer Verlag, Berlin, 5-9 and 136-139 (1982) (Equi. Diagram, Review, #, *, 26, 23)
[1982Miy] Miyazaki, T., Tsuzuki, T., Kozakai, T., Fujimoto, Y., “Phase Separation of Fe-Si-Al
Ordering Alloys” (in Japanese), Nippon Kinzoku Gakkai-Si, 46, 1111-1119 (1982) (Crys.
Structure, Experimental, 37)
[1982Wes] Westgren, H., “Formation of Intermetallic Compounds During DC Casting of Commercial
Purity Al-Fe-Si Alloy”, Z. Metallkd., 73, 361-368 (1982) (Crys. Structure, Experimental,
24)
[1983Gle] Glezer, A.M., Molotilov, B.V., Prokoshin, A.F., Sosnin, V.V., “Structural Features of a
SENDUST (Fe-Si-Al) Alloy Obtained by Quenching from the Melt. I. The Study of Atomic
Ordering Properties”, Phys. Met. Metallogr., 56(4), 110-117 (1983), translated from Fiz.
Met. Metalloved., 56(4), 750-757 (1983) (Crys. Structure, Experimental, *, 12)
[1983Per] Perepezko, J.H., Boettinger, J.W., “Use of Metastable Phase Diagrams in Rapid
Solidification”, Proc. Mater. Soc. Symp., Alloy Phase Diagrams, 19, 223-240 (1983)
(Review, Theory, 52)
[1983Sch] Schneeweiss, O., Zemcik, T., Zak, T., Mager, S., “Atomic Structure and Magnetic
Properties of the Pseudobinary Alloys Fe3(Al,Si)”, Phys. Status Solidi A, 79A, 125-129
(1983) (Experimental, 10)
[1984Ber] Berecz, E., Bader, I., Weberner, Kovacs, E., Hovath, J., Szina, G., “Thermodynamic
Examination of Aluminium Alloys by the Electrochemical Method” (in Hungarian),
Banyasz. Kohasz. Lapok, Kohasz, 117, 413-417 (1984) (Experimental, Thermodyn., 10)
[1984Don] Dons, A.L., “AlFeSi-Particles in Commercial Pure Aluminium”, Z. Metallkd., 75, 170-174
(1984) (Equi. Diagram, Experimental, #, *, 10)
[1984Mat] Matsumura, S., Sonobe, A, Oki, K., Eguchi, T., “Ordering with Phase Separation in an
Fe-Al-Si Alloy”, in “Phase Transformations in Solids”, Proc. Conf. Mater. Res. Soc.,
Elsevier, Amsterdam, 21, 269-274 (1984) (Crys. Structure, Experimental, 12)
[1985Cao] Cao, R., Li, G., Wu, X., “Some Thermodynamic Properties in Process of Thermal Reduction
of Magnesium with High Aluminium Alloy” (in Chinese), Acta Metall. Sin., 21, A471-A476
(1985) (Experimental, Thermodyn., 9)
[1985Don1] Dons, A.L., “Superstructure in -Al(MnFeCrSi)”, Z. Metallkd., 76, 151-153 (1985) (Crys.
Structure, Experimental, *, 11)
375
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1985Don2] Dons, A.L., “AlFeSi-Particles in Industrially Cast Aluminium Alloys”, Z. Metallkd., 76,
609-612 (1985) (Experimental, 14)
[1985Gri] Griger, A., Stefaniay, V., Turmezey, T., “Analysis of Ternary Al-Fe-Si Phases on High
Purity Base”, Proc.: 6th Int. Symp. High Purity Mater. Sci. Techn., Supplement, Dresden,
GDR, 6-10 May, 187-188 (1985) (Experimental)
[1985Liu] Lui, P., Thorvaldsson, L., Dunlop, G.L., “The Formation of Intermetallic Compounds
during Solidification of Dilute Al-Fe-Si Alloys”, Ultramicroscopy, 17, 178 (1985) (Crys.
Structure, Experimental)
[1985Riv] Rivlin, V.G., “Assessment of Phase Equilibria in Ternary Alloys of Iron”, J. Less-Common
Met., 114, 111-121 (1985) (Equi. Diagram, Review, #, *, 4)
[1985Suz] Suzuki, H., Arai, K., Shiga, M., Nakamura, Y., “Mössbauer Effect of Al-Fe-Si Intermetallic
Compounds”, Metall. Trans. A, 16A, 1937-1942 (1985) (Experimental, 22)
[1986Len] Lendvai, A., “Phase Diagram of the Al-Fe System up to 45 mass% Iron”, J. Mater. Sci. Lett.,
5, 1219-1220 (1986) (Equi. Diagram, Experimental, 7)
[1986Dun] Dunlap, R.A., Dini, K., “Amorphization of Rapidly Quenched Quasicrystalline
Al-Transition Metal Alloys by the Addition of Si”, J. Mater. Res., 1, 415-419 (1986) (Crys.
Structure, Experimental, 19)
[1986Liu1] Liu, P., Dunlop, G.L., “Constituent Formed during Solidification of Al-Fe-Si Alloys”, Proc.
Conf. Aluminium Alloys: Their Physical and Mechanical Properties, I, Chalottesville,
Virginia, USA, 15-20 (1986) (Crys. Structure, Experimental, *, 20)
[1986Liu2] Lui, P., Thorvaldsson, L., Dunlop, G.L., “Formation of Intermetallic Compounds during
Solidification of Dilute Al-Fe-Si Alloys”, Mater. Sci. Technol., 2, 1009-1018 (1986) (Crys.
Structure, Experimental, *, 26)
[1986Miy] Miyazaki, T., Kozaki, T., Tsuzuki, T., “Phase Decomposition of Fe-Si-Al Ordered Alloys”,
J. Mater. Sci., 21, 2557-2564 (1986) (Equi. Diagram, Experimental, #, *, 26)
[1986Tak] Takahashi, M., “Magnetic Properties of Iron-Silicon-Aluminium Alloy Single Crystals” (in
Japanese), Kotai Butsuri, 21, 259-273 (1986) (Experimental, 48)
[1987Ben] Bendersky, L.A., Biancaniello, F.S., Schaefer, R.J., “Amorphous Phase Formation in
Al70Si17Fe13 Alloys”, J. Mater. Res., 2, 427-430 (1987) (Experimental, 21)
[1987Cha] Chandrasekaran, M., Liu, Y.P., Vincent, R., Staniek, G., “On a Metastable Rhombohedral
Al-Fe-Si Intermetallic Phase”, Proc. Electron Microsc. Analysis Group Meeting,
Manchester, Sept. (1987), 63-65 (1988) (Crys. Structure, Experimental, 5)
[1987Czi] Cziraki, A., Fogarassy, B., Oszko, A., Szabo, I., Teravaginov, A., Reibold, M., “Effect of
Heat Treatment on the Microstructure of Cast Al-Fe-Si Alloys”, Mater. Sci. Forum, 13-14,
343-350 (1987) (Crys. Structure, Experimental, 5)
[1987Dob] Dobrzynski, L., Giebultowicz, T., Kopcewicz, M., Piotrowski, M., Szymanski, K., “Neutron
and Mössbauer Studies of Fe3-xAlxSi Alloys”, Phys. Status Solidi A, 101A, 567-575 (1987)
(Crys. Structure, Experimental, 24)
[1987For] Fortnum, R.T., Mikkola, D.E., “Effects of Molybdenum, Titanium and Silicon Additions on
the D03 Reversible B2 Transition-Temperature for Alloys near Fe3Al”, Mater. Sci. Eng., 91,
223-231 (1987) (Crys. Structure, Experimental, 37)
[1987Gri1] Griger, A., Lendrai, A., Stefaniay, V., Turmezey, T., “On the Phase Diagrams of the Al-Fe
and Al-Fe-Si Systems”, Mater. Sci. Forum, 13/14, 331-336 (1987) (Equi. Diagram,
Experimental, 9)
[1987Gri2] Griger, A., “Powder Data for the H Intermetallic Phases with Slight Variation in
Composition in the System Al-Fe-Si”, Powder Diffr., 2, 31-35 (1987) (Crys. Structure,
Experimental, *, 21)
[1987Liu] Liu, P., Dunlop, G.L., “Determination of the Crystal Symmetry of Two Al-Fe-Si Phases by
Convergent-Beam Electron Diffraction”, J. Appl. Crystallogr., 20, 425-427 (1987) (Crys.
Structure, Experimental, 13)
[1987Nag] Nagy, S., Homonnay, Z., Vertes, A., Murgas, L., “Mössbauer Investigation of Iron in
Aluminium. II. Al-Fe-Si Samples”, Acta Metall., 35, 741-746 (1987) (Experimental, 2)
376
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1987Pri] Prince, A., “Comment on Intermetallic Phases in the Al-side of the AlFeSi-Alloy System”,
J. Mater. Sci. Lett., 6, 1364 (1987) (Equi. Diagram, Theory, #, 1)
[1987Skj1] Skjerpe, P., “Intermetallic Phases Formed during DC-Casting of an Al-0.25 wt.% Fe-0.13
wt.% Si Alloy”, Metall. Trans. A, 18A, 189-200 (1987) (Crys. Structure, Experimental, 35)
[1987Skj2] Skjerpe, P., Gjonnes, J., “Solidification Structure and Primary Al-Fe-Si Particles in
Direct-Chilled-Cast Aluminum Alloys”, Ultramicroscopy, 22, 239-250 (1987) (Crys.
Structure, Experimental, 21)
[1987Skj3] Skjerpe, P., “An Electron Microscopy Study on the Phase Al3Fe”, J. Microsc., 148, 33-50
(1987) (Crys. Structure, Experimental, Theory, 12)
[1987Ste] Stefaniay, V., Griger, A., Turmezey, T., “Intermetallic Phases in the Aluminum-Side Corner
of the AlFeSi-Alloy System”, J. Mater. Sci., 22, 539-546 (1987) (Crys. Structure, Equi.
Diagram, Experimental, #, *, 13)
[1987Tur] Turmezey, T., “AlFe and AlFeSi Intermetallic Phases in Aluminum Alloys”, Mater. Sci.
Forum, 13/14, 121-132 (1987) (Crys. Structure, Experimental, 12)
[1988Ben1] Bendersky, L., “Rapidly Solidified Al-Fe-Si Alloys”, Mater. Sci. Eng., 98, 213-216 (1988)
(Crys. Structure, Experimental, 9)
[1988Ben2] Bendersky, L.A., McAlisetr, A.J., Biancaniello, F.S., “Phase Transformation during
Annealing of Rapidly Solidified Al-Rich Al-Fe-Si Alloys”, Metall. Trans. A, 19A,
2893-2900 (1988) (Crys. Structure, Experimental, 29)
[1988Cha] Chandrasekaran, M., Lin, Y.P., Vincent, R., Staniek, G., “The Structure and Stability of
Some Intermetallic Phases in Rapidly Solidified Al-Fe”, Scr. Metall., 22, 797-802 (1988)
(Crys. Structure, Experimental, 9)
[1988Dor] Dorofeyeva, Ye.A., Sasnin, Y.V., Stolokotniy, V.L., “Cross-Relaxation of Magnetic
Permeability in Alloy FeSiAl”, Phys. Met. Metallogr., 65(3), 172-174 (1988)
(Experimental, 2).
[1988Liu1] Liu, P., Dunlop, G.L., “Long-range Ordering of Vacancies of BCC -AlFeSi”, J. Mater.
Sci., 23, 1419-1424 (1988) (Crys. Structure, Experimental, 20)
[1988Liu2] Liu, P., Dunlop, G.L., “Crystallographic Orientation Relationships for Al-Fe and Al-Fe-Si
Precipitates in Aluminum”, Acta Metall., 36, 1481-1489 (1988) (Crys. Structure,
Experimental, 20)
[1988Ray] Raynor, G.V., Rivlin, V.G., “Al-Fe-Si”, in “Phase Equilibria in Iron Ternary Alloys”,
122-139 (1988) (Equi. Diagram, 39)
[1988Zak] Zakharov, A.M., Gul´man, I.T., Arnol´d, A.A., Matsenko, Yu.A., “Phase Diagram of the
Aluminium-Silicon-Iron System in the Concentration Range of 10-14% Si and 0-3% Fe”,
Russ. Metall., (3), 177-180 (1988) (Equi. Diagram, Experimental, #, *, 8)
[1989Bon] Bonnet, M., Rogez, J., Castanet, R., “EMF Investigation of Al-Si, Al-Fe-Si and Al-Ni-Si
Liquid Alloys“, Thermochim. Acta, 155, 39-56 (1989) (Experimental, Thermodyn., 15)
[1989Tib] Tibballs, J.E., “Al-Si Substitution in Al(FeMn)Si Phases”, Mater. Sci. Forum, (1989) (23)
[1989Ger1] German, N.V., Bel`skii, V.K., Yanson, T.I., Zarechnyuk, O.S., “Crystal Structure of the
Compound Fe1.7Al4Si”, Sov. Phys. Crystallogr., 34(3), 437-438 (1989) (Crys. Structure,
Experimental, 5)
[1989Ger2] German, N.V., Zavodnik, V.E., Yanson, T.I., Zarechnyuk, O.S., “Crystal Structure of
FeAl2Si”, Sov. Phys. Crystallogr., 34(3), 439-440 (1989) (Crys. Structure, Experimental, 5)
[1991Don] Dons, A.L., “Simulation of Solidification a Short Cut to a Better Phase Diadram
Al-Mg-Fe-Si Alloys”, Z. Metallkd., 82(9), 684-688 (1991) (Calculation, Equi. Diagram,
Experimental, Thermodyn., 17)
[1991Fuk] Fukaya, M., Miyazaki, T., Kozakai, T., “Phase Diagrams Calculated for Fe-rich Fe-Si-Co
and Fe-Si-Al Ordering Systems”, J. Mater. Sci., 26(2), 5420-5426 (1991) (Calculation,
Equi. Diagram, 42)
[1991Lan] Langsrud, Y., “The Use of Phase Diagrams for Calculating Solidification Paths”, “User
Aspects of Phase Diagrams”, Proc. Conf., Hayes, F.H. (Ed.), The Inst. of Metals, 1991,
90-100 (Publ. 1991) (Theory, 7)
377
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1992Gho] Ghosh, G., “Aluminium-Iron-Silicon”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.14596.1.20, (1992) (Crys. Structure, Equi. Diagram,
Assessment, 134)
[1992Zak] Zakharov, A.M., Guldin, I.T., Arnold, A.A., Matsenko, Yu.A., “Phase Equilibria in
Multicomponent Aluminum Systems with Copper, Iron, Silicon, Manganese and Titanium”,
Metalloved. Obrab. Tsv. Splavov, RAN. Inst. Metallurgii. M, 6-17 (1992) (Experimental,
Equi. Diagram, 14)
[1993Car] Carpenter, G.J.C., Le Page, Y., “Revised Cell Data for the -FeSiAl Phase in Aluminum
Alloys”, Scr. Metall. Mater., 28, 733-736 (1993) (Crys. Structure, Experimental, 6)
[1993Sch] Schroeer, W., Hartig, C., Mecking, H., “Plasticity of D03-ordered Fe-Al and Fe-Al-Si
Single-Crystals”, Z. Metallkd., 84(5), 294-300 (1993) (Equi. Diagram, Experimental, 30)
[1994Ang] Anglezio, J.C., Servant, C., Ansara, I., “Contribution to the Experimental and
Thermodynamic Assessment of the Al-Ca-Fe-Si System - I. Al-Ca-Fe, Al-Ca-Si, Al-Fe-Si
and Ca-Fe-Si Systems”, Calphad, 18(3), 273-309 (1994) (Calculation, Equi. Diagram,
Thermodyn., 71)
[1994Koz] Kozakai, T., Miyazaki, T., “Experimental and Theoretical Investigations on Phase Diagrams
of Fe Base Ternary Ordering Alloys”, ISIJ Int., 34(5), 373-383 (1994) (Calculation, Equi.
Diagram, Magn. Prop., 18)
[1994Mur] Murali, S., Guru Row, T.N., Sastry, D.H., Raman, K.S., Murthy, K.S.S., “Crystal Structure
of -FeSiAl5 and (Be-Fe)-BeSiFe2Al8 Phases”, Scr. Metall. Mater., 31(3), 267-271 (1994)
(Experimental, 13)
[1994Rag] Raghavan, V., “The Al-Fe-Si System”, J. Phase Equilib., 15(4), 414-416 (1994) (Equi.
Diagram, Review, 27)
[1994Rom] Romming, Chr., Hansen, V., Gjonnes, J., “Crystal Structure Of Beta-Al4.5FeSi”, Acta
Crystallogr., Sect. B: Struct. Crystallogr. Crys. Chem., B50(3), 307-312 (1994) (Crys.
Structure, Experimental, 10)
[1995Bel] Belov, N.A., “Analysis of Nonequilibrium Solidification of Subeutectic Sillumines Using
Multicomponent Phase Diagrams”, Russ. Metall. (Engl. Transl.), (1), 41-47 (1995) (Equi.
Diagram, Experimental, 5)
[1995Gue1] Gueneau, C., “FeAl3Si2”, Acta Crystallogr., Sect. C: Cryst. Struct. Commun., C51, 177-179
(1995) (Crys. Structure, Experimental, 9)
[1995Gue2] Gueneau, C., Servant, C., “Fe2Al3Si3”, Acta Crystallogr., Sect. C: Cryst. Struct. Commun.,
C51, 2461-2464 (1995) (Crys. Structure, Experimental, 8)
[1995Gue3] Gueneau, C., Servant, C., Ansara, I., “Experimental and Thermodynamic Assessments of
Substitutions in the AlFeSi, FeMnSi, FeSiZr and AlCaFeSi Systems”, “Appl. Thermodyn.
Synth. Procee. Mater.”, Proc. Symp., Nash, P., Sundman, B. (Eds.), The Minerals, Metals
and Materials Society, Warrendale, Pa, 303-317 (1995) (Expermental, Theory, 19)
[1996All] Allen, C.M., O’Reilly, K.A.Q., Cantor, B., Evans, P.V., “Nucleation of Phases in Al-Fe-Si
Alloys”, Mater. Sci. Forum, 217-222, 679-684 (1996) (Calculation, Equi. Diagram, 14)
[1996Cho] Choi, Y., Ra, H., “Microstructure of Gas Atomized Al-Fe-Si Alloy Powders” (in Korean),
J. Korean Inst. Met., 34(2), 230-235 (1996) (Experimental, 11)
[1996Fri] Friemelt, K., Ditusa, J.F., Bucher, E., Aeppli, G., “Coulomb Interactions in Al Doped FeSi
at Low Temperatures”, Ann. Phys., Leipzig, 5(2), 175-183 (1996) (Crys. Structure,
Experimental, 25)
[1996Mor] Morris, D.G., Gunther, S., “Order-Disorder Changes in Fe3Al Based Alloys and the
Development of an Iron-Base - `` Superalloy”, Acta Mater., 44(7), 2847-2859 (1996)
(Crys. Structure, Equi. Diagram, Experimental, 23)
[1996Mul] Mulazimoglu, M.H., Zaluska, A., Gruzleski, J.E., Parray, F., “Electron Microscopy Study of
Al-Fe-Si Intermetallics in 6021 Aluminum Alloys”, Metall. Mater. Trans. A, 27A, 929-936
(1996) (Crys. Structure, Experimental, 48)
378
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1996Mur] Murali, S., Raman, K.S., Murthy, K.S.S., “Al-7Si-0.3Mg Cast Alloy: Formation and Crystal
Structure of -FeSiAl5 and (Be-Fe)-BeSiFe2Al8 Phases”, Mater. Sci. Forum, 217-222,
207-212 (1996) (Crys. Structure, Experimental, 8)
[1996Szy] Szymanski, K., Baas, J., Dobrzynski, L., Satula, D., “Magnetic and Mössbauer Investigation
of FeSi2-xAlx”, Physica B (Amsterdam), 225, 111-120 (1996) (Crys. Structure,
Experimental, 20)
[1996Yan] Yanson, T.I., Manyako, M.B., Bodak, O.I., German, N.V., Zarechnyuk, O.S., Cerny, R.,
Pacheko, J.V., Yvon, K., “Triclinic Fe3Al2Si3 and Orthorhombic Fe3Al2Si4 with New
Structure Types”, Acta Crystallogr., Sect. C: Cryst. Struct. Commun., C52, 2964-2967
(1996) (Crys. Structure, Experimental, 15)
[1997All] Allen, C.M., O`Reilly, K.A.Q., Cantor, B., Evans, P.V., “Heterogeneous Nucleation of
Solidification of Equilibrium and Metastable Phases in Melt-Spun Al-Fe-Si Alloys”, Mater.
Sci. Eng. A, A226-A228, 784-788 (1997) (Experimental, Phys. Prop., 10)
[1997Can] Cantor, B., “Impurity Effects on Heterogenous Nucleation”, Mater. Sci. Eng. A,
A226-A228, 151-156 (1997) (Crys. Structure, Experimental, 38)
[1997Sto] Stone, I.C., Jones, H., “Effect of Cooling Rate and Front Velosity on Solidification
Microstructure Selection in Al-3.5 wt.% Fe-0 to 8.5 wt.% Si Alloys”, Mater. Sci. Eng. A,
A226-A228, 33-37 (1997) (Equi. Diagram, Experimental, 10)
[1997Vyb] Vybornov, M., Rogl, P., Sommer, F., “The Thermodynamic Stability and Solid Solution
Behavior of the Phases 5-Fe2Al7.4Si and 6-Fe2Al9Si2”, J. Alloys Compd., 247, 154-157
(1997) (Crys. Structure, Equi. Diagram, Experimental, Review, 7)
[1998Akd] Akdeniz, M.V., Mekhrabon, A.O., “The Effect of Substitutional Impurities on the Evolution
of Fe-Al Diffusion Layer”, Acta Mater., 46(4), 1185-1192 (1998) (Calculation,
Thermodyn., 55)
[1998Dit] Ditusa, J.F., Friemelt, K., Bucher, E., Aeppli, G., Ramirez, A.P., “Heavy Fermion
Metal-Kondo Insulator Transition in FeSi1-xAlx”, Phys. Rev. B, B58(16), 10288-10301
(1998) (Crys. Structure, Experimental, 62)
[1998Kol] Kolby, P., “System Al-Fe-Si”, in “COST 507, Thermochemical Database for Light Metal
Alloys”, Vol. 2, Ansara, I., Dinsdale, A.T., Rand, M.H. (Eds), Office for official publications
of the European Communities, Luxembourg, 319-321 (1998) (Assessment, Thermodyn.)
[1999Cho] Choi, Y.S., Lee, L.S., Kim, W.T., Ra, H.Y., “Solidification Behavior of Al-Si-Fe Alloys and
Phase Transformation of Metastable Intermetallic Compound by Heat Treatment”, J. Mater.
Sci., 34(9), 2163-2168 (1999) (Equi. Diagram, Experimental, 14)
[1999Liu] Liu, Z.-K., Chang, A., “Thermodynamic Assessment of the Al-Fe-Si System”, Metall.
Mater. Trans. A., 30A(7), 1081-1095 (1999) (Calculation, Thermodyn., 56)
[1999Mek] Mekhrabov, A.O., Akdeniz, M.V., “Effect of Ternary Alloying Elements Addition on
Atomic Ordering Characteristics of Fe-Al Intermetallics”, Acta Mater., 47(7), 2067-2075
(1999) (Calculation, Theory, Thermodyn., 63)
[1999Oht] Ohta, Y., Miura, S., Mishima, Y., “Thermoelectric Semiconductor Iron Disilicides Produced
by Sintering Elemental Powders”, Intermetallics, 7, 1203-1210 (1999) (Equi. Diagram,
Experimental, Thermal Conduct., 19)
[1999Tay] Taylor, J.A., Schaffer, G.B., St. John, D.H., “The Role of Iron in the Formation of Porosity
in Al-Si-Cu-Based Casting Alloys: Part II. A Phase-Diagram Approach”, Metall. Mater.
Trans. A, 30A, 1651-1655 (1999) (Calculation, Crys. Structure, Experimental, 12)
[2000Bha] Bhattamishra, A.K., Chattoraj, I., Basu, D.K., De, P.K., “Study on the Influence of the Si/Fe
Ratio on the Corrosion Behavior of Some Al-Fe-Si Alloys”, Z. Metallkd., 91(5), 393-396
(2000) (Corrosion, Experimental, 23)
[2000Dut] Dutta, B., Rettnmayr, M., “Effect of Coolig Rate on the Solidification Behavior of Al-Fe-Si
Alloys”, Mater. Sci. Eng. A, A283, 218-224 (2000) (Equi. Diagram, Experimental, 23)
[2000Li1] Li, Y., Ochin, P., Quivy, A., Telolahy, P., Legendre, B., “Enthalpy of Formation of Al-Fe-Si
Alloys ( 5, 10, 1, 9)”, J. Alloys Compd., 298, 198-202 (2000) (Experimental,
Thermodyn., 20)
379
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[2000Li2] Li, Y., Legendre, B., “Enthalpy of Formation of Al-Fe-Si Alloys II ( 6, 2, 3, 8, 4)”,
J. Alloys Compd., 302, 187-191 (2000) (Experimental, Thermodyn., 21)
[2000Sri] Sritharan, T., Murali, S., Hing, P., “Synthesis of Aluminium-Iron-Silicon Intermetallics by
Reaction of Elemental Powders”, Mater. Sci. Eng. A, A286, 209-217 (2000) (Crys.
Structure, Experimental, 18)
[2000Zhe] Zheng, J.G., Vincent, R., Steeds, J.W., “Crystal Structure of an Orthorhombic Phase in
beta-(Al-Fe-Si) Precipitates Determined by Convergent-Beam Electron Diffraction”,
Philos. Mag. A, A80(2), 493-500 (2000) (Crys. Structure, Experimental, 11)
[2001Cho] Cho, H.S., Kim, K.S., Jeong, H.G., Yamagata, H., “Microstructure and Mechanical
Properties of Extruded Rapidly Solidified Al-16Si-5Fe Based Alloys”, Key Eng. Mater.,
189-191, 479-483 (2001) (Experimental, Mechan. Prop., 5)
[2001Hsu] Hsu, G., O´Reilly, K.A.Q., Cantor, B., Hamerton, R., “Non-Equilibrium Reactions in 6xxx
Series Al Alloys”, Mater. Sci. Eng. A, A304-A306, 119-124 (2001) (Equi. Diagram,
Experimental, 14)
[2001Jha] Jha, R., Haworth, C.W., Argent, B.B., “The Formation of Diffusian Coatings on Some
Low-Alloy Steels and Their High Temperature Oxidation Behavior: Part 1 Diffusion
Coatings”, Calphad, 25(4), 651-665 (2001) (Calculation, Equi. Diagram, 9)
[2001Kre] Krendelsberger N., “Constitution of the Systems Aluminium-Manganese-Silicon,
Aluminium-Iron-Silicon, und Aluminium-Iron-Manganese-Silicon”, Tezisy Inst. Phys.
Chem. Univ., Vienna, 2001 (Crys. Structure, Equi. Diagram, Experimental, #, *, 83)
[2001Sha] Sha, G., O´Reilly, K., Cantor, B., Worth, J., Hamerton, R., “Growth Related Metastable
Phase Selection in a 6xxx Series Wrought Al Alloy”, Mater. Sci. Eng. A, A304-A306,
612-616 (2001) (Crys. Structure, Equi. Diagram, Experimental, 9)
[2002Mer] Meredith, M.W., Worth, J., Hamerton, R.G., “Intermetallic Phase Selection During
Solidification of Al-Fe-Si(-Mg) Alloys”, Mater. Sci. Forum, 396-402, 107-112 (2002)
(Equi. Diagram, Experimental, 9)
[2002Rag] Raghavan, V., “Al-Fe-Si (Aluminium-Iron-Silicon)”, J. Phase Equilib., 25(4), 107-112
(2002) (Equi. Diagram, Review, 24)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Assessment, Crys. Structure, 58)
[2003Luk] Lukas, H.L., “Al-Si (Aluminum-Silicon)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Assessment, Equi. Diagram, Crys. Structure, 29)
Table 1: Chronological Survey of Ternary Phases in the Al-Fe-Si System
Author Phase Designation Composition (mass%)Comments
Fe Al Si
[1927Gwy] , , , - - - Ternary alloys up to ~20%Fe and 30%Si
(mass%) were studied. The -phase reported to
be solid solution of Fe, Al and Si.
[1928Dix] (Fe-Si)
(Fe-Si)
30.0
27.0
62.0
68.0
8.0
15.0
Ternary alloys up to 41%Fe and 29%Si(mass%)
were studied using pure Al(99.95%).Annealing:
1-5 weeks at 560°C. These two crystal species
were reported to be ternary solid solutions
rather than ternary compounds. Reported to
form a part-section with Fe4Al13 and (Fe-Si).
[1931Fin] (Fe-Si)
(Fe-Si)
30.3
27.3
61.4
57.7
8.3
15.0
Alloys and heat treatments were same as
[1928Dix]. They assumed (Fe-Si) was a solid
solution of Si in Fe4Al13.
[1931Fus] Fe2Al6Si3 31.3 45.2 23.5 Fe2Al6Si3 formed by a peritectic reaction.
380
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1932Nis],
[1933Nis]
Fe2Al3Si2P
44.9
-
32.5
-
22.6
-
Fe2Al3Si2 was reported around the composition
Al-32Fe-30Si (mass%). The -phase was not
studied further.
[1935Bos] Fe2Al6Si3 - - -
[1936Jae] FeAl4Si2Hexagonal
Orthorhombic
Triclinic
27.2
-
-
-
47.6
-
-
-
25.2
-
-
-
XRD, goniometric and dilatometric
measurements were carried out in ternary alloys
up to 40%Fe and 30% Si (mass%). The
chemical compositions of the hexagonal
(a=836, c=1458 pm), orthorhombic (a=609,
b=996, c=374 pm) and triclinic (a=688, b=593,
c=432 pm, = 104.75°, =130.67°, =68.4°)
phases were not given. FeAl4Si2 has tetragonal
structure (a=615, c=947 pm).
[1937Ser] FeAlnSi
n = 4
n = 5
FeAl4Si2
29.1
25.6
25.4
56.3
61.6
49.1
14.6
12.8
25.5
Microscopic and XRD were carried out in
alloys up to 10%Fe and 25%Si (mass%). The
densities of FeAl5Si and FeAl4Si2 were
reported to be 3.35 and 3.30 g cm-3,
respectively. FeAl4Si2 was found to have cubic
crystal structure.
[1937Ura] -
-
-
-
-
-
According to these authors and are formed
by peritectic reaction, they have no definite
composition, and are solid solutions.
[1940Tak] K1:Fe3Al3Si2K2:Fe6Al12Si5K3:Fe5Al9Si5K4:FeAl3Si2K5:Fe6Al15Si5K6:FeAl4Si
55.0
41.9
42.2
28.9
38.1
29.1
26.6
40.5
36.7
41.9
46.0
56.3
18.4
17.6
21.1
29.2
15.9
14.6
These authors reported six ternary phases (K1 to
K6) formed by peritectic reactions.
[1943Phi] (Fe-Si)
(Fe-Si)
-
-
-
-
-
-
They investigated ternary alloys up to 12
mass% Fe and 6 mass% Si.
[1950Phr] c-FeAlSi
m-FeAlSi
t-FeAlSi
31.9
27.2-
27.8
-
62.5
59.3-
58.2
-
5.6
13.5-
14.0
-
Alloys up to 42%Fe and 30%Si(mass%) were
studied. c-FeAlSi has cubic (a=1254.83 pm),
m-FeAlSi has monoclinic (a=b=612.23,
c=4148.36 pm, =91°) and t-FeAlSi has
tetragonal (a=612.23, c=947.91 pm) structure.
[1951Pra2] (Fe-Si)
-(Fe-Si)
32.1-
32.7
26.7-
27.3
59.5-
57.0
59.5-
57.8
8.4-
10.3
13.8-
14.9
Chemical analysis and XRD were carried out on
extracted crystals. The crystal structure of
(Fe-Si) was reported to be the same as Fe4Al13
and (Fe-Si) represents a distinct ternary
compound.
[1951Now] (Fe-Si)
(Fe-Si)
(Fe-Si)
(Fe-Si)
30.6
27.2
28.9
-
59.1
59.1
41.9
-
10.3
13.7
29.2
-
150 ternary alloys up to 45%Fe and 30% Si
(mass%) were investigated by thermoanalytical,
microscopic and XRD methods. Homogeneity
ranges of these phases were reported to be
small. Approximate stoichiometries of (Fe-Si),
(Fe-Si), (Fe-Si) can be represented as
Fe1.5Al6Si, FeAl4.5Si, Fe0.5Al1.5Si,
respectively. The latter has tetragonal structure
(a = 495.0, c = 707.0 pm).
Author Phase Designation Composition (mass%)Comments
Fe Al Si
381
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1952Arm]
[1955Arm]1
2
3
27.3
29.2
35.3
65.7
59.5
51.9
7.0
11.3
12.8
Alloys up to 20%Fe and 50% Si (mass%) were
studied. Microscopic, XRD and density
measurements were performed to characterize
the phases in as-cast alloys. The crystal
structures of 1, 2 and 3 were reported to be
cubic (a = 1254.83 pm), hexagonal (a = 496,
c = 702.11 pm) or orthorhombic (a = 4360,
b = 4960, c = 7080 pm) and cubic (a = 1603.23
pm), respectively. The densities were 3.50, 3.58
and 3.65 g cm-3, respectively.
[1953Rob] -FeAlSi 32.5 58.8 8.7 Single crystals of -FeAlSi, prepared by
[1951Pra1] and [1951Pra2] were studied by
X-ray diffraction. The crystal structure and
density were reported to be hexagonal (with
P63/mmc symmetry and a = 1230, c = 2620 pm)
and 3.62±0.02 g cm-3 respectively.
[1954Spi] c-FeAlSi
t-FeAlSi
m-FeAlSi
-
-
-
-
-
-
-
-
-
The crystal structures of c-FeAlSi, t-FeAlSi and
m-FeAlSi were reported to be cubic
(a = 1254.23 pm), tetragonal (a = 612.23,
c = 948.94 pm) and monoclinic (a = b = 612.23,
c = 4148.36 pm, = 91°), respectively. They
correspond to (Fe-Si), (Fe-Si) of [1943Phi]
and of [1927Gwy], respectively.
[1955Bla] Fe2Al9Si2 27.2 59.1 13.7 XRD was carried out on the extracted crystals
of [1951Pra1]. The crystal structure and density
were reported to be tetragonal (with 4/m
symmetry and a = 618±6, c = 4250±50 pm) and
3.50±0.1 g cm-3, respectively.
[1955Obi] (Fe-Si)
(Fe-Si)
30.2-
32.8
23.4-
25.8
58.1-
60.0
57.6-
58.5
11.2-
7.2
19.0-
15.7
(Fe-Si) was obtained in Al-5Fe-(3 to 7)Si
(mass%) which were water quenched after
annealing at 615 to 620°C for 1 h, and (Fe-Si)
was obtained in Al-4Fe-(9 to 13)Si (mass%)
alloys which were f/c cooled after the same heat
treatment. These crystals were extracted from
alloys after subjecting to different heat
treatments and were studied by XRD. The
powder patterns obtained from these two phases
were almost the same as c-FeAlSi and
m-FeAlSi of [1950Phr]. The lattice parameters
of (Fe-Si) and (Fe-Si) were a=1254.8 pm;
and a = b = 612.2, c = 4148.4 pm, and = 91°,
respectively.
[1956Spe] (Mn, Fe)AlSi - - - Found in wrought commercial 2024 alloy.
[1964Lai] FeAl5Si - - - Formed in an Al-1.5 mass% Si alloy plated with
Fe and annealed at 500°C. The ternary phase
was identified by X-ray and electron diffraction
techniques.
Author Phase Designation Composition (mass%)Comments
Fe Al Si
382
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1967Coo] -FeAlSi 31.9 61.7 6.4 XRD study of these crystals yielded cubic
structure with a=1256 pm, 138 atoms/unit cell
and Im3 symmetry. The composition of the
crystals was close to Fe5Al20Si2 and the density
was ~3.59±0.06 g cm-3.
[1967Mun] -CrFeAlSi
-FeAlSi
-FeAlSi
-FeAlSi
-FeAlSi
-
-
-
33.0-
38.0
-
-
-
-
54.0-
43.5
-
-
-
-
13.0-
18.5
-
Alloys containing up to 22 mass% (Fe+Si) were
cooled at 0.75°C/min. The phases were
analyzed by X-ray and electron diffraction. The
crystal structures of -CrFeAlSi, -FeAlSi and
-FeAlSi were reported to be cubic (a=1250 to
1270 pm), hexagonal (a=1230, c=2620 pm) and
C-face-centered monoclinic (a=1780±10,
b=1025±5, c=890±5 pm, =132°), resp. The
"cubic" (a=1603 pm) pattern of 3 of
[1955Arm] was indexed on the basis of this
monoclinic cell. -FeAlSi was reported to be
the same as 2 of [1952Arm].
[1967Sun] 1(FeAlSi)
2(Fe2Al8Si)
3(FeAl3Si)
(FeAl5Si)
(FeAl4Si2)
31.1
30.0-
33.0
34.0-
35.2
25.5-
26.5
25.0-
26.0
60.8
62.6-
56.0
50.4-
47.7
62.4-
58.9
49,0-
47.0
8.1
7.4-
11.0
15.6-
17.1
12.1-
14.6
26.0-
27.0
50 different ternary and quaternary alloys were
analyzed by chemical and X-ray diffraction.
The 1 crystals were reported to contain 1.05
mass% Mn. The crystal structures of 1 and 2
were reported to be cubic (a = 1250±10 pm) and
hexagonal, respectively.
[1969Pan] FeAl3Si2 28.9 41.9 29.2 The alloy was annealed at 800°C for 14 h and
water quenched, and was analyzed by XRD.
The crystal structure was reported to be
tetragonal (a = 607, c = 950 pm) of PdGa5-type,
[1973Kow] Fe2Al9Si2 - - - Found in Al-11.17Si-0.4Fe-0.49Mg-9.8Si and
Al-0.1Fe-0.4Mg-7.5Si-0.1Ti (mass%) alloys.
The extracted crystals were analyzed by XRD
and microprobe analysis. The composition of
the precipitate as given by the authors does not
add up to 100.
[1974Mur],
[1981Zar]
A: Fe15Al57-47Si28-38
B: Fe22Al40Si38
C: Fe32Al38Si30
D: Fe36Al36Si28
E: Fe40Al40Si20
F: Fe25Al60Si15
G: Fe25Al50Si25
K: Fe22Al63-52Si15-36
L: Fe15Al70Si15
M: Fe17Al72Si11
26.5-
27.5
36.4
48.9
53.3
57.7
40.5
40.6
36.7-
36.6
26.6
29.7
40.0-
48.6
32.0
28.1
25.8
27.8
39.1
47.1
50.7-
41.7
60.0
60.7
33.5-
24.9
31.6
23.0
20.9
14.5
20.4
12.3
12.6-
21.7
13.4
9.6
The crystal structures of Fe25Al50Si25,
Fe25Al60Si15 and Fe22Al63-52Si15-36 were
reported to be orthorhombic (a = 768, b = 1530,
c = 1600 pm), hexagonal (a = 752.6, c = 763.2
pm) and monoclinic (a = 420, b = 760, c = 1533
pm, = 89°), respectively. The crystal
structures of other phases were not reported.
The A-phase has hexagonal crystal structure
with lattice parameters varying from
a = 630±0.5, c = 941±0.7 pm at Fe15Al57Si28 to
a = 612±0.5, c = 953±0.7 pm at Fe15Al47Si38.
In the as-cast samples, the F-phase has
hexagonal structure, but its structure is different
after annealing at 600°C.
Author Phase Designation Composition (mass%)Comments
Fe Al Si
383
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1975Bar] FeAl5Si
Fe2Al8Si
25.0
31.0
62.0
61.0
13.0
8.0
These two phases were found in
Al-Fe-Mn-Mg-Si alloys. The crystal structures
of FeAl5Si and Fe2Al8Si were reported to be
monoclinic (a = b = 612, c = 4150 pm, = 91°)
and hexagonal (with P63/mmc symmetry and
a = 1230, c = 2630 pm), respectively.
[1977Cor] -(FeAlSi) 32.5 58.8 8.7 The extracted crystal of [1951Pra2] were
analyzed by X-ray diffraction using Mo-K ,
Fe-K and Cu-K radiations. The crystal
structure was reported to be hexagonal
(a = 1240.4±0.1, c = 2623.4±0.2 pm) with 44.9
atoms of Fe, 167.8 atoms of Al and 23.9 atoms
of Si and the density was reported to be
3.665 g cm-3.
[1977Hoi] -FeAlSi
'-FeAlSi
-
-
-
-
-
-
Found in an Al-0.2 mass% Fe-0.55 mass%
Mg-0.6 mass% Si alloy. -FeAlSi was present
in as-cast alloy and it transforms to '-FeAlSi
upon annealing at 580°C for 1 h. The crystal
structures of -FeAlSi and '-FeAlSi were
reported to be monoclinic (a=b=618, c=2080
pm, =91°) and hexagonal (a=1230, c=2630
pm), respectively.
[1977Sim] '-Fe5Al20Si2-Fe2Al8Si
Unknown phase
-
-
34.1
-
-
65.5
-
-
<0.5
Found in strip cast Al-0.5 mass% Fe-0.2 mass%
Si alloy. The precipitates were characterized by
TEM with EDAX analyzer. The crystal
structures of '-Fe5Al20Si2, -Fe2Al8Si and the
unknown phases were cubic (a = 1260 pm),
hexagonal and monoclinic (a = 869±6, b =
635±2, c = 632±6 pm, = 93.4°±0.5°,
isomorphous with Al9Co2), respectively.
[1979Mor] 2-FeAlSi
-FeAlSi
30.0-
33.0
25.0-
30.0
64.0-
55.0
63.0-
55.0
6.0-1
2.0
12.0-
15.0
About 80 extracted particles from the
homogenized commercial 6063 aluminium
alloy were analyzed by EDAX. The size and
Fe/Si ratio in 2-FeAlSi were found to be 3 m
and 2.75 to 5.5, respectively. Similar figures for
the -FeAlSi were 8 m and 1.6 to 2.25.
[1982Wes] '-FeAlSi
"-FeAlSi
-
-
-
-
-
-
Found in direct-chilled cast commercial purity
Al-Fe-Si alloys. The precipitates were
characterized by TEM/STEM and EDAX
analyzer. The crystal structures of '-FeAlSi
and "-FeAlSi were found to be monoclinic
(a = 890, b = 490, c = 4160 pm, = 92°) and
tetragonal (a = 1260, c = 3720 pm),
respectively. The Fe/Si ratio in ' was almost
unity and that in " was between 7 and 9.
Author Phase Designation Composition (mass%)Comments
Fe Al Si
384
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1984Don] v-FeAlSi
(Fe3Al12.4-14.6Si1.0-2.1)
31.6-
27.0
63.1-
63.5
5.3-
9.5
Found in direct-chill cast as well as heat treated
(400 to 600°C) three industrial cast alloys.
Electrical resistivity and TEM/EDAX were
performed to characterize the phases. The
crystal structure was reported to be monoclinic
(a = 847, b = 635, c = 610 pm, = 93.4°).
[1985Don1] T-FeAlSi
(Fe3Al13Si1.0-1.5)
-FeAlSi
(Fe3Al13Si1.0-2.0)
30.6-
29.9
29.2-
30.7
64.2-
62.6
61.0-
64.2
5.2-
7.5
9.8-
5.1
Found in both strip cast and direct-chill cast of
10 commercial Al-alloys which were heat
treated between 400 to 600°C. The precipitates
were analyzed by TEM and the crystal
structures of T-FeAlSi and -FeAlSi reported
to be c-centered monoclinic (a = 2810, b =
3080, c = 2080 pm, = 97.74°) and bcc (a =
1250 pm).
[1985Don2] -FeAlSi
'-FeAlSi
-FeAlSi
v-FeAlSi
T-FeAlSi
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
Found in a number of strip cast alloys in the
range of Al-(0.21 to 2.98) mass% Fe-(0.06 to
1.16) mass% Si, and also after heat treatment at
450°C for 1 week.
[1985Gri] - 31.5 60.7 7.8 Found in as-cast and heat treated Al-(17 to 35)
mass% Fe (4 to 14) mass% Si alloy. The
precipitates were characterized by X-ray
diffraction and EDAX analysis.
[1985Liu],
[1986Liu1],
[1986Liu2],
[1987Liu],
[1988Liu1],
[1988Liu2]
-FeAlSi
1-FeAlSi
2-FeAlSi
25.0
25.8
27.8
69.7
70.5
68.8
5.3
3.7
3.4
Dilute Al-Fe-Si alloys with Fe/Si mass ratios of
2 and 4 were studied. Formation of the
precipitates was reported to be a function of
Fe/Si ratio, alloy purity, solidification rate and
alloy heat treatment. The composition and the
crystal structures of the phases were analyzed
by EDAX and STEM. The crystal structures of
-FeAlSi, 1-FeAlSi and 2-FeAlSi were found
to be bcc (a = 1256 pm), c-centered
orthorhombic (with Cmmm symmetry and a =
1270, b = 3620, c = 1270 pm) and monoclinic
(with Pm symmetry and a = 1250, b = 1230, c =
1930 pm, = 109°), respectively. In the
commercial alloy with Fe/Si ratio of 2,
1-FeAlSi transformed to 2-FeAlSi upon
annealing at 600°C. But in a high purity alloy
with Fe/Si ratio of 2, neither 1 nor 2-FeAlSi
formed, and -FeAlSi persisted even after
prolonged annealing at 600°C.
[1985Suz] -FeAlSi
-FeAlSi
32.0
27.0
60.0
59.0
8.0
14.0
The and crystals were extracted from Al-4
mass% Fe-5 mass% Si and Al-4 mass% Fe-10
mass% Si ingots, respectively, which were heat
treated at 590 to 640°C for 1 h. The precipitates
were characterized by EPMA, X-ray diffraction
and Mössbauer spectroscopy.
Author Phase Designation Composition (mass%)Comments
Fe Al Si
385
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1986Dun] -FeAlSi
-FeAlSi
-
-
-
-
-
-
The and phases were observed after
complete crystallization of an Fe14Al74Si12
amorphous alloy obtained by melt-spinning
(cooling rate: ~1.5 106 °C/s).
[1987Cha],
[1988Cha]
- 27.0-
19.0
73.0-
78.0
0.0-
3.0
Found in Al-6 mass% Fe alloy which was
atomized and extruded at 400°C. The crystal
structure of the metastable phase was reported
to be rhombohedral (with R3c or R3c symmetry,
a = 890 pm, = 111.8°) or hexagonal (a =
1470, c = 780 pm). The above phase was not
present after a heat treatment at 450°C for 54 h.
[1987Czi] -FeAlSi
‘-FeAlSi
-FeAlSi
-
-
-
-
-
-
-
-
-
Investigated microstructures of direct-chill cast
and heat treated alloys: Al-0.58 mass% Fe-0.28
mass% Si and Al-0.54 mass% Fe-0.95 mass%
Si. The as-cast microstructure of first alloy
contains - and '-AlFeSi precipitates having
hexagonal and cubic structure, respectively. The
as-cast microstructure of first alloy contains
-AlFeSi precipitates. Isothermal heat treatment
at 350, 400, 450, 530 and 600°C resulted in the
formation of Fe4Al13 and FeAl6 precipitates.
[1987Gri2] H-FeAlSi 33.5 58.5 8.0 Alloys close to the composition of Fe2Al8Si
were prepared and annealed at 600°C for 1
month. X-ray powder diffraction and EPMA
were used to characterize the phase. The
hexagonal structure (a = 1240.56±0.7, c =
2623.6±0.2 pm and P6c/mmc symmetry) was
confirmed. The details of the powder diffraction
data were also presented.
[1987Nag] C-FeAlSi
H-FeAlSi
-
-
-
-
-
-
A number of ternary alloys in direct-chill cast
state and heat treated (450 to 620°C) were
investigated by means of X-ray diffraction,
EPMA and Mössbauer spectroscopy.
C-FeAlSi was reported to be metastable and
decomposes into Fe4Al13 and Si, which in turn
react to form H-FeAlSi.
[1987Skj1] "-FeAlSi 30.9-
32.5
65.4-
63.3
3.7-
4.2
Found in direct-chill casting of Al-0.25 mass%
Fe-0.13 mass% Si alloy. The precipitates were
analyzed by EDAX, TEM and HREM. The
crystal structure was reported to be c-centered
orthorhombic (a=1300, b=3600, c=1260 pm).
[1987Ste] -FeAlSi
-FeAlSi
-FeAlSi
2-FeAlSi
28.0-
36.0
25.0-
28.0
31.0-
37.0
40.0-
42.0
66.0-
51.0
62.0-
56.0
60.0-
45.0
48.0-
42.0
6.0-
13.0
13.0-
16.0
9.0-
18.0
12.0-
16.0
Alloys up to 20 to 35 mass% Fe and 4 to 14
mass% Si were investigated. As-cast alloys
were reported to contain some non-equilibrium
phases. The compositions of the ternary phases
were found to depend on the heat treatment. The
precipitates were analyzed by means of X-ray
diffraction and electron probe microanalysis.
Author Phase Designation Composition (mass%)Comments
Fe Al Si
386
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
[1987Tur] -FeAlSi
C-FeAlSi
Hexagonal
Rhombohedral
-
-
-
-
-
-
-
-
-
-
-
-
-FeAlSi (having cubic structure) formed in an
Al-0.5 mass% Fe-1 mass% Si alloy, whereas
C-FeAlSi, hexagonal and rhombohedral
phases formed in an Al-0.5 mass% Fe-0.2
mass% Si alloy. The lattice parameters of latter
three phases were a = 1256 pm; a = 1776, c =
1088 pm; a = 2082 pm and = 95.2°,
respectively.
[1988Ben2] -FeAlSi
'-FeAlSi
''-FeAlSi
-
-
-
-
-
-
Decomposition of rapidly solidified Al-(10 to
14) mass% Fe-2 mass% Si alloys were
investigated by TEM. -FeAlSi forms from an
amorphous phase at 380°C and was reported to
be metastable and decomposes into '-FeAlSi
and "-FeAlSi superlattices above 430°C. The
crystal structures of -FeAlSi, '-FeAlSi and
"-FeAlSi were reported to be cubic (a = 1250
pm), rhombohedral (with R3 symmetry and a
= 2080, = 95.2°) or c-hexagonal (a = 2080, c
= 3260 pm) and trigonal (with P3 symmetry and
a = 1776, c = 1088 pm), respectively.
[1988Zak] -FeAl5Si
-FeAl4Si2
25.9-
26.6
25.9-
27.8
61.3-
60.1
48.8-
45.8
12.8-
13.3
25.3-
26.4
-FeAl5Si has monoclinic structure and
-Fe4Si2 has tetragonal structures and their
densities are 3.61 and 3.36 g cm-3, respectively.
[1993Car] -Fe3Al10Si2 - - - -Fe3Al10Si2 has B-face centered orthorhombic
structure with lattice parameters a = 618.4, b =
625, c = 2069 pm. The approximate
composition corresponds to the EDS data.
However, based on the density data of
[1950Phr] and measured unit cell volume, the
proposed formula is Fe2Al5Si
[1994Mur]
[1996Mur]
-FeAl5Si 19.5-
26.8
57.3-
67.9
12.5-
15.8
Observed in Al-7Si-0.3Mg-0.6Fe,
Al-7Si-0.3Mg-0.8Fe,
Al-7Si-0.3Mg-0.64Fe-0.27Be and
Al-7Si-0.3Mg-1Fe-0.26Be (mass%) alloys.
The density of -phase is 3.29 g cm-3.
[1996Mul] -Fe2Al8Si
-FeAl5Si
31.7
25.1
60.0
61.9
8.3
13.0
The and phases were observed in an Al-0.29
mass% Fe-0.58 mass% Si-0.58 mass% Mg
alloy. -Fe2Al8Si forms by L
(Al) + -Fe2Al8Si, and -FeAl5Si forms by
L+ -Fe2Al8Si (Al)+ -FeAl5Si. -Fe2Al8Si
is cubic with a = 1250 pm, and -FeAl5Si is
monoclinic with lattice parameters a = b = 612
pm, c = 4150 pm and = 91°.
[1999Cho] -FeAl4Si2 25.9- 61.3- Observed in Al-8 mass% Fe-20 mass% Si and
Al-5 mass% Fe-30 mass% Si alloys, cooled at
about 10°C/min. -FeAl4Si2 has tetragonal
structure, and it transforms to equilibrium
Fe2Al9Si2 phase at 500°C.
Author Phase Designation Composition (mass%)Comments
Fe Al Si
387
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Table 2: Crystallographic Data of Solid Phases
[2000Sri] -Fe2Al8Si
'-(Fe,Al,Si)
-FeAl5Si
-FeAl3Si
-FeAl9Si3FeAl4Si2
31.6
32.1
27.2
33.0-
38.0
15.0
25.4
60.6
52.9
59.3
44.0-
54.0
65.0
49.1
7.8
8.7
13.3
13.0-
18.0
20.0
25.5
Bulk intermetallics prepared from elemental
powders by self-propagating high temperature
synthesis. However, only -Fe2Al8Si and
FeAl4Si2 were single phase.
[2000Zhe] -(Fe-Al-Si) - - - Observed in Al-7Si-0.3Mg-0.6Fe (mass%) alloy
prepared by [1996Mur]. They found that
-FeAl5Si is actually a multiphase composite.
An A-centered orthorhombic phase (space
group Cmcm, #63) with a=618, b=620 and
c=2080 pm was observed.
[2001Hsu] C-FeAlSi - - - Observed in a model 6xxx alloy containing 0.3
mass% Fe, 0.6 mass% Si and 0.8 mass% Mg.
Cubic C-FeAlSi may form by L+Fe4Al13
(Al)+ C-FeAlSi and L (Al)+ C-FeAlSi. The
atomic ratio Al:Fe:Si in C-FeAlSi may vary
from 7:4:1 to 9:5:1.
[2001Kre] 1/ 9: Fe3(Al0.4Si0.6)5
2: Fe2(Al1-xSix)7
0.2 < x < 0.33
3: FeAl2.25Si0.75
4: FeAl3Si2
5: Fe2Al7.4Si
6: FeAl4.5Si
7: FeAl1.5Si1.5
8: FeAl0.67Si1.33
10: Fe5Al12Si3
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
-
All ternary phases exist at 550°C. Previously
reported 1 and 9 [1992Gho] are established as
one phase with large homogeneity range.
[2001Sha] -FeAlSi
-FeAlSi
-
-
-
-
-
-
Observed in a model 6xxx alloy containing 0.3
mass% Fe, 0.6 mass% Si and 0.8 mass% Mg.
-FeAlSi may be simple cubic with a = 1252
pm, or bcc with a = 1256 pm. -FeAlSi is
monoclinic. They may form by the following
reactions: L+Fe4Al13 (Al)+ -FeAlSi, L (Al)+
-FeAlSi, and L+ -FeAlSi (Al)+ -FeAlSi.
-FeAlSi is metastable.
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
(Al)
660.452
cF4
Fm3m
Cu
a = 404.88 pure Al at 24°C [V-C]
( Fe)
1538
cI2
Im3m
W
a = 286.65 pure Fe at 20°C [V-C]
Author Phase Designation Composition (mass%)Comments
Fe Al Si
388
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
(Si)
1414
cF8
Fm3m
C-diamond
a = 543.088
a = 542.86
at 20°C and 99.999 at.% purity [V-C]
at 20°C and 99.97 at.% purity [V-C]
1, Fe3Al
552.5
cF16
Fm3m
BiF3
a = 578.86 to 579.3 [2003Pis], solid solubility
ranges from 22.5 to 36.5 at.% Al
2, FeAl
1310
cP2
Pm3m
CsCl
a = 289.76 to 290.78 [2003Pis], at room temperature solid
solubility ranges
from 22.0 to 54.5 at.% Al
, Fe2Al31102-1232
cI16? a = 598.0 [2003Pis], solid solubility ranges
from 54.5 to 62.5 at.% Al
FeAl2 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
[2003Pis], at 66.9 at.% Al
solid solubility ranges
from 65.5 to 67.0 at.% Al
, Fe2Al5 1169
oC24
Cmcm
a = 765.59
b = 641.54
c = 421.84
[2003Pis], at 71.5 at.% Al
solid solubility
ranges from 71.0 to 72.5 at.% Al.
Fe4Al13
1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7 to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
[2003Pis], 74.16 to 76.7 at. % Al
solid solubility ranges
from 74.5 to 75.5 at.% Al
[2003Pis], at 76.0 at.% Al.
Also denoted FeAl3 or Fe2Al7
1, Fe3Si
1235
cF16
Fm3m
BiF3
a = 565.54 [V-C]; 11.0 to 30.5 at.% Si
[Mas]
2
1280
cP2
Pm3m
CsCl
- 10.0 to 23.5 at.% Si [Mas]
Fe2Si
1212-1040
hP6
P63/mmc
Fe2Si
a = 405.2
c = 508.55
[V-C]; 33.0 to 34.5 at.% Si
[Mas]
Fe5Si31060-825
hP16
P63/mmc
Mn5Si3
a = 675.52
c = 471.74
[V-C]
FeSi
1410
cP8
P213
FeSi
a = 448.91 [V-C]; 49.0 to 51.0 at.% Si
[Mas]
FeSi2(h)
1220-937
tP3
P4/mmm
FeSi2
a = 269.5
c = 509.0
[V-C]; 69.5 to 73.0 at.% Si
[Mas]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
389
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
FeSi2(r)
982
oC48
FeSi2
a = 986.3
b = 779.1
c = 783.3
[V-C]
* 1/ 9,
Fe3Al2Si3
-
aP16
P1
Fe3Al2Si3
-
a = 465.1
b = 632.6
c = 749.9
= 101.37°
= 105.92°
= 101.23°
a = 462.3
b = 637.4
c = 759.9
= 102.81°
= 105.6°
= 100.85°
a = 469.1
b = 632.5
c = 751.1
= 100.6°
= 105.5°
= 101.78°
a = 468.7
b = 633.1
c = 751.9
= 100.43°
= 105.44°
= 101.63°
[1940Tak], likely to correspond to the
E-phase of [1974Mur] and [1981Zar].
D-phase of [1981Zar] and 9 of
[1992Gho].
[1996Yan], Fe3Al2Si3 annealed at 600°C
[2001Kre], at Fe38.2Al29Si32.8
[2001Kre], at Fe38Al35Si27
[2001Kre], at Fe37Al41Si22
* 2, -AlFeSi,
Fe2Al5Si2
-
c**
mC*
m**
-
a = 1603.23
a = 890.0
b = 1025.0
c = 1780.0
= 132.0°
a = 889.3
b = 1018.8
c = 1766.9
= 132.18°
a = 420.0
b = 760.0
c = 1533.0
= 89.0°
at Fe6Al12Si6 [1940Tak]
[1952Arm, 1955Arm], in an Al-35.3
mass% Fe-12.8 mass% Si alloy
[1967Mun],
Fe19.4-23Al59-61.4 Si27.6-15.6 and is likely
to correspond to the K-phase of
[1974Mur] and [1981Zar]
[2001Kre], at Fe22Al60Si18
[1974Mur, 1981Zar]. K-phase at
Fe22Al63-52Si15-26.
Annealed at 600°C.
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
390
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
* 3,
Fe5Al9Si5,
FeAl2Si
-
oC128
Cmma
FeAl2Si
-
a = 768.0
b = 1530.0
c = 1600.0
a = 799.5
b = 1516.2
c = 1522.0
a = 726.2
b = 1551.2
c = 1550.6
a = 795.8
b = 1517.8
c = 1523.7
[1940Tak], likely to correspond to the
G-phase of [1974Mur] and [1981Zar]
[1974Mur, 1981Zar], G-phase at
FeAl2Si. Annealed at 600°C.
[1989Ger2] at 600°C,
Fe25Al50Si25
[2001Kre], at Fe25Al55Si20
[2001Kre], at Fe25Al50Si25
* 4, -AlFeSi,
FeAl3Si2 tI24
I4/mcm
PdGa5
a = 607.0
c = 950.0
a = 615.0
c = 947.0
a = 612.23
c = 947.91
a = 612.23
c = 948.91
a = 612.0
c = 953.0
a = 630.0
c = 941.0
a = 606.1
c = 952.5
a = 608.74
c = 951.36
[1940Tak], at FeAl3Si
[1969Pan], annealed at 800°C
for 14 h and water quenched.
[1936Jae], at FeAl4Si2. In an
Al-27.04Fe-25.01Si (mass%) alloy
[1950Phr], an Al-15 mass%
Fe-20 mass% Si alloy
[1954Spi]
[1974Mur, 1981Zar], A-phase
at FeAl2.76Si2.24. Annealed at 600°C.
[1974Mur, 1981Zar], A-phase at
FeAl3.35Si1.65. Annealed at 600°C.
[1995Gue1]
[2001Kre], at Fe16.9Al49.5Si33.3. Single
phase at 700°C.
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
391
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
* 5, -AlFeSi,
Fe2AL7.4Si
Fe46(Al0.875Si0.125)200-x
x 7
-
hP245
P63/mmc
Fe2Al7.4Si
-
a = 1240.4
c = 2623.4
a = 1240.56
c = 2623.6
a = 1239.4
c = 2621.0
a = 1239.2
c = 2619.3
a = 1241.0
c = 2626.4
a = 1230.0
c = 2630.0
a = 1230.0
c = 2630.0
a = 1230.0
c = 2620.0
a = 1230.0
c = 2630.0
a = 1240.06
c = 2622.41
a = 1238.9
c = 2625.5
a = 1239.86
c = 2621.9
[1940Tak], at Fe6Al15Si5[1977Cor], at Fe1.9Al7.1Si. Likely to
correspond to the M-phase of [1974Mur]
and [1981Zar].
[1987Gri2], at Fe2.1Al7.6Si.
Annealed at 600°C for a month.
[1987Gri2], 9.5 ± 5 mass% Si in 5.
Annealed at 600°C for a month.
[1987Gri2], 9.0 ± 5 mass% Si in 5.
Annealed at 600°C for a month.
[1987Gri2], 7.0 ± 4 mass% Si in 5.
Annealed at 600°C for a month.
[1975Bar], at Fe1.95Al7.93Si
[1953Rob]
[1967Mun]
[1977Hoi]
[1997Vyb], at Fe19.2Al71.2Si9.6
[2001Kre], at Fe19Al69Si12
[2001Kre], at Fe18Al71Si11
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
392
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
* 6, -AlFeSi
Fe2Al9Si2
-
C2/c
mC52
Fe2Al9Si2
oC?
Cmcm
t**
-
-
a = 612.23
b = 612.23
c = 4148.36
= 91.0°
a = 612.23
b = 612.23
c = 4148.36
= 91.0°
a = 612.2
b = 612.2
c = 4148.4
= 91.0°
a = 612.0
b = 612.0
c = 4150.0
= 91.0°
a = 2081.3
b = 617.5
c = 616.1
= 90.42°
a = 612
b = 612
c = 4150
= 91°
a = 579.2
b = 1227.3
c = 431.3
= 98.9°
a = 615.59 to 620.89
b = 616.87 to 619.78
c = 2076.7 to 2081.2
= 90.1° to 90.6°
a = 2079.7
b = 616.9
c = 616.87
= 90.01°
a = 2082.7
b = 616.6
c = 616.71
= 90.01°
a = 618.4
b = 625.0
c = 2069.0
a = 618.0
b = 620.0
c = 2080.0
a = 618.0
c = 4250.0
[1940Tak], at FeAl4Si
[1950Phr], Fe2Al9Si2. Composition may
vary from 27.2 to 27.4 mass% Fe and
13.5 to 13.6 mass% Si. Likely to
correspond to the L-phase of [1974Mur]
and [1981Zar].
[1954Spi]
[1955Obi]
[1975Bar], at Fe2Al10.26Si2.06
[1994Rom]
[1996Mul], at Fe14Al71.6Si14.4
[1994Mur, 1996Mur]
[1997Vyb]
[2001Kre], at Fe15Al68.5Si16.5
[2001Kre], at Fe15Al69Si16
[1993Car]
[2000Zhe]
[1955Bla], at Fe2Al8.98Si2
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
393
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Table 3: Classification of Metastable Phases Based on the Crystal System
* 7,
Fe22Al40Si38
Fe(Al0.5Si0.5)3
P21/c
mP64
Fe2Al3Si3
-
a = 717.9
b = 835.4
c = 1445.5
= 93.8
a = 718.9
b = 831.7
c = 1454.2
= 93.48
[1974Mur, 1981Zar], B-phase.
Annelaed at 600°C.
[1995Gue2] at 800°C
[2001Kre] at Fe25.3Al45Si29.7
* 8,
Fe3Al2Si4,
Fe(Al0.33Si0.67)2
oC36
Cmcm
Fe3Al2Si4
-
a = 366.8
b = 1238.5
c = 1014.7
a = 366.7
b = 1236.2
c = 1014.0
[1974Mur, 1981Zar], C-phase.
Fe32Al38Si30 Annealed at 600°C.
[1996Yan], at Fe3Al2Si4 annealed at
500°C
[2001Kre]
* 10,
Fe5Al12Si3Fe(Al0.8Si0.2)3
hP26 or
hP28
P63/mmc
Mn3Al10 or
Co2Al5
a = 752.6
c = 763.2
a = 750.9
c = 759.4
a = 1551.8
c = 729.7
[1974Mur, 1981Zar], F-phase in the
as-cast sample. The crystal structure of
F-phase after annealing at 600°C is
different from that in the as-cast samples.
[1989Ger1], at Fe1.7Al4Si
[2001Kre], at Fe25Al60Si15
Phase
Designation
Crystal
System
Composition (mass%) Lattice
Parameters [pm]
References
Fe Al Si
1 Cubic 25.4
31.9
27.3
-
30.2- 32.8
31.9
-
31.1
-
29.2-30.7
25.0
-
-
49.1
62.5
65.7
-
58.1- 60.0
61.7
-
60.8
-
61.0-64.2
69.7
-
-
25.5
5.6
7.0
-
11.7- 7.2
6.4
-
8.1
-
9.8- 5.1
5.3
-
-
-
a = 1254.83
a = 1254.83
a = 1254.53
a = 1254.8
a = 1256.0
a = 1250 to 1270
a = 1250±10
a = 1260.0
a = 1250
a = 1256.0
a = 1256.0
a = 1250
a = 1250
[1937Ser]
[1950Phr]
[1952Arm], [1955Arm]
[1954Spi]
[1955Obi]
[1967Coo]
[1967Mun]
[1967Sun]
[1977Sim]
[1985Don1]
[1986Liu1, 1986Liu2, 1987Liu]
[1987Tur]
[1988Ben2]
[1996Mul]
2 Tetra-
gonal
-
-
-
-
-
-
a = 495.0
c = 707.0
a = 1260.0
c = 3720.0
[1951Now]
[1982Wes]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
394
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
3 Ortho-
rhombic
-
29.2
25.8
30.9-32.5
-
59.5
70.5
65.4-63.3
-
11.3
3.7
3.7- 4.2
a = 609.0
b = 996.0
c = 374.0
a = 4360.0
b = 4960.0
c = 7080.0
a = 1270.0
b = 3620.0
c = 1270.0
a = 1300.0
b = 3600.0
c = 1260.0
[1936Jae]
[1952Arm], [1955Arm],
[1967Mun]
[1986Liu1], [1986Liu2],
[1987Liu]
[1987Skj1]
4 Rhombo-
hedral
27.0-19.0
-
-
73.0-78.0
-
-
0.0- 3.0
-
-
a = 890.0
= 111.8°
a = 2082.0
= 95.2°
a = 2080.0
= 95.2°
[1987Cha], [1988Cha]
[1987Tur]
[1988Ben2]
5 Hexagonal -
29.2
27.0-19.0
-
-
-
59.5
73.0-78.0
-
-
-
11.3
0.0-3.0
-
-
a = 836.0
c = 1458.0
a = 496.0
c = 702.1
a = 1470.0
c = 780.0
a = 1776.0
c = 1088.0
a = 1776.0
c = 1088.0
[1936Jae]
[1952Arm], [1955Arm],
[1967Mun]
[1987Cha], [1988Cha]
[1987Tur]
[1988Ben2]
Phase
Designation
Crystal
System
Composition (mass%) Lattice
Parameters [pm]
References
Fe Al Si
395
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Table 4: Invariant Equilibria
6 Mono-
clinic
32.1-32.7
-
34.1
-
31.6-27.0
30.6-29.9
27.8
59.5-57.0
-
65.5
-
63.1-63.5
64.2-62.6
68.8
8.4-10.3
-
< 0.5
-
5.3- 9.5
5.2- 7.5
3.4
-
a = 618.0
b = 618.0
c = 2080.0
= 91.0°
a = 869.0 ± 6
b = 635.0 ± 2
c = 632.0 ± 6
= 93.4 ± 0.5°
a = 890.0
b = 490.0
c = 4160.0
= 90.0°
a = 847.0
b = 635.0
c = 610.0
= 93.4°
a = 2810.0
b = 3080.0
c = 2080.0
= 97.74°
a = 1250.0
b = 1230.0
c = 1930.0
= 109.0°
[1951Pra2]
[1977Hoi]
[1977Sim]
[1982Wes]
[1984Don]
[1985Don1]
[1986Liu1], [1986Liu2],
[1987Liu]
7 Triclinic - - - a = 688.0
b = 593.0
c = 432.0
= 104.75°
= 130.67°
= 68.4°
[1936Jae]
Reaction T [°C] Type Phase Composition (mass%)
Fe Al Si
L + Fe2Si 1 + FeSi 1180 U1 - - - -
L + 2 + Fe2Al5 1120 U2 L
, Fe2Al3
2
Fe2Al5
51.0
56.5
58.0
45.0
46.0
43.0
28.0
52.0
3.0
0.5
14.0
3.0
L + 1 + FeSi 1 1050 P1 L
1
FeSi
1
50.0
63.0
66.3
55.0
31.0
26.0
0.4
26.6
19.0
11.0
33.3
18.4
L + 2 Fe2Al5 + 1 1030 U3 L
2
Fe2Al5
1
48.5
65.0
45.0
55.0
37.5
25.0
52.5
26.6
14.0
10.0
2.5
18.4
Phase
Designation
Crystal
System
Composition (mass%) Lattice
Parameters [pm]
References
Fe Al Si
396
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
L + Fe2Al5 Fe4Al13 + 1 1020 U4 L
Fe2Al5Fe4Al13
1
48.0
45.0
39.2
55.0
38.0
52.5
60.0
26.6
14.0
2.5
0.8
18.4
L + FeSi FeSi2(h) + 1 1000 U5 L
FeSi
FeSi2(h)
1
42.0
66.3
44.8
55.0
26.0
0.4
0.5
26.6
32.0
33.3
54.7
18.4
L + Fe4Al13 + 1 2 940 P2 L
Fe4Al13
1
2
40.0
39.2
55.0
41.9
41.0
60.0
26.6
40.5
19.0
0.8
18.4
17.6
L + 1 + 2 7 935 P3 L
1
2
7
39.0
55.0
41.9
42.2
39.0
26.6
40.5
36.7
22.0
18.4
17.6
21.1
L + 1 FeSi2(?) + 7 885 U6 L
1
FeSi2(?)
7
28.0
55.0
49.7
42.2
36.0
26.6
0.5
36.7
36.0
18.4
49.8
21.1
L + FeSi2(?) 7 + (Si) 880 U7 L
FeSi2(?)
7
(Si)
26.0
49.7
42.2
0.01
38.0
0.5
36.7
0.013
36.0
49.8
21.1
99.977
L + 7 + (Si) 4 865 P4 L
7
(Si)
4
23.0
42.2
0.01
28.9
45.0
36.7
0.013
41.9
32.0
21.1
99.977
29.2
L + Fe4Al13 + 2 5 855 P5 L
Fe4Al13
2
5
25.0
39.2
41.9
38.1
58.0
60.0
40.5
46.0
17.0
0.8
17.6
15.9
L + 7 2 + 4 835 U8 L
7
2
4
22.0
42.2
41.9
28.9
56.0
36.7
40.5
41.9
22.0
21.1
17.6
29.2
L + 2 4 + 5 790 U9 L
2
4
5
18.0
41.9
28.9
38.1
61.0
40.5
41.9
46.0
21.0
17.6
29.2
15.9
L + 4 + 5 6 700 P6 L
4
5
6
7.2
28.9
38.1
29.1
78.8
41.9
46.0
56.3
14.0
29.2
15.9
14.6
L + Fe4Al13 (Al) + 5 632 U10 L
Fe4Al13
(Al)
5
2.0
39.2
0.05
38.1
93.8
60.0
99.31
46.0
4.2
0.8
0.64
15.9
Reaction T [°C] Type Phase Composition (mass%)
Fe Al Si
397
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Table 5: Coordinates of the /( + ) and ( + )/ Phase Boundaries in the Al-Fe-Si System
L + 5 (Al) + 6 613 U11 L
5
(Al)
6
1.8
38.1
0.04
29.1
92.0
46.0
98.96
56.3
6.2
15.9
1.0
14.6
L + 4 6 + (Si) 600 U12 L
4
6
(Si)
1.5
28.9
29.1
0.01
84.2
41.9
56.3
0.012
14.3
29.2
14.6
99.978
L 6 + (Al) + (Si) 573 E1 L
6
(Al)
(Si)
0.5
29.1
0.01
0.01
87.8
56.3
98.34
0.01
11.7
14.6
1.65
99.98
Composition mass% Temperature [°C] of the
Al Si /( + ) boundary ( + )/ boundary
0.16
0.19
0.31
0.44
0.44
0.48
0.64
0.71
0.74
0.25
0.58
0.93
0.19
0.53
0.13
0.23
0.65
0.24
905
952
1014
935
976
948
1030
1048
1000
1385
1351
1300
1350
1326
1347
1275
1270
1303
Reaction T [°C] Type Phase Composition (mass%)
Fe Al Si
20
40
60
80
20 40 60 80
20
40
60
80
Fe Al
Si Data / Grid: at.%
Axes: at.%
τ1 [1940Tak]
τ2
τ3
τ4
τ5 [1940Tak]
τ6
τ7 [1974Mur, 1981Zar]
τ8 [1974Mur, 1981Zar]τ9 [1974Mur, 1981Zar]
τ5
[1974Mur, 1981Zar]
[1974Mur, 1981Zar]
[1974Mur, 1981Zar]
[1940Tak]
[1940Tak]
[1940Tak]
[1936Jae]
τ10 [1974Mur, 1981Za
[1985Gri2] [1975Bar][1977Cor]
[1967Mur][1955Obi][1950Phr]
[1950Phr]
[1955Bla]
[1975Baz]
τ5 [2001Kra]
τ10 [2001Kre]
τ3 [2001Kre]
τ1/τ9 [2001Kre]
τ8 [2001Kre]τ8 [1996Yan]
[2001Kre][1988Zak]
[2001Kre, 1988Za[1996Mul]
τ7 [2001Kre]
[1974Mur, 1981Zar]
Fig. 1: Al-Fe-Si.
Distribution of the
equilibrium ternary
phases, as reported by
different authors
398
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
10
20
30
40
60 70 80 90
10
20
30
40
Fe 50.00Al 50.00Si 0.00
Al
Fe 0.00Al 50.00Si 50.00 Data / Grid: at.%
Axes: at.%
[1986Lin1,1986Lin2, 1987Lin][1986Lin1, 1986Lin2, 1987Lin]
µ6µ3[1987Skj1][1977Sim]
µ1
[1952Arm][1985Don1]
[1985Don1][1984Don][1950Phr]
[1967Coo][1955Obi]
[1955Obi]
µ4 or µ5[1987Cha, 1988Cha]
[1951Bra2]
µ6
[1967Sun]µ6
[1984Don]
[1952Arm, 1967Mun], µ3 or µ4
µ1
[1968Don]
µ1, [1937Ser]
10 200
250
500
750
1000
1250
1500
Fe 75.00Al 25.00Si 0.00
Fe 75.00Al 0.00Si 25.00Si, at.%
Tem
pera
ture
, °C
(αFe)
1223°C
750°C
550°C
α2(B2)
α1(DO3)
640°C
460°C
(αFe)+α1+α2
(αFe)+α1
(αFe)+α2
Fig. 2: Al-Fe-Si.
Distribution of the
metastable ternary
phases, as reported by
different authors
Fig. 3: Al-Fe-Si.
The Fe3Al-Fe3Si
sections showing the
boundaries of 1
(D03), 2 (B2) and
( Fe) (disordered
bcc) phases
399
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Fig
. 4a:
Al-
Fe-
Si.R
eact
ion
schem
e, p
art
1
Al-
Fe
Fe-
Si
A-B
-CA
l-F
e-S
iA
l-S
i
l + α
2ε
12
32
p1
L+
Fe 2
Si
α 1+
FeS
ica
.11
50
U1
l F
eSi+
FeS
i 2(h
)
12
12
e 1
l F
eSi 2
(h)+
(Si)
12
07
e 2
l F
eSi+
Fe 2
Si
12
03
e 3
lα 1
+ F
e 2S
i
12
00
e 4
lη
+ε
11
65
e 5
L +
α2
η+
τ 11
030
U3
L +
η F
e 4A
l 13
+τ 1
10
20
U4
Fe 2
Si+
FeS
i F
e 5S
i 3
10
60
p3
Fe 2
Si
Fe 5
Si 3
+F
e 3S
i
10
40
e 8
FeS
i+F
eSi 2
(h)
FeS
i 2(r
)
98
2p4
FeS
i 2(h
)F
eSi 2
(r)+
(Si)
93
7e 9
ε +
η F
eAl 2
11
56
p2
lη
+ F
e 4A
l 13
11
60
e 6
εα 2
+ F
eAl 2
11
02
e 7L
+ ε
α 2+
η1
120
U2
L +
α1
+ F
eSi
τ 11
050
P1
L +
FeS
i F
eSi 2
(h)
+ τ1
10
00
U5
L+
τ 1 +
τ2
τ 79
35
P3
L +
Fe 4
Al 13
+τ 1
τ 29
40
P2
L +
τ1
FeS
i 2(r
) +
τ7
88
5U6
L+
α 1+
FeS
iF
eSi+
α 1+
Fe 2
Si
L+
α 2+
ηε+
α 2+
η
α 1+
FeS
i+τ 1
L+
FeS
i+τ 1
FeS
i+F
eSi 2
(h)+
τ 1
L+
FeS
i 2(r
)+τ 7
τ 1+
FeS
i 2(r
)+τ 7
L+
τ 2+
τ 7
τ 7+τ
1+
τ 2
Fe 4
Al 13+L
+τ 2
Fe 4
Al 1
3+L
+τ 1
Fe 4
Al 13+η
+τ 1
α 2+η
+τ 1
η+L
+τ 1L
+α 1
+τ 1
L+
τ 1+
τ 2
L+
τ 1+
τ 7
L+
FeS
i 2(h
)+τ 1
Fe 4
Al 13+
τ 1+
τ 2
400
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Fig
. 4b:
Al-
Fe-
Si.R
eact
ion s
chem
e, p
art
2
Al-
Fe
Fe-
Si
A-B
-CA
l-F
e-S
iA
l-S
i
L +
FeS
i 2(r
)τ 7
+ (
Si)
88
0U7
L +
τ7
+ (
Si)
τ 4
86
5P4
L +
τ7
τ 2+
τ 48
35
U8
L +
Fe 4
Al 13
+τ 2
τ 58
55
P5
L +
τ2
τ 4+
τ 57
90
U9
L +
τ4
+τ 5
τ 67
00
P6
l F
e 4A
l 13
+ (
Al)
65
5e 11
L +
Fe 4
Al 13
(A
l) +
τ5
63
2U10
L +
τ5
(A
l) +
τ6
61
3U11
L +
τ4
τ 6+
(S
i)6
00
U12
Lτ 6
+ (
Al)
+ (
Si)
57
3E1
l (
Al)
+ (
Si)
57
7e 12
Fe 5
Si 3
α 2+
FeS
i
82
5e 10
L+
(Al)
+τ 6
τ 5+
(Al)
+τ 6
τ 6+
(Al)
+(S
i)
τ 4+
τ 6+
(Si)
L+
τ 6+
(Si)
FeS
i 2(r
)+τ 7
+(S
i)L
+τ 7
+(S
i)
τ 7+
(Si)
+τ 4 τ 7
+τ 2
+τ 4
τ 2+
τ 4+
τ 5L
+τ 2
+τ 5
L+
τ 7+
τ 4
L+
(Si)
+τ 4
Fe 4
Al 13+
(Al)
+τ 5
L+
(Al)
+τ 5
L+
τ 4+
τ 6L
+τ 5
+τ 6
τ 4+
τ 5+
τ 6
Fe 4
Al 13+
τ 2+
τ 5L
+τ 2
+τ 5
L+
FeS
i 2(h
)+(S
i)L
+F
eSi 2
(r)+
τ 7
L+
τ 2+
τ 7
L+
τ 2+
Fe 4
Al 13
L+
Fe 4
Al 13+
τ 5L+
τ 2+
τ 4
401
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Si, mass%
Fe,mass%
2
0
Al10
2
3
4
5
6
0
1
4 6 8 12 14 16
(Al)
650°C
660°C
670°C680°C
690°C
700°C
710°C720°C730°C740°C750°C760°C770°C780°C
640°C
620°C
620°C
610°C
610°C
600°C
590°C
580°C
630°C
(Si)
U11
P6
U12
E1
U10
Fe Al 13
4 �5
�2
�6
�4
20
40
60
80
20 40 60 80
20
40
60
80
Fe Al
Si Data / Grid: at.%
Axes: at.%
1400
1350
1300
12501207°C,e2
FeSi2(h)
1212°C, e1
(Si)
1050
1000950
900P4
U7
τ1
U5
P1
U3
P2
U8τ7
U9P5τ2
U6
900
U4
τ5
τ6
(Al)U10
U11
P6 U12e12
700
750800
850
U2
Fe2 Al
5
Fe4 Al
13
τ4
655°C,e11
13501300 1250 1150
FeSi
Fe2Si U1
α2
1300
1350
1200
1100
1200°C, e4
1203°C, e3
1400
1500
1232°C, p1 1165°C, e5 1160°C, e6
(αFe)
α2
α1
ε
E1
P3
1200
Fig. 6: Al-Fe-Si.
Liquidus surface
Fig. 5: Al-Fe-Si.
Calculated liquidus
surface of Al-corner
[1999Liu]
402
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
10
90
10
Fe 20.00Al 80.00Si 0.00
Al
Fe 0.00Al 80.00Si 20.00 Data / Grid: at.%
Axes: at.%
L+τ4
L+τ4+τ6
L+τ6
L+τ5+τ6
L+τ5
L
L+Fe4Al13+τ5
L+Fe4Al13
L+(Al)
L+(Al)+Fe4Al13(Al)
(Al)+Fe4Al13
20
40
60
80
20 40 60 80
20
40
60
80
Fe Al
Si Data / Grid: at.%
Axes: at.%
FeSi2(h)+L+(Si)
L+(Si)
L
L+FeSi2(h)FeSi
2 (h)+L+τ1
FeSi2(h)
FeSi2 (h)+τ
1 +FeSi
L+τ1
τ1
τ1 +η+α
2
L+Fe4Al13
τ1+L+Fe4Al13
Fe4Al13
Fe4Al13+τ1+Fe2Al5
FeAl2 η
α2+η
α1+τ1
α2
α1+FeSi
α1+Fe5Si3+FeSiFeSi+τ
1 +α1
FeSi
Fe5Si3
α1+Fe5Si3
(γFe) (γFe)+(αFe)
(αFe)
α1
Fig. 7: Al-Fe-Si.
Isothermal section
at 1000°C
Fig. 8: Al-Fe-Si.
Isothermal section of
the Al-corner
at 640°C
403
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
20
40
60
80
20 40 60 80
20
40
60
80
Fe Al
Si Data / Grid: at.%
Axes: at.%
Fe4Al13ηFeAl2(αFe)+α2
α2
α1+α2
FeSi
FeSi2
(Si)+FeSi2
(Si)
(Al)+(Si)
(Al)
(Al)+(Si)+τ
4
τ4 +τ
7 +(Si)
(Si)+FeSi2 +τ7
τ7+τ8+FeSi2τ8+FeSi2+FeSi
τ1/τ9+FeSi+α2
(αFe)+α1
(αFe)
α1
α2
α2+τ1/τ9+η
FeAl2+α2 (Al)+τ5+Fe4Al13
(Al)+τ6+τ4τ6
τ5
τ10
τ2
τ7
τ3
τ1/τ9
α1+FeSiτ4
τ8
τ1 /τ
9 +τ8 +τ
10
τ1 /τ
9 +FeSi+τ8
10
20
30
70 80 90
10
20
30
Fe 40.00Al 60.00Si 0.00
Al
Fe 0.00Al 60.00Si 40.00 Data / Grid: at.%
Axes: at.%
τ2
τ5
Fe4Al13
(Al)+Fe4Al13+τ5
(Al)
(Al)+τ6+(Si)(Al)+τ5+τ6
τ6
Fig. 10: Al-Fe-Si.
Isothermal section
at 600°C
Fig. 9: Al-Fe-Si.
Isothermal section of
the Al-corner
at 570°/600°C, see
text
404
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Fe 1.00Al 99.00Si 0.00
Al
Fe 0.00Al 99.00Si 1.00 Data / Grid: at.%
Axes: at.%
(Al)+τ6+(Si)
(Al)+(Si)
(Al)
(Al)+τ5
(Al)+τ5+τ6
(Al)+τ6
(Al)+Fe4Al13
(Al)+τ5+Fe4Al13
20
40
60
80
20 40 60 80
20
40
60
80
Fe Al
Si Data / Grid: at.%
Axes: at.%
(Al)+(Si)+τ
6
τ6α2
τ8
FeSi2
FeSi
ηFeAl2 Fe4Al13
τ4τ1/τ9 τ7
τ2
τ3τ10 τ5
FeSi+FeSi2+τ
8 (Si)+τ8+τ7
(Si)+τ7 +τ
4
(Si)
(Al)
FeSi
2+τ
8+(
Si)
Fig. 12: Al-Fe-Si.
Isothermal section of
the Al-corner
at 500°C
Fig. 11: Al-Fe-Si.
Partial isothermal
section at 550°C
405
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
70
80
90
10 20 30
10
20
30
Fe Fe 60.00Al 40.00Si 0.00
Fe 60.00Al 0.00Si 40.00 Data / Grid: at.%
Axes: at.%
(αFe)
(αFe)+α1
α2 α1+α2
α1+α2
α1 α2
70
80
90
10 20 30
10
20
30
Fe Fe 60.00Al 40.00Si 0.00
Fe 60.00Al 0.00Si 40.00 Data / Grid: at.%
Axes: at.%
(αFe)α2
α1
Fig. 14: Al-Fe-Si.
Isothermal section of
the Fe-corner
at 650°C
Fig. 13: Al-Fe-Si.
Isothermal section of
the Fe-corner
at 700°C
406
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
70
80
90
10 20 30
10
20
30
Fe Fe 60.00Al 40.00Si 0.00
Fe 60.00Al 0.00Si 40.00 Data / Grid: at.%
Axes: at.%
α2
α1+α2
α1
(αFe)+α1
α1+α2
(αFe)
α2
Fig. 16: Al-Fe-Si.
Isothermal section of
the Fe-corner
at 450°C
70
80
90
10 20 30
10
20
30
Fe Fe 60.00Al 40.00Si 0.00
Fe 60.00Al 0.00Si 40.00 Data / Grid: at.%
Axes: at.%
(αFe)
α1+α2
(αFe)+α1
α1 α2
α2
Fig. 15: Al-Fe-Si.
Isothermal section of
the Fe-corner
at 550°C
407
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
10400
500
600
700
800
Fe 1.97Al 98.03Si 0.00
Fe 1.98Al 83.22Si 14.80Si, at.%
Tem
pera
ture
, °C
(Al)+τ6+(Si)(Al)+Fe4Al13+τ5
(Al)+Fe4Al13
(Al) +τ5
(Al)+τ5+τ6
(Al)+τ6
(Al)+L+τ6 L+τ6+(Si)
L+τ4+τ6
L+τ4
L+τ6
L+τ5+τ6
L+τ5
L+Fe4Al13+τ5(Al)+L+Fe4Al13
(Al)+τ5+L
L+Fe4Al13
L
632°C
613°C
573°C
600°C
Fig. 18: Al-Fe-Si.
Polythermal section at
a constant Fe content
of 4.0 mass%
10500
600
700
Fe 0.30Al 99.70Si 0.00
Fe 0.30Al 80.30Si 19.40Si, at.%
Tem
pera
ture
, °C
Fe4Al13+(Al)
(Al)+Fe4Al13+τ5
(Al)+τ5
(Al)+τ5+τ6
τ6+(Al)
L+τ6+(Al)
(Al)+(Si)+τ6
L+(Si)+τ6
L+(Si)+τ4
L+(Si)
L+τ5+(Al)
L+(Al)
11.33 at.%573
613
L+(Al)+Fe4Al13655°C, e11
632
L
Fig. 17: Al-Fe-Si.
Polythermal section at
a constant Fe content
of 0.7 mass%
408
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
400
500
600
700
Fe 2.00Al 90.10Si 7.90
Fe 0.00Al 92.30Si 7.70Al, at.%
Tem
pera
ture
, °C
LL+τ5
L+τ5+τ6
L+τ5+Fe4Al13
L+Fe4Al13
L+τ6
(Al)+L+τ6 573°CL+(Al)
(Al)+τ6+(Si)
(Al)+(Si)
L+(Al)+(Si)
91 92
Si, mass%
Fe,mass%
10-3
�
0.2
0
Al
0.4 0.6 0.80 1.0 1.2 1.4 1.6 1.8
10
15
20
25
30
35
40
45
50
5
�6
�5
(Si)
Fe Al4 13
640°C
630°C
620°C
610°C
590°C
580°C570°C
560°C550°C530°C510°C490°C470
450
600°C
Fig. 19: Al-Fe-Si.
Polythermal section
at a constant Si
content of 8.0 mass%
Fig. 20: Al-Fe-Si.
(Al)-solidus (dash
lines) and -solvus
(solid lines) surfaces,
calculated using the
dataset of [1999Liu]
409
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Si
Fe, mass%
Si,mass%
1
0
Al2 3 4 5 60
2
4
6
12
10
8
e , 577°C12
e , 655°C11
secondary (Al)
650°C
640°C
630°C
sec. FeAl3
650°C
640°C
sec. �5
U10
sec.
� 6
U11
E1
sec.
(Si)
sec. (Si)
sec. �6
tern. (Si)
640°C
650°C
660°C
660°C
tern. �6
sec. �6
670°C
620°
C
sec.
� 5
620°C
600°C
590°C
600°C
580°C
590°C
sec. (Al)
sec. (Al)
tern. (Al)
630°C
secondary �5
ternary (Al)
615°C
615°C
620°C 630°C
Fig. 21: Al-Fe-Si.
Surface of secondary
crystalization of
Al-corner
410
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
Aluminium – Iron – Samarium
Gabriele Cacciamani and Paola Riani
Literature Data
The Al-Fe-Sm system has been investigated only for low Sm content (0-33 at.%). Phase equilibria have
been studied by [1974Viv2] at 500°C and 0-33 at.% Sm by means of XRD and micrography.
Microstructural studies have also been performed by [1999Kub] on selected alloys homogenized at 1050°C
in the region close to the Sm2(Fe1–xAlx)17 phase.
The Sm2(Fe1–xAlx)17 phase has been widely studied. Structural and magnetic properties of this phase have
been investigated by [1976McN, 1991Wei, 1994Jia, 1995Che, 1995Yan, 1996Zar, 1998Ono, 1999Ren,
2000Kub, 2000Ren, 2001Ter]. The same properties for the R2(Fe1–xTx)17 phases with R = Rare Earth and
T = Al, Si, Ga have been recently reviewed by [2002Ram].
The structure of the binary and/or ternary Laves phases along the SmAl2-SmFe2 section has been
investigated by [1968Dwi, 1971Oes, 1973Zar, 1975Dwi].
Other phases have been investigated by [1974Viv1, 1976Bus, 1978Bus] ( 3 or Sm(Fe1–xAlx)12), [1992Hu]
( 2 or Sm6Fe11Al3), [1998Thi] ( 4 or SmFe2Al10), [2000Sam] (Sm(Fe1–xAlx)7, metastable).
Alloy samples were generally prepared by arc or induction melting the pure elements (typically 99.5% Sm
and 99.99% Fe and Al) under an inert atmosphere. Samples were then homogenized at appropriate
temperature (typically 500-1000°C) and quenched.
Amorphous alloys were also obtained by [2001Kon1, 2001Kon2] who studied also their magnetic
properties.
Binary Systems
The accepted Al-Fe phase diagram [2003Pis] is mainly based on the assessment by [1993Kat], except for
the Fe-rich region where the ordering equilibria between the ( Fe), FeAl and Fe3Al solid solutions have
been recently investigated by [2001Ike].
The Al-Sm binary system is accepted from the assessment by [2003Bod], and Fe-Sm from [2000Oka]
(reporting a previous assessment by [1993Oka]). A thermodynamic assessment of the Fe-Sm system has
been recently produced by [2002Zin].
Solid Phases
Table 1 summarizes the crystal structure data relevant to all the Al-Fe-Sm solid phases. Four ternary phases
and several binary-based solid solutions have been identified in the system. Most of them show quite
extended line solubility due to the mutual substitution between Fe and Al (at constant Sm concentration).
The ternary Laves phase 1 shows the MgZn2 type structure [1968Dwi, 1973Zar, 1975Dwi] (not detected
by [1971Oes]), different from the binary solid solutions Sm(Al1–xFex)2 and Sm(Fe1–xAlx)2 belonging to the
MgCu2 type. The solubility ranges of the three phases have been investigated by [1974Viv2, 1975Dwi].
2 has been identified by [1992Hu] by powder XRD (Debye-Sherrer and Guinier-Huber methods) in
samples annealed at 800°C and quenched. No solid solubility has been reported.
The structure of 3 has been mainly studied at the SmFe4Al8 composition [1976Bus]. Its solubility range
has been determined by [1974Viv2].
4 has been identified by [1998Thi]. It does not show any solid solubility.
Structural properties of Sm2(Fe1–xAlx)17 have been studied, as a function of the Al concentration, by several
authors, generally at temperatures where the Th2Zn17 type structure is stable. Single crystal [1998Ono] and
Rietveld refinement [2001Ter] have been carried out. The ternary solubility of the high temperature form
(Ni2Th17 type), however has not been determined.
A metastable phase, Sm(Fe1–xAlx)7, has been obtained by [2000Sam]; its tetragonal structure is similar to
Sm2Fe14B with empty boron sites.
411
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
Isothermal Sections
[1974Viv2] determined the Al-Fe-Sm isothermal section at 500°C in the 0-33 at.% Sm composition range.
It is presented in Fig. 1, slightly adapted in order to be consistent with the accepted binary systems (Sm3Al11
was not included in the original section). The 2 phase, identified by [1992Hu] in samples annealed at higher
temperature, is not reported in this section.
Notes on Materials Properties and Applications
Magnetic properties such as coercive force, TC, magnetic anisotropy, etc. of Sm2(Fe1–xAlx)17 have been
investigated as a function of the Al concentration by several authors [1976McN, 1991Wei, 1994Jia,
1995Che, 1995Kat, 1996Kat, 1996Zar]. [1996Sab] calculated magnetic properties and site occupancies,
[1999Kub] investigated the influence of the Fe substitution by Al on the microstructure and the HDDR
(hydrogenation-disproportionation-desorption-recombination) process and [1998Lon] investigated the
Sm2(Fe1–xAlx)17 solid solution by Mössbauer spectroscopy: he confirmed that Al site occupancies are
independent on the R element, determined the Fe site magnetic moments and revealed an important covalent
contribution in the Al-Fe bonding. Magnetic properties of the metastable Sm(Fe1–xAlx)7 phase [2000Sam]
and of amorphous Al-Fe-Sm alloys [2000Fan, 2001Kon1, 2001Kon2] have been studied.
[1998Hag] studied the magnetic properties of the Sm(Fe1–xAlx)12, phase at the SmFe4Al8 composition and
[2003Kan] carried out an atomistic simulation of its lattice constants.
References
[1958Tay] Taylor, A., Jones, R.M., “Constitution and Magnetic Properties of Iron-Rich
Iron-Aluminium Alloys”, J. Phys. Chem. Solids, 6, 16-37 (1958) (Crys. Structure,
Experimental, 49)
[1961Lih] Lihl, F., Ebel, H., “X-Ray Examination of the Constitution of Iron-Rich Alloys of the
Iron-Aluminium System” (in German), Arch. Eisenhuettenwes., 32, 483-487, (1961) (Crys.
Structure, Experimental, 12)
[1968Dwi] Dwight, A.E., “The Crystal Chemistry of Some Scandium and Lanthanide Compounds”,
Proc.: 7th Rare Earth Res. Conf., Coronado, Calif., 1, 273-281 (1968) (Crys. Structure, 8)
[1971Bus] Buschow, K.H.J., “The Samarium-Iron System”, J. Less-Common Met., 25, 131-34 (1971)
quoted by H. Okamoto, (Equi. Diagram, Crys. Structure, Experimental)
[1971Oes] Oesterreicher, H., “Structural Studies of Rare-Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Experimental, Crys. Structure, 6)
[1973Zar] Zarechnyuk, O.S., Rykhal, R.M., Vivchar, O.I., “Laves Phases in Ternary Systems
Rare-Earth Metal - Transition Metal of the IV Period - Aluminium”, Sb. Nauchn. Rab. Inst.
Metallofiz., Akad. Nauk Ukr. SSR, 42, 92-94 (1973) (Crys. Structure, Experimental,
Review)
[1974Viv1] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12-type Structure in R-Fe-Al
Systems” (in Russian), Tezisy Dokl.-Vses. Konf. Kristallokhim. Intermet. Soedin., Rykhal,
R.M. (Ed.), Vol. 2, Gos. Univ., Lvov, 41 (1974) (Crys. Structure, Experimental, 0)
[1974Viv2] Vivchar, O.I., Zarechnyuk, O.S; Ryabov, V.R., “The Ternary System Sm-Fe-Al in the
Range 0-33.3 at.% Sm” (in Russian), Dop. Akad. Nauk Ukrain. RSR, Ser. A, Fiz-Mat. Tekh.
Nauki, 4, 363-365 (1974) (Experimental, Crys. Structure, Equi. Diagram, *, 7)
[1975Dwi] Dwight, A.E., Kimball, C.W., Preston, R.S., Taneja, S.P., Weber, L., “Crystallographic and
Mössbauer Study of (Sc, Y, Ln)(Fe, Al)2 Intermetallic Compounds”, J. Less-Common Met.,
40, 285-291 (1975) (Crys. Structure, Experimental, 8)
[1976Bus] Buschow, K.H.J., van der Vucht, J.H.N., van den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth-3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Crys. Structure, Experimental, 2)
412
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
[1976McN] McNeelly, D., Oesterreicher, H., “Structural and Low-Temperature Magnetic Studies on
Compounds Sm2Fe17 with Al Substitution for Fe”, J. Less-Common Met., 44, 183-193
(1976) (Crys. Structure, Experimental, 26)
[1978Bus] Buschow, K.H.J., van der Kran, A.M., “Magnetic Ordering in Ternary Rare Earth Iron
Aluminium Compounds (RFe4Al8)”, J. Phys. F: Met. Phys., 8, 921-932 (1978) (Magn.
Prop., Experimental, 8)
[1986Gri] Griger, A., Syefaniay, V., Turmezey, T., “Crystallographic Data and Chemical
Compositions of Aluminum-Rich Al-Fe Intermetallic Phases”, Z. Metallkd., 77, 30-35
(1986) (Equi. Diagram, Crys. Structure, Experimental, 23)
[1989Gle] Glebova, O.D., Domyshev, O.V., Basargin, O.V., Zakharov, A.I., “X-Ray Study of Phase
Composition and Thermal Expansion Coefficient of Sm2Fe17 Compound” (in Russian), Fiz.
Met. Metalloved., 68(3), 185-87 (1989), quoted by H. Okamoto, (Equi. Diagram, Crys.
Structure, Experimental)
[1991Wei] Weitzer, F., Hiebl, K., Rogl, P., “Samarium-Iron Based Magnet Materials with the
Th2Zn17-Type Structure”, J. Appl. Phys., 69(10), 7215-7218 (1991) (Crys. Structure,
Experimental, 20)
[1992Hu] Hu, B.P., Coey, J.M.D., Klesnar, H., Rogl, P., “Crystal Structure, Magnetism and 57Fe
Mössbauer Spectra of Ternary RE6Fe11Al3 and RE6Fe13Ge Compounds”, J. Magn. Magn.
Mater., 117, 25-231 (1992) (Crys. Structure, Experimental, Magn. Prop., Moessbauer, 14)
[1993Kat] Kattner, U.R., Burton, B.P., “Al-Fe (Aluminum-Iron)”, in “Phase Diagrams of Binary Iron
Alloys”, Okamoto, H. (Ed.), ASM International, Materials Park, Ohio 44073-0002, 12-28
(1993) (Review, 99)
[1993Oka] Okamoto, H., “Fe-Sm (Iron-Samarium)”, in “Phase Diagrams of Binary Iron Alloys”,
Okamoto, H. (Ed.), ASM International, Materials Park, Ohio 44073-0002, 382-84 (1993)
(Review, 17)
[1994Bur] Burkhardt, U., Grin, J., Ellner, M., Peters, K., “Structure Refinement of the Iron-Aluminium
Phase with the Approximate Composition Fe2Al5”, Acta Crystallogr., Sect. B: Struct.
Crystallogr. Crys. Chem., 50B, 313-316 (1994) (Crys. Structure, Experimental, 9)
[1994Gri] Grin, J., Burkhardt, U., Ellner, M., Peters, K., “Refinement of the Fe4Al13 Structure and its
Relationship to Quasihomological Homotypical Structures”, Z. Kristallogr., 209, 479-487
(1994) (Crys. Structure, Experimental, 39)
[1994Jia] Jianmin, W., Feng, L., Tai, L.C., “The Structure and Magnetic Properties of
Sm2(Fe1–xCox)17–yAly”, J. Magn. Magn. Mater., 134, 53-58 (1994) (Crys. Structure,
Experimental, Magn. Prop., 24)
[1995Che] Cheng, Z., Shen, B., Liang, B., Zhang, J., Wang, F., Zhang, S., Gong, H., “The Change in
Magnetic Anisotropy in R2Fe17–xAlx Compounds (RSm or Tb)”, J. Phys.: Condensed
Matter, 7, 4707-4712 (1995) (Crys. Structure, Experimental, Magn. Prop., 16)
[1995Kat] Kato, H., Shiomi, J., Koide, T., Iriyama, T., Yamada, M., Nakagawa, Y., “High Field
Magnetization and Spin Reorientation in Sm2(Fe1–xAlx)17 Single Crystals”, J. Alloys
Compd., 222, 62-66 (1995) (Crys. Structure, Experimental, Magn. Prop., 14)
[1995Yan] Yang, F., Li, X., Tang, N., Wang, J., Lu, Z., Zhao, T., Li, Q., Liu, J.P., de Boer, F.R.,
“Magnetic Properties of Sm2Fe17Ny with Al Substituted for Fe”, J. Alloys Compd., 221,
248-253 (1995) (Crys. Structure, Experimental, Magn. Prop., 21)
[1996Kat] Kato, H., Knide, T., Yamada, M., Motokawa, M., Miyazaki, T., “High Field Magnetization
and Spin Reorientation in Sm2(Fe1–xAlx)17 and Nd2(Fe1–xAlx)17 Single Crystals”, Sci. Rep.
Res. Inst. Tohoku Univ. Ser. A, 42A(2), 283-288 (1996) (Experimental, Magn. Prop.)
[1996Sab] Sabirianov, R.F., Jaswal, S.S., “Electronic Structure and Magnetism in Sm2Fe17–xAx (A =
Al, Ga, Si)”, J. Appl. Phys., 79(82), 5942-44 (1996) (Crys. Structure, Experimental, Magn.
Prop.) as quoted in [C.A.] 124:358574R
[1996Zar] Zarek W., “Influence of Si, Al and C on the Crystal Structure and Magnetic Properties of
Sm2Fe17”, J. Magn. Magn. Mater., 157/158, 91-92 (1996) (Crys. Structure, Magn. Prop.,
Experimental, 8)
413
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
[1997Kog] Kogachi, M., Haraguchi, T., “Quenched in Vacansies in B2-Structured Intermetallic
Compound FeAl”, Mater. Sci. Eng. A, 230A, 124-131 (1997) (Crys. Structure,
Experimental, 23)
[1998Ali] Aliravci, C.A., Pekgueleryuez, M.O., “Calculation of Phase Diagrams for the Metastable
Al-Fe Phases Forming in Direct-Chill (DC)-Cast Aluminium Alloy Ingots”, Calphad, 22,
147-155 (1998) (Calculation, Equi. Diagram, 20)
[1998Hag] Hagmusa, I.H., Brueck, E., de Boer, F.R., Buschow, K.H.J., “Magnetic Properties of
RFe4Al8 Compounds Studied by Specific Heat Measurements”, J. Alloys Compd., 278,
80-82 (1998) (Experimental, Magn. Prop., 9)
[1998Lon] Long, G.J., Pringle, O.A., Ezekwenna, P.C., Mishra, S.R., Hautot, D., Grandjean, F., “A
Mössbauer Spectral Study of the Sm2Fe17–xAlx Solid Solutions”, J. Magn. Magn. Mater.,
186, L10-L20 (1998) (Crys. Structure, Experimental, Moessbauer, 22)
[1998Ono] Ono, Y., Shiomi, J., Kato, H., Iriyama, T., Kajitani, T., “X-Ray Diffraction Study of
Sm2(Fe1–xAlx)17 Single Crystals with x = 0.058, 0.081”, J. Magn. Magn. Mater., 187(1),
113-116 (1998) (Crys. Structure, Experimental, 15)
[1998Sac] Saccone, A., Cacciamani, G., Maccio, D., Borzone, G., Ferro, R., “Contribution to the Study
of the Alloys and Intermetallic Compounds of Aluminium with the Rare-Earth Metals”,
Intermetallics, 6, 201-215, (1998) (Experimental, Crys. Structure, Equi. Diagram, 62)
[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10 (Ln = Y, La-Nd,
Sm, Cd-Lu and T = Fe, Ru, Os) with YbFe2Al10 Type Structure and Magnetic Properties of
the Iron-Containing Series”, J. Mater. Chem., 8(1), 125-130 (1998) (Crys. Structure,
Experimental, Magn. Prop., 31)
[1999Dub] Dubrovinskaia, N.A., Dubrovinsky, L.S., Karlsson, A., Saxena, S.K., Sundman, B.,
“Experimental Study of Thermal Expansion and Phase Transformations in Iron-rich Fe-Al
Alloys”, Calphad, 23(1), 69-84 (1999) (Equi. Diagram, Experimental, 16)
[1999Kub] Kubis, M., Gutfleisch, O., Gebel, B., Mueller, K-H., Harris, I.R., Schultz, L., “Influence of
M = Al, Ga and Si on Microstructure and HDDR-Processing of Sm2(Fe,M)17 and Magnetic
Properties of their Nitrides and Carbides”, J. Alloys Compd., 283, 296-303 (1999) (Equi.
Diagram, Experimental, 21)
[1999Ren] Ren, Z.Y., Lee, W.-Y., Qin, C.-D., Ng, D.H.L., Ma, X.-Y., “Structural and Magnetic
Properties of Sm2Fe17–xTxM (T = Co, Ti; M = Al, Si) Compounds”, J. Appl. Phys., 85(8),
4672-4674 (1999) (Crys. Structure, Experimental, 10)
[2000Fan] Fan, G.J., Loser, W., Roth, S., Eckert, J., “Glass-Forming Ability of RE-Al-TM Alloys (RE
= Sm, Y; TM = Fe, Co, Cu)”, Acta Mater., 48(15), 3823-3831(2000) (Magn. Prop.,
Experimental, 30)
[2000Kub] Kubis, M., Eckert, D., Gebel, B., Mueller, K.-H., Schultz, L., “Intrinsic Magnetic Properties
of Sm2Fe17–xMxNy/Cy (M = Al, Ga or Si)”, J. Magn. Magn. Mater., 217, 14-18 (2000)
(Experimental, Magn. Prop., 14)
[2000Oka] Okamoto, H., Desk Handbook Phase Diagrams for Binary Alloys, ASM International,
Materials Park, OH 44073-0002 (2000)
[2000Ren] Ren, Z.Y., Ng, D.H.L., Dai, S.Y., “Structural and Magnetic Properties of Sm2Fe16MAl2 (M
= Mn, Mo; Ni) and their Carbides”, IEEE Trans., Magn., 36, 3330-3332 (2000) (Crys.
Structure, Experimental, Magn. Prop., 7)
[2000Sam] Samata, H., Kamonji, M., Sasaki, H., Yashiro, S., Kai, M., Uchida, T., Nagata, Y.,
“Magnetic Properties of Sm(Fe1–xAlx)7 Crystals”, J. Alloys Compd., 311, 130-136 (2000)
(Crys. Structure, Experimental, Magn. Prop., 13)
[2001Ike] Ikeda, O., Ohnuma, I., Kainuma, R., Ishida, K., “Phase Equilibria and Stability of Ordered
BCC Phases in the Fe-Rich Portion of the Fe-Al System”, Intermetallics, 9, 755-761 (2001)
(Thermodyn., Experimental, 18)
[2001Kon1] Kong, H.Z., Li, Y., Ding, J., “Magnetic Hardening in Amorphous Alloy Sm60Fe30Al10”,
Scr. Mater., 44(5), 829-834 (2001) (Crys. Structure, Experimental, Magn. Prop., 16)
414
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
[2001Kon2] Kong, H.Z., Ding, J., Wang, L., Li, Y., “Amorphous Magnetic RE-Fe-Al Alloys”, IEEE
Trans., Magn., 37(4), 2500-2502 (2001) (Experimental, Magn. Prop., 9)
[2001Ter] Teresiak, A., Kubis, M., Mattern, N., Mueller, K.-H., Wolf, B., “Crystal Structure of
Sm2Fe17–yMy Compounds with M = Al, Si, Ga”, J. Alloys Compd., 319, 168-173 (2001)
(Crys. Structure, Experimental, 26)
[2002Ram] Rama Rao, K. V. S., Ehrenberg, H., Markandeyulu, G., Varadaraju, U. V., Venkatesan, M.,
Suresh, K. G., Murthy, V. S., Schidt, P. C., Fuess, H., “On the Structural and Magnetic
Properties of R2Fe17–x(A,T)x (R = Rare Earth; A = Al, Si, Ga; T = Transition Metal)
Compounds”, Phys. Status Solidi A, 189A(2), 373-388 (2002) (Crys. Structure, Magn.
Prop., Review, 51)
[2002Zin] Zinkevich, M, Mattern, N., Handstein, A., Gutfleisch, O., “Thermodynamics of Fe-Sm,
Fe-H and H-Sm Systems and its Application to the Hydrogen - Disproportionation -
Desorption - Recombination (HDDR) Process for the System Fe17Sm2-H2”, J. Alloys
Compd., 339, 118-139 (2002) (Thermodyn., Assessment, 101)
[2003Bod] Bodak, O., “Al-Sm (Aluminum-Samarium)”, MSIT Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 7)
[2003Kan] Kang, Y., Chen, N., Shen, J., “Atomistic Simulation of the Lattice Constants and Lattice
Vibrations in RT4Al8 (R = Nd, Sm; T = Cr, Mn, Cu, Fe)”, J. Alloys Compd., 352, 26-33
(2003) (Crys. Structure, 40)
[2003Pis] Pisch, A., “Al-Fe (Aluminium-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 58)
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
( Fe)
1538 - 1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)
1394 - 912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2, 1993Kat]
Dissolves up to 1.2 at.% Al
( Fe)
< 912
cI2
Im3m
W
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
Pure Fe at 25°C [Mas2]
Dissolves up to 45.0 at.% Al at 1310°C
0-18.8 at.% Al, HT [1958Tay]
0-19.0 at.% Al, HT [1961Lih]
0-18.7 at.% Al, 25°C [1999Dub]
( Sm)
1074 - 922
cI2
Im3m
W
a = 410 [Mas2], dissolves up to 12 at.% Al at
760°C [1998Sac]
415
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
( Sm)
922 - 734
hP2
P63/mmc
Mg
a = 366.30
c = 584.48
[Mas2]
( Sm)
< 734
hR9
R3m
Sm
a = 362.90
c = 2620.7
at 25°C [Mas2]
Fe4Al13
< 1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7° to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
74.16-76.70 at.% Al [1986Gri]
sometimes called FeAl3 in the literature
at 76.0 at.% Al [1994Gri]
Fe2Al5< 1169
oC24
Cmcm
a = 765.59
b = 641.54
c = 421.84
at 71.5 at.% Al [1994Bur]
FeAl2< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [1993Kat]
1102 - 1232
cI16” a = 598.0 at 61 at.% Al [1993Kat]
FeAl
< 1310
cP8
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5-47.5 at.% Al [1961Lih]
36.2-50.0 at.% Al [1958Tay]
39.7-50.9 at.% Al [1997Kog] quenched
in water from 500°C
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
24- 37 at.% Al [2001Ike]
23.1-35.0 at.% Al [1958Tay]
24.7-31.7 at.% Al [1961Lih]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
Metastable
81.8 at.% Al [1993Kat]
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
Metastable
85.7 at.% Al [1993Kat]
[1998Ali]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[1998Ali]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
416
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
Sm3Al11
< 1380
tI10
I4/mmm
BaAl4
a = 428.4
c = 990
[1998Sac]
Sm3Al11
(metastable)
oI28
Immm
La3Al11
a = 433.3
b = 1281
c = 997
[V-C2]
SmAl3< 1130
hP8
P63/mmc
Ni3Sn
a = 638.2
c = 460.0
[1998Sac]
Sm(FexAl1–x)2
< 1480
SmAl2
cF24
Fd3m
MgCu2 a = 794.3
0 x 0.45 (0 to 30 at.% Fe) [1975Dwi]
[V-C2]
SmAl
< 960
oP16
Pbcm
DyAl
a = 590.1
b = 1160.2
c = 568.8
[1998Sac]
Sm2Al
< 860
oP12
Pnma
Co2Si
a = 666.2
b = 519.0
c = 962.5
[1998Sac]
Sm2Fe17
1280 - ~1200
hP38
P63/mcm
Ni17Th2
a = 849
c = 830
[1989Gle]
Sm2(Fe1–xAlx)17
Sm2Fe17
1200
hR57
R3m
Th2Zn17
a = 854 to 878.2
c = 1243 to 1275.6
a = 857.0
c = 1244.0
a = 855
c = 1244
a = 854.5 to 883.4
c = 1247.7 to 1283.1
a = 855.37 to 863.40
c = 1244.34 to 1255.29
a = 861.3
c = 1253
a = 859.1
c = 1249.4
a = 861.4
c = 1252.5
a = 859.1
c = 1248.8
a = 861.8
c = 1252.2
0 x 0.41 (annealed at 1000°C)
[1995Che]
[1971Bus]
[1989Gle]
0 x 0.56 (annealed at 800°C)
[1976McN]
0 x 0.18 (annealed at 800°C)
[1991Wei]
x = 0.12 (annealed at 1000°C) [1994Jia]
x = 0.058
x = 0.081 (single crystal, structure
refinement) [1998Ono]
x = 0.06
x = 0.12 (powders, Rietveld refinement)
[2001Ter]
SmFe3
< 1010
hR12
R3m
Ni3Pu
a = 518.7
c = 2491.0
[1971Bus]
Sm(Fe1–xAlx)2
< 900
SmFe2
cF24
Fd3m
MgCu2 a = 741.7
0 x 0.25 (0 to 17 at.% Al) [1975Dwi]
[1971Bus]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
417
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Sm
Sm(Fe1–xAlx)7 tP64
P42/mnm
a = 876
c = 1214
a = 878
c = 1215
a = 875
c = 1223
x = 0 (metastable phase) [2000Sam]
x = 0.047 [2000Sam]
x = 0.07 [2000Sam]
* 1, Sm(Fe1–xAlx)2
SmFeAl
hP12
P63/mmc
MgZn2 a = 547
c = 884
a = 536 to 540
c = 868 to 875
0.3 x 0.475 (20 to 32 at.%Al)
[1975Dwi]
at x = 0.5 [1968Dwi]
0.3 x 0.45 [1974Viv2]
* 2, Sm6Fe11Al3 tI80
I4/mcm
La6Co11Ga3
a = 811.43
c =2299.49
[1992Hu] (annealed at 800°C)
* 3, Sm(FexAl1–x)12
SmFe4Al8
tI26
I4/mmm
ThMn12
a = 881 to 871
c = 505 to 501
a = 877.3
c = 505.1
0.275 x 0.467 (25.4 - 43 at.% Fe)
[1974Viv2]
at x = 0.33 [1976Bus]
* 4, SmFe2Al10 oC52
Cmcm
YbFe2Al10
a = 898.9
b = 1018.6
c = 904.3
[1998Thi] (single crystal, structure
refinement)
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
References/Comments
20
40
60
80
20 40 60 80
20
40
60
80
Sm Fe
Al Data / Grid: at.%
Axes: at.%
τ1
SmFe2 SmFe3αSm2Fe17
FeAl
FeAl2
Fe2Al5
Fe4Al13τ4
τ3
SmAl3
SmAl2
Sm3Al11
(Al)
(αFe)
Fe3Al
Sm(FexAl1-x)2
Sm(Fe1-xAlx)2
Fig. 1: Al-Fe-Sm.
Isothermal section at
500°C
418
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Tb
Aluminium – Iron – Terbium
Gabriele Cacciamani
Literature Data
The Al-Fe-Tb phase equilibria have not been systematically investigated: [1975Oes] analyzed several
samples quenched from the melt or annealed at 1000°C along sections at constant Tb content and [2001Yan]
studied the 500°C solubility ranges of the different phases at the Tb2(Fe,Al)17 ratio. Several authors studied
the structural and magnetic properties of the Al-Fe-Tb phases: particular attention was dedicated to the solid
solutions at the Tb2(Fe,Al)17 ratio [1973Oes1, 1976Bol, 1992Jac, 1995Che, 1996Mao, 1998Yel, 2001Yan]
and to the Tb(Fe1-xAlx)12 ternary phase [1974Viv, 1976Bus, 1980Fel, 1988Che, 1997Yan, 1998Sch,
1999Sch]. Binary and (or) ternary phases at the Tb(Fe,Al)2 atomic ratio have been mainly investigated by
[1971Oes, 1973Oes2, 1973Zar, 1974Dwi, 2000Shi]. The remaining phases have been studied by [1972Oes]
and [1998Thi].
Samples have been generally prepared by arc melting the pure elements (usually 99.9 mass% pure) under
an inert atmosphere. In a few cases cold crucible induction melting [1996Mao] or synthesis in Al2O3 at 400
to 800°C [1998Thi] was used. [1975Dwi] induction melted Al-Fe master alloys with appropriate amounts
of rare earth. Samples were generally annealed at appropriate temperatures (typically 600-800°C for one or
more weeks, according to the experimental needs) and then quenched.
Binary Systems
The binary systems Al-Fe and Al-Tb are accepted from [2003Pis] and [2003Gro], respectively. The Fe-Tb
phase equilibria are accepted from [1996Oka] which is mainly based on the thermodynamic assessment by
[1994Lan].
Solid Phases
Crystal structure data are reported in Table 1. Al-Fe binary compounds and phases are not reported to
dissolve Tb. Al-Tb and Fe-Tb phases generally show more or less extended solubility ranges due to
substitution between Al and Fe.
The binary Laves phases TbAl2 [1973Oes2] and TbFe2 [1973Oes2, 2000Shi] (isostructural, MgCu2 type)
dissolve more than 20 at.% of the third element. At intermediate compositions, however, a different Laves
phase ( 1, MgZn2 type) is formed: the solubility ranges have been determined by [1975Dwi] and crystal
structures have been studied by [1971Oes, 1973Oes2, 1973Zar, 1974Dwi, 2000Shi]. According to
[1974Dwi] the cubic MgCu2 cell of TbFe2 shows a rhombohedral distortion which decreases with
increasing Al content. [1972Oes] found the Tb6Fe23 phase to dissolve an appreciable amount of Al.
The 2 phase has been observed only by [1975Oes] and no isostructural phases have been found in other
systems with similar rare earths: its existence has then to be considered doubtful.
The solid solutions at the Tb2(Fe,Al)17 ratio have been studied by different authors, sometime with
contradictory results. The recent results by [2001Yan] (lattice parameters and solubility ranges at 500°C)
seem particularly accurate. However it has to be considered that the range of stability of the different
structures is probably appreciably dependent on temperature. According to [1996Mao] a TbFe7 metastable
phase with the TbCu7 type structure is present also in the Fe-Tb binary sub-system.
The 4 phase has been studied by several authors at the TbFe4Al8, [1974Viv], TbFe6Al6 [1980Fel,
1988Che, 1998Sch] and TbFe5Al7 [1997Yan] compositions. Also in this case the solubility range
appreciably varies with temperature.
Finally, with the same Tb(Fe,Al)12 ratio, a different ternary phase ( 5, at the composition TbFe2Al10) was
studied by [1998Thi].
419
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Tb
Isothermal Sections
Partial indications on isothermal phase equilibria at different temperatures have been reported in literature,
especially by [1975Oes] and [2001Yan]. However it is not possible to draw any reliable isothermal section
at a defined temperature. Data about the composition ranges of the solid solutions are reported in Table 1.
Notes on Materials Properties and Applications
Structural and magnetic ordering in the Laves phases has been studied by [1975Dwi] by Mössbauer
measurements.
Magnetic properties have been studied for 4 at different compositions: TbFe4Al8 [1978Bus, 1988Sch,
1999Sch, 2000Duo, 2000Sik] (magnetic properties have been studied as a function of temperature and
magnetization direction; coercivities extremely large at low temperatures have been revealed), TbFe6Al6[1981Fel, 1988Che, 1998Sch] (ferrimagnetic ordering occurs at about 340 K), TbFe4.4Al7.6 [2001Duo,
2002Duo] (observation of a field-induced transformation from easy-plane antiferromagnetic to easy-axis
ferrimagnetic structure at 5 K and determination of the intersublattice-coupling constant), and for 5
[1998Thi, 2000Ree] (magnetic properties have been determined by a SQUID magnetometer in the 2-300 K
temperature range; antiferromagnetic order below 14 K was observed), 1, Tb(Fe1-xAlx)2 [1973Oes1,
2000Shi] (magnetostriction measured also in samples where Al was partially substituted by Mn) and the
phases at the Tb2(Fe,Al)17 ratio [1995Che, 1996Mis] (changes in magnetic anisotropy and Mössbauer
studies). Magnetic properties have been reviewed by [1994Liu, 2002Ram].
References
[1971Oes] Oesterreicher, H., “Structural Studies of Rare-Earth Compounds RFeAl”, J. Less-Common
Met., 25, 341-342 (1971) (Crys. Structure, Experimental, 6)
[1972Oes] Oesterreicher, H., Pitts, R., “The Th6Mn23 Structure at an Unusual Composition
Tb0.167Fe0.693Al0.20”, J. Less-Common Met., 29,100-103 (1972) (Crys. Structure,
Experimental, 9)
[1973Oes1] Oesterreicher, H., “X-Ray and Neutron Diffraction Study of Ordering on Crystallographic
Sites in Rare-Earth-Base Alloys Containing Al and Transition Metals”, J. Less-Common
Met., 33, 25-41 (1973) (Crys. Structure, Experimental, 19)
[1973Oes2] Oesterreicher, H., “Structural, Magnetic and Neutron Diffraction Studies on TbFe2-TbAl2,
TbCo2-TbAl2 and HoCo2-HoAl2”, J. Phys. Chem. Solids, 34, 1267-1280 (1973) (Crys.
Structure, Experimental, Magn. Prop., 30)
[1973Zar] Zarechnyuk, O.S., Rikhal, R.M., Vivchar, O.I., “Laves Phases in Ternary Systems of the
Type Rare-Earth Metal-Transition Metal-Al” (in Russian), Akad. Nauk Ukr. SSR,
Metallofiz., 46, 92-94 (1973) (Crys. Structure, Experimental, 22)
[1974Dwi] Dwight, A.E., Kimball, C.W., “TbFe2, a Rhombohedral Laves Phase”, Acta Crystallogr,
Ser. B: Struct. Crystallogr. Crys. Chem., B30, 2791-2793 (1974) (Crys. Structure,
Experimental, 12)
[1974Viv] Vivchar, O.I., Zarechnyuk, O.S., “Compounds of the ThMn12-type Structure in R-Fe-Al
Systems” (in Russian), Tezisy. Dokl. - Vses. Konf. Kristallokhim. Intermet. Soedin.,
Rykhal, R.M. (Ed.), Vol. 2, L'vov. Gos. Univ.: Lvov, USSR., 41 (1974) (Crys. Structure,
Experimental, 0)
[1975Dwi] Dwight, A.E., Kimball, C.W., Preston, R.S., Taneja, S.P., Weber, L., “Crystallographic and
Mössbauer Study of (Sc, Y, Ln)(Fe, Al)2 Intermetallic Compounds”, J. Less-Common Met.,
40, 285-291 (1975) (Crys. Structure, Moessbauer, Experimental, 8)
[1975Oes] Oesterreicher, H., “Structural Studies on Materials from TbFe3 to Tb2Fe17 with Al
Substitution for Fe”, J. Less-Common Met., 40(2), 207-219 (1975) (Crys. Structure,
Experimental, 29)
420
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Tb
[1976Bol] Boller, H., Oesterreicher, H., “Tb2(Fe0.832Al0.168)17: A Simple Crystal Structure Derived
by Disordered Substitution in the Th2Ni17 Type”, J. Less-Common Met., 45, 103-109
(1976) (Crys. Structure, Experimental, 11)
[1976Bus] Buschow, K.H.J., Van Der Vucht, J.H.N., Van Den Hoogenhof, W.W., “Note on the Crystal
Structure of the Ternary Rare Earth-3d Transition Metal Compounds of the Type RT4Al8”,
J. Less-Common Met., 50, 145-150 (1976) (Crys. Structure, Experimental, 2)
[1978Bus] Buschow, K.H.J., Van der Kran, A.M., “Magnetic Ordering in Ternary Rare Earth Iron
Aluminium Compounds (RFe4Al8)”, J. Phys. F: Met. Phys., 8, 921-932 (1978)
(Experimental, Magn. Prop., 9)
[1980Fel] Felner, I., “Crystal Structures of Ternary Rare Earth-3d Transition Metal Compounds of the
RT6Al6 Type”, J. Less-Common Met., 72, 241-249 (1980) (Crys. Structure, Experimental,
10)
[1981Fel] Felner, I., Seh, M., Rakavy, M., Nowik, I., “Magnetic Order and Hyperfine Interactions in
RFe6Al6 (R = Rare Earth)”, Phys. Chem. Solids, 42, 369-377 (1981) (Crys. Structure, Magn.
Prop., Experimental, 6)
[1988Che] Chelkowska, G., Chelkowska, A., Winiarska, A., “Magnetic Susceptibility and Structural
Investigations of Rare Earth-Aluminium-Iron (REAl6Fe6) Compounds for RE = Yttrium,
Terbium, Dysprosium, Holmium, and Erbium”, J. Less-Common Met., 143, L7-L10 (1988)
(Crys. Structure, Magn. Prop., Experimental, 12)
[1988Sch] Schaefer, W., Groenefeld, M., Will, G., Gal, J., “Magnetic Helical Ordering in Intermetallic
Rare Earth-Iron-Aluminum Compounds”, Mater. Sci. Forum, 27-28, 243-248 (1988) (Crys.
Structure, Magn. Prop., Experimental, 9)
[1992Jac] Jacobs, T.H., Buscow, K.H.J., Zhou, G.F., Li, X., de Boer F.R., “Magnetic Interactions in
R2Fe17-xAlx Compounds (R = Ho, Y)”, J. Magn. Magn. Mater, 116(1-2), 220-230 (1992)
(Magn. Prop., Experimental, 15)
[1994Liu] Liu, J.P., Boer, F.R. de, Chatel, P.F. de, Coehoorn, R., Buschow, K.H.J., “On the 4f-3d
Exchange Interaction in Intermetallic Compounds”, J. Magn. Magn. Mater., 132, 159-179
(1994) (Magn. Prop., Review, 64)
[1994Lan] Landin, S., Agren, J., “Thermodynamic Assessment of Fe-Tb and Fe-Dy Phase Diagrams
and Prediction of the Fe-Tb-Dy Phase Diagram”, J. Alloys Compd., 207/208, 449-453
(1994) (Equi. Diagram, Assessment)
[1995Che] Cheng, Z., Shen, B., Liang, B., Zhang, J., Wang, F., Zhang, S., Gong, H., “The Change in
Magnetic Anisotropy in R2Fe17-xAlx Compounds (R = Sm or Tb)”, J. Phys.: Condens.
Matter, 7, 4707-4712 (1995) (Crys. Structure, Experimental, Magn. Prop., 16)
[1996Mao] Mao, O., Yang, J., Altounian, Z., Stroem-Olsen, J.O., “Metastable RFe7 Compounds (R =
Rare Earths and Their Nitrides with TbCu7 Structure)”, J. Appl. Phys., 79(8), 4605-4607
(1996) (Crys. Structure, Magn. Prop., Experimental, 5)
[1996Mis] Mishra, S.R., Long, G.J., Pringle, O.A., Marasinghe, G.K., Middleton, D.P., Buschow,
K.H.J., Grandjean, F., “A Magnetic and Moessbauer Spectral Study of the Tb2Fe17-xAlxSolid Solutions”, J. Magn. Magn. Mater., 162, 167-176 (1996) (Crys. Structure,
Experimental, 30)
[1996Oka] Okamoto, H., “Fe-Tb (Iron – Terbium)”, J. Phase Equilib., 17, 165 (1996) (Equi. Diagram,
Assessment, 5)
[1997Yan] Yanson, T.I., Manyako, M.B., Bodak, O.I., Cerny, R., Pacheko, J.V., Yvon, K., “Crystal
Structure of Terbium Iron Aluminide, TbFexAl12-x (x = 4.28), Lutetium Iron Aluminide,
LuFexAl12-x (x = 4 and 6.1), and Lanthanum Iron Aluminide, LaFexAl12-x (x = 4)”, Z.
Kristallogr. NCS, 212, 505-507 (1997) (Crys. Structure, Experimental, 6)
[1998Sch] Schaefer, W., Kockelmann, W., Jansen, E., Fredo, S., Gal, J., “Structural Characteristics of
Rare Earth (R = Tb, Ho, Er) Ternary Magnetic Intermetallics RFexAl12-x with Iron
Concentrations x = 6”, Mater. Sci. Forum, 278-281, 542-547 (1998) (Crys. Structure, Magn.
Prop., Experimental, 14)
421
Landolt-BörnsteinNew Series IV/11A2
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Al–Fe–Tb
[1998Thi] Thiede, V.M.T., Ebel, T., Jeitschko, W., “Ternary Aluminides LnT2Al10 (Ln = Y, La-Nd,
Sm, Cd-Lu and T = Fe, Ru, Os) with YbFe2Al10 Type Structure and Magnetic Properties of
the Iron-Containing Series”, J. Mater. Chem., 8(1), 125-130 (1998) (Crys. Structure, Magn.
Prop., Experimental, 31)
[1998Yel] Yelon, W.B., Luo, H., Chen, M., Chang, W.C., Tsai, S.H., “A Neutron Diffraction
Structural Study of R2Fe17-xAlx(C) (R = Tb, Ho) Alloys”, J. Appl. Phys., 83(11), 6914-6916
(1998) (Crys. Structure, Experimental, 14)
[1999Sch] Schobinger-Papamantellos, P., Buschow, K.H.J., Hagmusa, I.H., de Boer, F.R., Ritter, C.,
Fauth, F., “Magnetic Ordering of TbFe4Al8 Studied by Neutron Diffraction. I”, J. Magn.
Magn. Mater., 202, 410-425 (1999) (Crys. Structure, Experimental, 25)
[2000Duo] Duong, N.P., Hagmusa, I.H., Brueck, E., de Boer, F.R., Buschow, K.H.J., “Magnetic
Properties of TbFe4Al8”, J. Alloys Compd., 313, 21-25 (2000) (Crys. Structure,
Experimental, Magn. Prop., 16)
[2000Ree] Reehuis, M., Fehrmann, B., Wolff, M.W., Jetschko, W., Hofmann, M., “Antiferromagnetic
Order in TbFe2Al10 and DyFe2Al10”, Physica B, 276-278, 594-595 (2000) (Crys. Structure,
Experimental, Magn. Prop., 4)
[2000Shi] Shin, J.-C., Hsu, S.-Y., Chao, L.-J., Chin, T.-S., “The Magnetostriction of
Tb(Fe0.9MnxAl0.1-x)2 Alloys”, J. Appl. Phys., 88(6), 3541-3544 (2000) (Crys. Structure,
Experimental, Phys. Prop., 19)
[2000Sik] Sikora, W., Schobinger-Papamantellos, P., Buschow, K.H.J., “Symmetry Analysis of the
Magnetic Ordering in RFe4Al8 (R = La, Ce, Y, Lu and Tb) Compounds (II)”, J. Magn.
Magn. Mater., 213, 143-156 (2000) (Calculation, Crys. Structure, Magn. Prop., 8)
[2001Yan] Yanson, T., Manyako, M., Bodak, O., Cerny, R., Yvon, K., “Effect of Aluminium
Substitution and Rare-Earth Content on the Structure of R2(Fe1-xAlx)17 (R = Tb, Dy, Ho,
Er) Phases”, J. Alloys Compd., 320(1), 108-113 (2001) (Crys. Structure, Equi. Diagram,
Experimental, 9)
[2002Duo1] Duong, N.P., Brueck, E., de boer, F:R., Buschow, K.H.J., “Magnetic Properties of
GdFe5Al7 and TbFe4.45Al7.55”, J. Alloys Compd., 338, 213-217 (2002) (Crys. Structure,
Experimental, Magn. Prop., 5)
[2002Duo2] Duong, N.P., Brueck, E., Brommer, P.E., de Visser, A., de Boer, F.R., Buschow, K.H.J.,
“Extraordinary Magnetization Behavior of SingleCrystalline TbFe4.4Al7.6”, Phys. Rev. B,
65(2), 020408-1 - 020408-4 (2002) (Experimental, Magn. Prop., 8)
[2002Ram] Rama Rao, K.V.S., Ehrenberg, H., Markandeyulu, G., Varadaraju, U.V., Venkatesan, M.,
Suresh, K.G., Murthy, V.S., Schidt, P.C., Fuess, H., “On the Structural and Magnetic
Properties of R2Fe(17-x)(A, T)x (R = Rare Earth, A = Al, Si, Ga, T = Transition Metal)
Compounds”, Phys. Status Solidi A, 189A(2), 373-388 (2002) (Crys. Structure, Magn.
Prop., Review, 51)
[2003Grö] Gröbner, J., Matusch, D., Turkevich, V., “Al-Tb (Aluminum – Terbium)”, MSIT Binary
Evaluation Program, in MSIT Workplace, Effenberg, G. (Ed.), MSI, Materials Science
International Services GmbH, Stuttgart; to be published, (2003) (Crys. Structure, Equi.
Diagram, Assessment, 5)
[2003Pis] Pisch, A., “Al-Fe (Aluminium-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Crys. Structure, Equi. Diagram, Assessment, 58)
422
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Al–Fe–Tb
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments
( Al) hP2
P63/mmc
Mg
a = 269.3
c = 439.8
at 25°C, 20.5 GPa [Mas2]
( Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe) hP2
P63/mmc
Mg
a = 246.8
c = 396.0
at 25°C, 13 GPa [Mas2]
( Fe)
1538-1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)
1394-912
cF4
Fm3m
Cu
a = 364.67 at 915°C [V-C2, Mas2]
dissolves up to 1.2 at.% Al
( Fe)
< 912
cI2
Im3m
W
a = 286.65
a = 286.64 to 289.59
a = 286.60 to 289.99
a = 286.60 to 290.12
pure Fe at 25°C [Mas2]
dissolves up to 45.0 at.% Al at 1310°C
0-18.8 at.%Al, HT [2003Pis]
0-19.0 at.% Al, HT [2003Pis]
0-18.7 at.% Al, 25°C [2003Pis]
( Tb) HP hR3
R3mW
a = 341
c = 2450
at 25°C, 6 GPa [Mas2]
( Tb)
1356 - 1289
cI2
Im3m
W
a = 402 [Mas2]
( Tb)
1289 – (-53)
hP2
P63/mmc
Mg
a = 360.55
c = 569.66
at 25°C [Mas2]
( 'Tb)
< -53
oC4
Cmcm
'Dy
a = 360.55
c = 569.66
at 25°C [Mas2]
Fe4Al13
< 1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7° to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
74.16-76.70 at.% Al [2003Pis]
sometimes called FeAl3 in the
literature
at 76.0 at.% Al [2003Pis]
423
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Tb
Fe2Al
5< 1169
oC24
Cmcm
Fe2Al
5
a = 765.59
b = 641.54
c = 421.84
at 71.5 at.% Al [2003Pis]
FeAl2
< 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
at 66.9 at.% Al [2003Pis]
1102 - 1232
cI16?
-
-
a = 598.0 at 61 at.% Al [2003Pis]
FeAl
< 1310
cP8
Pm3m
CsCl
a = 289.48 to 290.5
a = 289.53 to 290.9
a = 289.81 to 291.01
a = 289.76 to 190.78
34.5 - 47.5 at.% Al [2003Pis]
36.2 - 50.0 at.% Al [2003Pis]
39.7 - 50.9 at.% Al [2003Pis] 500°C
quenched in water
room temperature
Fe3Al
< 547
cF16
Fm3m
BiF3
a = 579.30 to 578.86
a = 579.30 to 578.92
~24 - ~37 at.% Al [2003Pis]
23.1 - 35.0 at.% Al [2003Pis]
24.7 - 31.7 at.% Al [2003Pis]
Fe2Al9 mP22
P21/c
Co2Al9
a = 869
b = 635
c = 632
= 93.4°
metastable
81.8 at.% Al [2003Pis]
FeAl6 oC28
Cmc21
FeAl6
a = 744.0
b = 646.3
c = 877.0
a = 744
b = 649
c = 879
metastable
85.7 at.% Al [2003Pis]
[2003Pis]
FeAl4+x t** a = 884
c = 2160
(0 < x < 0.4) metastable
[2003Pis]
TbAl3< 1108
hR12
R3m
BaPb3
a = 617.6
c = 2116.5
[Mas2]
TbAl3(HP) hR20
R3m
HoAl3
a = 609.5
c = 3596
high pressure phase [V-C2]
Tb(FexAl1-x)2
TbAl2 < 1514
cF24
Fd3m
MgCu2
a = 786.5 to 770.7
a = 785.9
0 x 0.41 [1975Dwi]
at x = 0 – 0.37 [1973Oes2]
[Mas2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments
424
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Tb
TbAl
< 1079
oP16
Pmma
ErAl
a = 583
b = 1137
c = 562
[V-C2]
Tb3Al2 tP20
P42/mnm
Zr3Al2
a = 825.5
c = 756.8
[V-C2]
Tb2Al oP12
Pnma
Co2Si
a = 659.2
b = 511.3
c = 944.0
[Mas2]
Tb3Al cP4
Pm3m
Cu3Au
a = 479.4 [V-C2]
Tb(Fe1-xAlx)2
TbFe2
< 1187
cF24
Fd3m
MgCu2
a = 735.1 to 748.1
a = 739.07
a = 734.38
0 x 0.33 [1975Dwi]
at x = 0 - 0.26 [1973Oes2]
at x = 0.1 [2000Shi]
at x = 0 [V-C2]
Tb(Fe1-xAlx)2
TbFe2
hR*
R3m
a = 518.9
c = 1282.1
0 x 0.25 [1974Dwi]
at x = 0 rhombohedral distortion of the
cubic MgCu2 structure (decreasing
with increasing Al content) [1974Dwi]
TbFe3
< 1217
hR36
R3m
PuNi3
a = 511
c = 2442
[V-C2]
Tb6(Fe1-xAlx)23
Tb6Fe23
< 1276
cF116
Fm3m
Th6Mn23
a = 1217.3
a = 1207
at x = 0.25 [1972Oes]
at x = 0.0 [V-C2]
Tb2-y(Fe1-xAlx)17
Tb2Fe17
< 1312
hP38
P63/mmc
Th2Ni17 a = 853.2
c = 834.9
a = 848.7 to 859.1
c = 832.4 to 836.2
a = 845.1
c = 829.8
0 x 0.22 at 500°C
0 y 0.2 at 500°C [2001Yan]
at x = 0.19 [1973Oes2]
at x = 0 - 0.20, T = 500°C [2001Yan]
at x = 0.0 [V-C2]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments
425
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Tb
Tb2+y(Fe1-xAlx)17
Tb2Fe17
hR19
R3m
Th2Zn17
a = 852 to 866
c = 1241 to 1261
a = 857.68 to 862.12
c = 1251.91 to 1258.72
a = 872.6 to 876.1
c = 1266.3 to 1268.6
a = 875.6 to 880.7
c = 1264.5 to 1274.4
a = 854
c = 1243
0 x 0.56 at 500°C [2001Yan]
0 y 0.19 at 500°C at 52-60 at.%
Al [2001Yan]
at x = 0 - 0.3, T = 1000°C [1995Che]
at x = 0.12 - 0.24, T = 1100°C, neutron
diffraction [1998Yel]
at x = 0.40 - 0.47, T = 900°C [1992Jac]
at x = 0.45 - 0.56, T = 500°C,
[2001Yan]
at x = 0 [V-C2]
* 1, Tb(Fe1-xAlx)2 hP12
P63/mmc
MgZn2
a = 532.4 to 539.9
c = 875.8 to 872.1
a = 539.9
c = 872.1
a = 532.4
c = 870.6
0.35 x 0.54 [1975Dwi]
at x = 0.33 - 0.51 [1973Oes2]
at x = 0.5 [1971Oes]
TbFeAl
at x = 0.338 [1973Oes2]
* 2, Tb(Fe1-xAlx)3 hP24
P63/mmc
CeNi3
a = 522.6
c = 1679.4
0.20 x 0.33 at 1000°C
at x = 0.25 [1975Oes]
* 3, Tb(Fe1-xAlx)7 hP8
P6/mmm
TbCu7
a = 496.0 to 497.0
c = 420.1 to 420.3
a = 490
c = 418
0.23 x 0.26 at 500°C [2001Yan]
at x = 0, from graph in [1996Mao]
(metastable in the binary)
'3, Tb2(Fe1-xAlx)17 h**
P622
a = 853.2
c = 417.5
at x = 0.17, T = 800°C, disordered
derivative of Th2Ni17 [1976Bol]
(possibly the Tb(Fe1-xAlx)7 phase?)
* 4, Tb(FexAl1-x)12 tI26
I4/mmm
ThMn12
a = 874.9
c = 504.3
a = 874.0
c = 501.8
a = 865.1
c = 502.9
a = 865.1
c = 502.9
a = 868.1
c = 504.6
a = 874.3
c = 505.6
0.33 x 0.50
at x = 0.33 [1976Bus]
TbFe4Al8at x = 0.33 [1974Viv]
TbFe4Al8at x = 0.5 [1980Fel]
TbFe6Al6at x = 0.5 [1988Che]
at x = 0.5, neutron diffraction
[1998Sch]
at x = 0.36 [1997Yan]
* 5, TbFe2Al10 oC52
Cmcm
YbFe2Al10
a = 896.3
b = 1014.9
c = 901.3
[1998Thi]
Phase/
Temperature Range
[°C]
Pearson Symbol/
Space Group/
Prototype
Lattice Parameters
[pm]
Comments
426
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
Aluminium – Iron – Titanium
Gautam Ghosh
Literature Data
Certain alloy compositions of this system are of technological interest in many applications, such as
elevated-temperature structural alloys, surgical implants and hydrogen storage. As a result a large number
of experimental studies have been carried out to determine the phase equilibria. Earlier investigations are
due to [1940Nis, 1954Sto, 1958Bok, 1958Kor, 1963Luz, 1969Vol, 1970Vol, 1971Vol, 1973Mar] and
[1981Sei]. [1969Vol] used electrolytic Fe, “iodide” Ti and AV-000 grade Al. The alloys were annealed at
800°C (200-400 h), 700°C (300 h) and 500°-600°C (1000 h). After annealing they were water quenched.
Thermal analysis and phase analysis by X-ray diffraction and microstructural observation were performed.
Volkova et al. presented temperature-composition sections [1969Vol], isothermal sections at 1100, 800 and
550°C [1970Vol, 1971Vol]. [1981Sei] used electrolytic Fe, Ti sponge and 99.99% purity Al. First, the Fe-Ti
alloys were prepared by electron-beam melting and then the ternary alloys were made in an arc furnace
using an argon atmosphere. X-ray diffraction, metallographic analysis and microhardness tests were
conducted by [1981Sei] on about 80 ternary alloys. [1981Sei] presented a liquidus surface, a complete
isothermal section at 800°C, and a partial isothermal section at room temperature. A critical assessment of
these results along with several amendments of liquidus surface of [1981Sei] were presented by [1987Rag].
[1990Kum] presented a brief review of the phase equilibria.
[1987Men] studied order-disorder transitions involving ( Fe), B2 ( 2) and D03 ( 1)phases using five
ternary alloys of Fe-(17.3 to 25.2) at.% Al-(4.4 to 5.2) at.% Ti. They carried out the transmission electron
microscopic investigations to establish phase relations in the temperature range of 400 to 1000°C.
[1989Maz] produced 50 to 100 g ingots of nine ternary alloys in the composition range of Al-(16.6 to 34.1)
at.% Ti-(1.6 to 17.8) at.% Fe. The alloys were prepared by arc melting in vacuum. Some alloys were
annealed at 1200°C for 500 h in Ar-atmosphere, some were annealed subsequently at 800°C for 300 h. The
samples were chemically analyzed to determine their final composition and then examined by
metallography, X-ray diffraction and electron microprobe. It was reported that the O and N impurity levels
remained below 500 ppm by mass. [1991Nwo] determined the ( Ti)+( Ti) two-phase field at 700 and
800°C by annealing alloys for 10 h at 800°C and 30 h at 700°C. The alloys were prepared using elements
of following purity: Ti 99.5%, Al 99.99% and Fe 99.9%. The phases were detected by X-ray diffraction,
SEM and TEM and quantitatively analyzed by EDAX. These along with the earlier results were reviewed
by [1992Gho]. [1993Rag] presented an update of phase equilibria based on the published results between
1985 and 1992.
In a significant contribution, [1995Pal] determined two complete isothermal sections at 800 and 1000°C.
They prepared 59 ternary alloys in a crucible-free levitation furnace and cast into a copper mold. They used
elements of following purity: 99.99% Al, 99.97% Fe and 99.77% Ti. Prepared samples were encapsulated
in quartz ampoules and heat treated at 1000 and 800°C for 100 and 500 h, respectively, followed by
quenching in brine solution. In addition, they also performed six diffusion couple experiments at 1000°C.
The phase equilibria were studied by metallography, SEM, EPMA and XRD.
[1995Yan1] investigated the phase equilibria at 800°C using nine ternary alloys in the composition range
of Al-(0.5 to 8) at.% Fe-(25 to 35) at.% Ti. They used elements of purity of 99.999% Al, 99% Fe and 99%
Ti. The final heat treatment was at 800°C for 10 days. They employed SEM/EDX and TEM techniques to
identify the phases. [1998Ohn] studied the order-disorder transitions in Fe-rich alloys, and reported three
temperature-composition sections, and two isothermal sections of Fe-corner at 800 and 900°C. They
prepared 24 ternary alloys and several diffusion couples to study order-disorder transitions, and to
determine the phase equilibria using DSC/DTA, EPMA and TEM techniques. [1999Gor] investigated the
phase equilibria in ten ternary alloys that were heat treated at 1000°C for 96 h. Phase equilibria were
determined by metallography, EPMA and XRD. Supplementing the results of [1995Pal], [1999Gor]
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presented an updated isothermal section at 1000°C. [1999Li] studied the effect of 1 at.% Fe on the
Ti3Al-TiAl phase boundaries between 1000 and 1250°C.
The phase equilibria of Ti-rich alloys were investigated by [2000Kai1] and [2000Kai2]. [2000Kai1]
prepared alloys in the composition range of Ti-(35 to 47) at.% Al-(0.5 to 12) at.% Fe using 99.99% Al,
99.99% Fe and 99.7% Ti. The final heat treatments were at 1000°C for either 168 or 504 h, at 1200°C for
168 h, and at 1300°C for 24 h. They determined the tie-line compositions involving ( Ti), ( Ti) and TiAl
phases using EPMA. [2000Kai2] investigated the order-disorder transitions (A2 B2), and determined
tie-line compositions involving ( Ti), ( Ti) and FeTi phases in Ti-rich area at 1000°C. They used ternary
alloys in the composition range of Ti-(11 to 27) at.% Al-(3 to 25) at.% Fe. Furthermore, the tie-line
compositions were in diffusion couples equilibrated at 1000°C. [2000Mab] also investigated the phase
equilibria of Al-rich alloys in the composition range of Al-(2 to 14) at.% Fe-(25 to 40) at.% Ti. They
produced samples as sintered compacts and ingots. For sintered compacts the starting powders of 99.9% Al,
99.9% Fe and 99.5% Ti were used, and for ingots elements of purity of 99.99% Al, 99.9% Fe and 99.7% Ti
were used. The final heat treatments for the sintered compacts were at 1150°C for 24 h and at 1000°C for
48 h, while the ingots were heat treated at 1150°C for 48 h and at 1000°C for 144 h. The phase equilibria
were studied by SEM, EPMA, TEM and XRD. [2002Rag] presented a further update of phase equilibria
based on the published results between 1981 and 2000.
Very recently, [2001Pra] reported the phase compositions of eight as-cast ternary alloys. They found that
except for two alloys lying in the Fe2Ti+L21 field, the phase compositions agree with the previously
reported 800°C isothermal section due to Palm et al [1995Pal]. In a more recent significant work, Ducher
et al [2003Duc] re-investigated the liquidus surface using 38 alloys selected from those used by Palm et al
[1995Pal]. [2003Duc] used DTA, metallography, SEM/EDX and XRD to identify the reactions during
solidification. Based on their extensive results, a reaction scheme was proposed.
Binary Systems
The Al-Fe, Al-Ti and Fe-Ti binary phase diagrams are accepted from [2003Pis], [2003Sch] and [1982Kub],
respectively.
The Al-Fe phase diagram has undergone slight modification due to recently established congruent melting
behavior of the Fe4Al13 phase [1986Len]. The Al-Ti binary phase diagram is accepted from the recent
review of [2003Sch]. The system is characterized by the presence of five intermediate phases and eight
invariant reactions. [2003Sch] accepted the invariant temperatures based on a CALPHAD modeling of the
phase equilibria. However, in this assessment the temperature of the peritectoid reaction
TiAl+Ti2Al5 TiAl2 is taken as 1205°C [1991Mis] rather than 1199°C [2003Sch] for the reasons discussed
in “Invariant Equilibria”.
Solid Phases
The Fe3Al ( 1) phase dissolves a significant amount of Ti [1973Mar] and [1977Ath]. Addition of Ti in
Fe3Al increases both the D03 B2 and B2 A2 [1987Men, 1987For, 1994Sel, 1995Ant, 1996Pra, 1997Nis1,
1997Nis2, 1998Ohn, 1999Mek, 2003Ste] transition temperatures. For example, the increase in D03 B2
transition temperature of Fe3Al is about 60°C/at.% Ti [1995Ant]. Addition of Ti also increases the Curie
temperature [1994Sel] and lattice parameter of Fe3Al [1996Pra, 1997Nis2]. The details of substitution of
Fe by Ti have been studied using X-ray diffraction, transmission electron microscopy and Mössbauer
spectroscopy [1977Ath, 1995Mah]. The Mössbauer spectroscopic data show that Ti replaces Fe at a specific
lattice site with 8 nearest Fe atoms rather than a site with 4 Fe and 4 Al nearest atoms [1977Ath, 1995Mah].
This implies that TiFe2Al is a Heusler phase (L21) [1985Okp, 1995Mah] and not (Fe,Ti)3Al (D03).
The FeAl ( 2) phase also dissolves a significant amount of Ti [1995Pal, 1998Ohn, 1999Gor, 2002Aze]
leading to an increase in lattice parameter. For example, the lattice parameter of Fe0.7-xTixAl0.3 can be
expressed as [2002Aze]
a (in pm) = 291.0 + 9.2 x.
[1997And] determined the site occupancy of Ti in Fe50Al45Ti5 and Fe52Al45Ti3 ( 2) alloys by ALCHEMI
(Atom Location by CHanneling Enhanced MIcroanalysis) in TEM, and found that about 85% of the
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“Al-site” is occupied by Ti. The residual “Fe-site” occupancy is attributed to the kinetics of site-equilibrium
mechanism. The Fe4Al13, Fe2Al5 and FeAl2 phases can dissolve up to 6.5, 2.5 and 1.8 at.% Ti, respectively
[1995Pal]. At room temperature, Fe4Al13 can dissolve about 2.5 at.% Ti [1981Zhu].
The TiFe phase dissolves a substantial amount of Al [1980Dew, 1981Sei, 1995Pal, 1999Gor]. The
maximum solubilities at 800, 900 and 1000°C are 13, 24 and 33 at.% Al, respectively [1999Pal, 1999Gor].
The substitution of Al in TiFe causes a linear increase in lattice parameter [1980Dew, 1995Pal, 1999Lee].
For example, the lattice parameter (a) of Ti(Fe,Al) can be expressed as [1995Pal]
a (in pm) = 297.0 + 5.07 (50-xFe),
where xFe is the Fe-content in at.%. This is also in good accord with the lattice parameter reported by
[1980Dew].
The Laves phase TiFe2 also dissolves a substantial amount of Al [1967Mar, 1973Mar, 1974Dwi, 1980Dew,
1995Pal, 1999Gor]. The data of [1973Mar] show a linear increase of both a and c lattice contents as Al
replaces Fe in TiFe2. However, recent measurements by [1995Pal] show a linear increase of the a lattice
constant while a non-linear increase of the c lattice constant of Ti(Fe,Al)2 as
a (in pm) = 477.7 + 0.506 (70- xFe)
c (in pm) = 778.3 + 1.406 (70- xFe)-6.78532x10-3 (70- xFe)2
where xFe is the Fe-content in at.%.
Among the Al-Ti intermetallics, TiAl3, Ti2Al5, TiAl2, TiAl and Ti3Al can dissolve up to 1.2, 0.8, 2.5, 2.5
and 1.5 at.% Fe at 1000°C, respectively [1995Pal]. [2001Sun] obtained 1.92 at.% Fe in the TiAl phase in a
Ti52Fe2Al46 alloy that heat treated at 900°C for 8 h. [1985Pas] reported 0.5 at.% Fe in TiAl at 550 to 600°C.
All these results clearly demonstrate that the solubility of Fe in TiAl increases with temperature.
Furthermore, results of ALCHEMI experiments in TEM show that Fe atoms reside primarily on the Al-site
in TiAl structure [1999Hao, 2000Yan]. Due to low solubility, the site occupancy of Fe in Ti3Al could not
be determined conclusively [1999Hao].
The ternary phases accepted in this assessment are 2 (TiFeAl2) and 3 (Ti8Fe3Al22). The 2 phase was
discovered by [1967Mar], and subsequently confirmed by [1980Dew] and [1981Sei]. It forms by a
peritectic reaction at about 1225°C [2003Duc]. [1973Mar] reported that the homogeneity range of the 2
phase at 800°C is from 40 to 50 at.% Al at 24 at.% Fe, and that reported by [1981Sei] is from 53 to 55.5
at.% Al and 21 to 24 at.% Fe. [1980Dew] reported that the homogeneity range of the 2-phase at 1000°C is
from 28 to 52 at.% Al at 25 at.% Fe. Recent results of [1995Pal] show that 2 phase split into two islands at
1000°C, one with homogeneity range of 30 to 39 at.% Al, and the other with a homogeneity range of 44.5
to 54.5 at.% Al. Also, [1995Pal] reported that the ambient crystal symmetry of 2 changes from cubic, when
the Ti-content is in the range of 30.8 to 50.9 at.%, to tetragonal when the Ti-content is less than 24 at.%.
[1999Lev] also observed both cubic and tetragonal phases in a Al-49.6 at.% Ti-1.9 at.% Fe alloy that was
heat treated at 1400 and 1300°C for 40 min and 90 min, respectively, water quenching or furnace cooling.
The Ti-content in the tetragonal phase was less 16 at.%. [1999Lev] concluded that the tetragonal- 2 is a
metastable phase, and it forms from Ti(Fe,Al) by a massive transformation. Very recently, [2001Tok]
characterized the present in a Ti-1.9 at.% Fe-46.9 at.% Al alloy that was heat treated at 1200°C for 8 h
followed by water quenching or furnace cooling. They found the cubic- 2 (Ti38Fe23Al39) in furnace cooled
specimen while the tetragonal- 2’ (Ti52Fe10Al38) in water quenched specimen. A recent single crystal
X-ray study for the 2 phase revealed a slightly modified Th6Mn23 type structure by filling the octahedral
void of Th6Mn23 by Al/Ti-atoms [2003Gry].
The 3 phase was first reported by [1973Mar], and subsequently confirmed by [1980Dew], [1981Sei] and
[1991Nic]. [1981Sei] designated the composition of 3 as Ti24Fe9Al66, while [1989Maz] reported
Ti28Fe8Al64. All subsequent investigations also confirmed a homogeneity range [1992Dur1, 1992Win,
1993Nak, 1995Pal, 1995Yan1, 1999Yam, 2000Mab], which increases with temperature. For example, at
800°C the homogeneity range is about 5 at.% Fe [1995Pal, 1995Yan1], and at 1200°C it is about 7 at.% Fe
[1989Maz]. Notwithstanding this homogeneity range, both TiAl2 and TiAl3 phases have been observed in
3 compositions that are expected to be single phase. For example, [1991Wu] observed both TiAl2 and TiAl
in single crystals of Al66.8Fe5.8Ti27.4. [1992Mor] also observed TiAl2 in Al64Fe8Ti28 and Al63Fe8Ti29
alloys that were heat treated between 600 and 1150°C. [1994Yan] observed precipitation of TiAl2 phase in
a Ti28Fe8Al64 alloy which corresponds to the geometric centre of 3’s composition range. The alloy was
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prepared using 99.999% Al, 99% Fe and 99% Ti, and heat treated at 1200°C for 50 h. Furthermore,
[1994Yan] observed three types of TiAl2: TiAl2I (ZrGa2-type), TiAl2
II (HfGa2-type) and TiAl2III. The latter
is similar to the other two, but with different stacking sequence. It is believed to be stabilized by Fe, and has
never been observed in binary Al-Ti alloys.
Based on a geometric approach [1991Dur] and electron-concentration approach [1992Dur2], Durlu et al
argued that 3 should be considered as TiAl2-based rather than TiAl3-based L12 phase. Furthermore,
[1992Dur2] proposed that Fe should replace Ti in stabilizing L12 structure. On the other hand,
electronic-level ab initio calculations [1990Car, 1991Car] showed that replacement of Al by Fe in TiAl3indeed energetically favors the cubic L12 structure over the tetragonal D022 structure. Indeed, ALCHEMI
results [1992Ma] show that Fe atoms reside primarily on the Al-sublattice in Al62.5±xTi25±yFey alloys.
[1973Mar] also reported another compound Ti6Fe25Al69, but later at the same composition [1981Sei] found
a two-phase mixture of Fe2Al5 and 3. On the other hand, [1995Pal] reported that this composition
represents a ternary extension of the binary phase Fe4Al13. [1981Sei] reported the 1 (TiFe2Al) phase
having cubic structure with lattice parameter a = 414.0 pm; however, subsequent investigation failed to
confirm the existence of this phase [1995Pal]. A cubic phase at TiFe2Al (Heusler-type) also repotred by
[1983Bus], but with lattice parameter very different from [1981Sei].
The details of the crystal structures and lattice parameters of all the binary and ternary solid phases are listed
in Table 1.
Invariant Equilibria
Figure 1 shows the reaction scheme, mostly adopted from the very recent works of [2003Duc] and
[1995Pal]. No distinction is made between disordered ( Fe) and its ordered forms B2 and D03; similarly,
no distinction is made between disordered ( Ti) and ordered ( Ti); 2 is the Ti-rich variant and 2’ is the
Al-rich variant. The systematic study of [2003Duc] by DTA followed by careful characterization of
as-solidified microstructures have led to a number of changes in the reaction scheme compared to that first
proposed by [1981Sei]. The study of [1995Pal] has contributed significantly to our knowledge of solid-solid
phase equilibria. However, the reaction scheme proposed by [2003Duc] suffers from at least four
drawbacks, which have been rectified in this assessment.
First, [2003Duc] did not consider the primary crystallization of Ti2Al5. To account for this, we have
introduced two ternary invariant reactions, P1 (L+TiAl+Ti2Al5 3) and U1 (L+Ti2Al5 TiAl3+ 3),
tentatively occurring around 1380 and 1370°C, respectively. Second, [2003Duc] considered four binary
invariant reactions, labelled c1, pd1, pd2 and pd3, originating from Al-Ti system that are incompatible with
the presently accepted Al-Ti phase diagram. Accordingly, these and the associated ternary invariant
reactions are not considered in Fig. 1. Third, [2003Duc] proposed the invariant reaction U6 around 1150°C:
( Ti)+( Ti) Ti3Al+TiAl. However, this is inconsistent with the observation of the three-phase field
( Ti)+( Ti)+Ti3Al in 1100, 1000, 900 and 800°C isothermal sections [1995Pal, 1999Gor]. To overcome
this problem, we have rewritten the invariant reaction as ( Ti)+TiAl ( Ti) +Ti3Al. In addition, two more
corrections in the reaction scheme of [2003Duc] are made in this assessment. The monovariant and
invariant equilibria E3 and U10 of [2003Duc], respectively, are correctly written as L Fe4Al13+ 3 and
L+ 3 Fe4Al13+ 2’. Fourth, [2003Duc] proposed the invariant reaction U20 around 900°C: TiAl+Fe2Ti
2’+ 2. Once again, the consequences of this reaction contradict the experimental observations. For
example, the 2 phase splits into two islands, 2 and 2’ above 1000°C [1995Pal]. A further serious
drawback is that none of the experimental isothermal sections at 1000, 900 and 800°C shows 2’+ 2+Fe2Ti
and/or 2’+ 2+TiAl phase fields. Therefore, this invariant reaction is not considered in Fig. 1.
[2002Rag] proposed a reaction scheme in which the invariant reaction L+Ti2Al5 TiAl+TiAl3 (U2 in
[2002Rag]) takes place around 1340°C, and this gives rise to the three phase field Ti2Al5+TiAl+TiAl3 that
persists until about 1200°C. However, in the presence of ternary phase 3, in the vicinity of TiAl2 and TiAl3,
the existence of Ti2Al5+TiAl+TiAl3 phase field is very unlikely. Ducher et al [2003Duc] have discussed
other major differences between their reaction scheme and that proposed by [2002Rag].
[1989Maz] observed TiAl2 phase in ternary alloys heat treated at 1200°C. Accordingly, three-phase fields
such as TiAl3+TiAl2+ 3, TiAl2+TiAl+ 3 are expected at this temperature as they have been observed at
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1150°C [2000Mab]. To account for these three-phase fields at 1200°C, the binary invariant reaction
TiAl+Ti2Al5 TiAl2 is considered to take place at 1205°C [1991Mis] instead of 1199°C [2003Sch]. The
proposed reaction scheme in Fig. 1 is consistent with the observed phase fields in 1300 [2000Kai1], 1200
[2000Kai1], 1150 [2000Mab], 1100 [1970Vol], 1000 [1995Pal, 2000Mab], 900 [1999Gor] and 800°C
[1970Vol, 1973Mar, 1995Pal] isothermal sections, and also the vertical sections reported by other
investigators [1969Vol, 1973Vol, 1987Men, 1998Ohn].
Liquidus Surface
[1940Nis] and [1958Bok] reported the liquidus surface of Al-corner only. A comprehensive report of the
liquidus surface was first given by [1981Sei], and subsequently modified by [2003Duc]. Figure 2 shows the
liquidus surface and the melting grooves separating 13 different areas of primary crystallization. To
incorporate the primary crystallization of Ti2Al5, a slight modification has been made. The doubtful regions
of the liquidus surface are shown by dotted lines. Using the melting temperature data of [2003Duc],
approximate isotherms at 100°C intervals from 1600°C to 1000°C are also shown in Fig. 2.
Isothermal Sections
The early works of [1940Nis, 1954Sto] and [1958Bok] were restricted to the Al corner. [1958Bok] reported
two isotherms at 640 and 600°C with up to 2.2 at.% Fe and 1.1 at.% Ti. [1958Kor] reported the isothermal
sections at 1100, 1000, 800 and 550°C with up to 30 mass% (Fe+Al). Recent significant results are the
complete isothermal sections at 1000, 900 and 800°C [1995Pal, 1999Gor], isothermal sections of Al-corner
at 1150 [2000Mab], 1000 [2000Mab] and 800°C [1995Yan1], isothermal sections of Fe-corner at 900 and
800°C [1998Ohn], and isothermal sections of Ti-corner at 1300 and 1200°C [2000Kai1].
Figures 3 and 4 show the isothermal sections of Ti-corner depicting phase equilibria involving ( Ti), ( Ti)
and TiAl. The phase equilibria of the Al-corner at 1200 [1989Maz], and 1150°C [2000Mab] are shown in
Figs. 5 and 6, respectively. The original phase diagram reported by [2000Mab] had to be modified to comply
with the Al-Fe and Al-Ti binary phase diagrams. In particular, the liquid phase should be present in the
Al-rich side at 1150°C, but this was not considered by [2000Mab]. The phase boundaries involving the
liquid phase are shown dotted as their exact locations are not known.
Figure 7 shows a partial isothermal section in the region Ti-TiAl-TiFe at 1100°C, based on the work of
[1970Vol]. Figures 8, 9 and 10 show complete isothermal sections at 1000, 900 and 800°C adopted from
the works of [1995Pal], [1999Gor] and [2000Kai2]. Since ( Ti) in Al-Ti system undergoes a second-order
transition to form B2 structure [2000Ohn], a similar behavior is expected in ternary alloys as well. In fact,
[2000Kai2] established the phase boundaries at 1000°C associated with the second-order transition in
Ti-rich alloys. Accordingly, the ( Ti) field in Fig. 8 is divided into A2 and B2 regions by a second-order
line. Figure 11 shows the isothermal section at 550°C after [1970Vol] in the region of Ti-TiAl-TiFe. Below
550°C, the phase fields remain unchanged down to room temperature as has been confirmed by [1981Sei].
Minor adjustments have been made in the isothermal sections to comply with the binary phase diagrams
accepted here.
Temperature – Composition Sections
[1969Vol] determined three vertical sections at constant Al/Fe mass ratios 3:1, 1:1 and 1:3 and (Al+Fe) was
varied from 0 to 30 mass%. [1973Vol] determined four vertical sections of the Ti-rich alloys at 5, 10, 12
and 16 mass% Al. [1969Vol] reported three vertical sections in the Ti corner at constant Al/Fe ratios of 3:1,
1:1, and 1:3 with a (Al+Fe) content up to 30 mass%, and [1991Nwo] gave the transus and solubility for
sections with 2 and 4 mass% Al up to 16 mass% Fe.
Figures 12 and 13 show the vertical sections at constant Al-content of 25 and 23 at.%, respectively
[1998Ohn]. In addition to ( Fe)+ 2 phase field as in the case of Al-Fe system, the presence of 1+ 2 phase
field in the ternary system may be seen in Figs. 12 and 13. As discussed by [1998Ohn], the topology of the
phase boundaries involving ordered ( 1, 2) and disordered phases ( Fe) are consistent with the general
features of phase diagrams associated with multicritical points [1982All].
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Addition of about 5 at.% Ti is reported to shift the ( Fe)+ 1 phase field to higher temperature and to lower
Al contents compared to Al-Fe alloys [1987Men]. [1998Ohn] also re-investigated the vertical of Fe-5 at.%
Ti-xAl, and found good agreement with the results of [1987Men]. Their results are summarized in Fig. 14.
The effects of substitution of Fe by Ti in Fe3Al ( 1) and the substitution of Al by Ti in FeAl ( 2) on the
order-disorder transitions are summarized in Fig. 15. This conjoined vertical section was originally
published by [1998Ohn], but the Fe3Al-side has been significantly modified to make it consistent with the
Figs. 12 and 14. It is seen that Fe2TiAl (L21) undergoes a second-order phase transition to B2 at about
1220°C. However, the ideal transition temperature is predicted to be about 500°C higher [2002Ish]. The
addition of Co and Ni in Fe2TiAl should increase the critical temperature [2002Ish]. In Figs. 12, 13 and 15,
minor adjustments have been made to comply with the accepted Al-Fe phase diagram.
Thermodynamics
[1979Dew, 1979Kau1] and [1979Kau2] calculated the isothermal section at 1000°C. However, they did not
consider the ternary phases, because the Gibbs energies of formation of these phases are not known. The
calculated ternary ( Fe)/( Fe)+( Fe) and ( Fe)+( Fe)/( Fe) phase boundaries have also been reported
[1986Gho, 1988Kum].
[1987Kal] performed theoretical studies of the effect of Fe on the D019-type ordering of Ti3Al. They found
that Fe increases the ordering temperature.
[1990Car] studied the effect of Fe on the relative stability of cubic L12 and tetragonal D022 structures of
TiAl3 phase using ab initio (augmented-spherical-wave method) electronic band structure calculations.
They found that 4.5 at.% Fe is sufficient to stabilize the L12 structure which is in reasonable agreement with
the experimental homogeneity range of 3.
[1998Ohn] carried out theoretical studies of order-disorder phase transitions and the BCC phase equilibria,
in the composition range Fe-FeAl-FeTi, employing cluster variation method using the irregular tetrahedron
method. They considered first- and second-nearest neighbor as well as tetrahedron interactions. They found
an excellent agreement between the calculated and experimental results.
[2000Kai2] employed Bragg-Williams-Gorsky approximation to model A2/B2 transition in Ti-rich ternary
alloys. Extrapolating the ternary results to Al-Ti system, they predicted that a Ti-23.5 at.% Al alloy
undergoes metastable A2/B2 transition at 1000°C.
Notes on Materials Properties and Applications
[1983Bus] reported the magneto-optical Kerr rotation effect of the Heusler phase TiFe2Al. [1994Sel]
studied the magnetic and electrical properties of Fe0.73Al0.27-xTix (0 x < 0.16) alloys. [1979Sup] studied the
magnetic susceptibility of the 2 phase.
Addition of Ti in Fe73Al27 increases its hardness, and also its deformation mode [1996Pra]. The hardness,
density, temperature dependence of Young’s modulus and yield stress, and creep properties of
Ti33.1Fe33.9Al33 were reported by [1996Mac]. [2000Sha] demonstrated superplastic deformation of Fe-28
at.% Al-2 at.% Ti and Fe-28 at.% Al-4 at.% Ti alloys in the temperature range of 600 to 750°C. The
compressive creep behavior, in the temperature range of 600 to 800°C, of Fe-rich two- and three-phase
alloys is reported to exhibit power-law behavior with the exponent varying from 3 to 6, and the activation
energy varying from 400 to 600 kJ/mol [2001Pra]. The order-disorder transitions in Al-Fe and Al-Fe-Ti
alloys lead to non-monotonic behavior of temperature-dependent mechanical properties, which have been
discussed in detail by [1997Nis2] and [2003Ste].
The mechanical properties of the ternary phase 3 have been studied extensively. [1991Nic] reported the
hardness and Young’s modulus of 3 at Al22Fe3Ti8. [1991Wu] reported the deformation behavior of single
crystal Al66.8Fe5.8Ti27.4 ( 3) as a function orientation and temperature dependence of yield stress of up to
1200°C. The compressive yield stress as a function of temperature has been reported by [1991Ino] for 3 at
Al67.5Ti25Fe7.5 and by [1991Kum] for 3 at Al22Ti8Fe3. The hardness and cracking load of Al64Fe8Ti28 and
Al63Fe8Ti29 alloys were reported by [1992Mor]. The ambient yield and fracture properties of Ti30Fe4Al66
and Ti26Fe8Al66 were reported by [2002Bra].
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A Ti-5 mass% Al-2.5 mass% Fe is reported to be biocompatible, thus, a candidate implant material for hip
prosthesis [1986Zwi]. This alloy, with ( Ti)+( Ti) microstructure, exhibits superplasticity at 850°C.
Furthermore, powder metallurgy processing of this alloy reduces the Young’s modulus from about 111 GPa
to 10 GPa which is very close to that of bone (5 to 9 GPa) [1986Zwi]. The stress-induced –>
transformation and associated superplasticity in the temperature range of 777 to 927°C in a Ti-5.5 mass%
Al-1 mass% Fe alloy has been discussed by [2000Koi].
[1999Lee] studied the hydrogen absorption-desorption behavior of TiFe1-xAlx alloys at 50°C. Addition of
Al causes a increase in lattice parameter of TiFe, and also inhibits the formation of -hydride. The latter
was attibuted to different sizes of octahedral sites, and preferential site occupation of hydrogen atoms.
[2001Ish] also studied hydrogen absorption-desorption of Ti75-xAl25Fex (0 x 25) alloys. At x=15, the
desorption temperature is about 510°C which is about the same as binary Ti3Al; however, the hydrogen
absortion is significantly reduced.
Miscellaneous
The transus temperature increases with increasing Al content [1991Nwo]. [1973Kol] investigated the
solubility of Ti in liquid (Al) in the temperature range of 700° to 850°C for Al - 0.7 mass% Ti and Al - 0.46
mass% Fe - 0.7 mass% Ti alloys. They found that the presence of Fe up to 0.5 mass% does not affect the
solubility of Ti in (Al) in the above temperature range.
[1998Akd] proposed that the value of activity coefficient of Al in -(Fe,Al,Ti) alloys has a strong influence
on the formation and growth kinetics of interfacial diffusion layer.
[1998Leo] synthesized nanocrystalline single-phase alloys of different structures in Al50Fe50-xTix(10 x 40) by mechanical alloying. Along the quasibinary section Ti50Al50-Ti50Fe50, they observed a
number of phase transformations during mechanical alloying in the sequence A3 (hcp) C14 (hcp) D8a
(fcc) B2(bcc) A2(bcc). During continuous heating, they also found that the nanocrystalline state is
preserved until about 500°C.
[2000Izu] studied the sulfidation of TiAl-2 at.% Fe alloy at 900°C using a gas mixture of H2-H2S. The
multilayer sulfide-scale was reported to consist of Ti- and Al-sulfides. They discussed the results in terms
of diffusion paths.
References
[1940Nis] Nishimura, H., Matsumoto, E., “The Equilibrium Diagram of the Al-Fe-Ti System and the
Segregation of Fe and Ti” (in Japanese), Nippon Kinzoku Gakkaishi, 10, 339-343 (1940)
(Equi. Diagram, Experimental, #, *, 5)
[1954Sto] Stone, L., Margolin, H., “The Ti-V-Fe and Ti-Al-Fe Systems”, U.S. Atomic Energy
Commission Publication, AD-43730, 1-72 (1954) (Equi. Diagram, Experimental, #, *)
[1958Bok] Bok, Y.V., Mal`tsev, M.V., “Investigation of the Equilibrium Diagram of the Al-Fe-Ti
System” (in Russian), Izv. Vyss. Uchebn. Zaved. Tsvetn. Metall., 3, 110-114 (1958) (Equi.
Diagram, Experimental, #, *, 2)
[1958Kor] Kornilov, I.I., Pylaeva, E.N., Volkova, M.A., “An Investigation into the Equilibrium of the
Ternary System Ti-Al-Fe” (in Russian), Zh. Neorg. Khim., 3, 1391-1397 (1958) (Equi.
Diagram, Experimental, #, *, 13)
[1963Luz] Luzhinov, L.P., Novikova, V.M., Marsev, A.P., “Solubility of -Stabilizers in -Ti” (in
Russian), Metalloved. Term. Obrab. Met., 2, 13-16 (1963) (Experimental, 4)
[1967Mar] Markiv, V.Ya., Kripyakevich, P.I., “Compounds of the Type R(X',X")2 in the Systems with
R = Ti, Zr, Hf; X' = Fe, Co, Ni, Cu and X" = Al, Ga and Their Crystal Structures”, Sov. Phys.
Crystallogr., 11, 733-738 (1967) (Crys. Structure, Experimental, 25)
[1969Vol] Volkova, M.A., Kornilov, I.I., “Investigation of the Phase Transformation in Ti-rich
Ti-Al-Fe Alloys” (in Russian), Izv. Akad. Nauk SSSR, Met., 4, 236-240 (1969) (Equi.
Diagram, Experimental, #, *, 7)
[1970Vol] Volkova, M.A., Kornilov, I.I., “Phase Equilibria in Ti-rich Ti-Al-Fe Alloys” (in Russian),
Izv. Akad. Nauk SSSR, Met., 3, 187-193 (1970) (Equi. Diagram, Experimental, #, *, 6)
433
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
[1971Vol] Volkova, M.A., Kornilov, I.I., “Phase Equilibriums and Some Mechanical Properties the
Ti-Al-Fe and Ti-Al-V Alloys” (in Russian), Izv. Akad. Nauk SSSR, Met., 1, 200-205 (1971)
(Equi. Diagram, Experimental, #, *, 13)
[1973Kol] Kolpachev, A.A., Medvedeva, N.D., Samoilov, Yu.A., Titova, I.A., “Effect of Iron on
Titanium Solubility in Aluminium and Aluminium-Magnesium Alloys” (in Russian),
Tekhnol. Legk. Splavov, Nauchno-Tekh. Byull., Vses. Inst. Splavov, 8, 15-17 (1973)
(Experimental, 3)
[1973Mar] Markiv, V.Ya., Burnashova, V.V., Rybov, V.P., “The Systems Titanium-Iron-Aluminium,
Titanium-Nickel-Aluminium and Titanium-Copper-Aluminium” (in Russian), Akad. Nauk
Ukr. SSR, Metallofizika., 46, 103-110 (1973) (Equi. Diagram, Experimental, #, *, 24)
[1973Vol] Volkova, M.A., Kornilov, I.I., “Study on the Phase Constitution of Alloys of the Ternary
Titanium-Aluminium-Iron System” (in Russian), Khim. Met. Splav., 1, 77-80 (1973) (Equi.
Diagram, Experimental, #, *, 9)
[1974Dwi] Dwight, A.E., “Alloying Behavior of Zr, Hf and Actinides in Several Series of Isostructural
Compounds”, J. Less-Common Met., 34, 279-284 (1974) (Crys. Structure, Experimental, 6)
[1977Ath] Athanassiadis, F., La Caer, G., Foct, J., Rimlinger, L., “Study of Ternary Ordered Solid
Solutions Derived from Fe3Al by Substitution”, Phys. Status Solidi (a), 40, 425-435 (1977)
(Crys. Structure, Experimental, 20)
[1979Dew] Dew-Hughes, D., Kaufman, L., “Ternary Phase Diagrams of the Manganese-Titanium-Iron
and Aluminium-Titanium-Iron Systems: a Comparison of Computer Calculations with
Experiment”, Calphad, 3, 175-203 (1979) (Thermodyn., Theory, #, *, 23)
[1979Kau1] Kaufman, L., Dew-Hughes, D., “Illustration of Ternary Diagram Synthesis:
Manganese-Titanium-Iron and Aluminium-Titanium-Iron”, in Calculation of Phase
Diagrams and Thermochemistry of Alloy Phases, Y.A. Chang and J.F. Smith, Eds., The
Metallurgical Society of AIME, Warrendale, PA, 46-71 (1979) (Thermodyn., Theory, #,
*, 23)
[1979Kau2] Kaufman, L., Dew-Hughes, D., “Illustration of Ternary Diagram Synthesis:
Manganese-Titanium-Iron and Aluminium-Titanium-Iron”, Energy Res. Rep., 4(19), 1-21
(1979) (Thermodyn., Theory, #, *, 23)
[1979Sup] Suprunenko, P.A., Markiv, V.Ya., Storozhenko, A.L., “Magnetic Susceptibility of
Intermetallides with the Th6Mn23 Structure in the Systems Ti-Fe, Co, Ni-Al, Ga”, Ukr. Fiz.
Zh., 24, 114-116 (1979) (Experimental, 8)
[1980Dew] Dew-Hughes, D., “The Addition of Manganese and Aluminium to the Hydriding
Compound Iron-Titanium (Fe-Ti): Range of Homogeneity and Lattice Parameters”, Metall.
Trans. A, 11A, 1219-1225 (1980) (Experimental, #, *, 14)
[1981Sei] Seibold, A., “Phase Equilibria in the Ternary Systems Ti-Fe-O and Ti-Al-Fe” (in German),
Z. Metallkd., 72, 712-719 (1981) (Equi. Diagram, Experimental, #, *, 25)
[1981Zhu] Zhuang, Y.-H., Liu, J.-Q., Cheng, C.S., “A Room-Temperature Section of the Phase
Diagram of TiAl3-VAl3-MAl3of the Quaternary System Alloys of Al-Ti-V-M (M = Ni, Fe)”
(in Chinese), Acta Phys. Sin., 30, 972-975 (1981) (Equi. Diagram, Experimental, *, 9)
[1982All] Allen, S.M., Cahn, J.W., “Phase Diagram Features Associated with Multicritical Points in
Alloy Systems”, Bull. Alloy Phase Diagrams, 3(3), 287-295 (1982) (Theory, 25)
[1982Kub] Kubaschewski, O., “Iron-Titanium” in Iron-Binary Phase Diagrams, Springer Verlag,
Berlin, 152-156 (1982) (Equi. Diagram, Review, #, *, 26)
[1983Bus] Buschow, K.H.J., van Engen, P.G., Jongebreur, R., “Magneto-Optical Properties of Metallis
Ferromagnetic Materials”, J. Magn. Magn. Mater., 38, 1-22 (1983) (Magn. Prop., Optical
Prop., 23)
[1985Okp] Okpalugo, D.E., Booth, J.G., Faunce, C.A., “Onset of Ferromagnetism in 3d-Substituted
Fe-Al Alloys. I: Ti, V and Cr Substitutions”, J. Phys. F, Met. Phys., 15, 681-692 (1985)
(Crys. Structure, Experimental, 21)
434
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
[1985Pas] Pastushenko, S.N., “Mossbauer Spectroscopic Study of Phase Equilibria in the Ti-Al-Fe
Ternary System” (in Russian), Raschety Eksp. MetodyPostroeniya Diagramm Sostoyaniya.,
Ageev, N.N. Nauka, Moscow, 148-151 (1985) (Experimental, 10)
[1986Gho] Ghosh, G., Raghavan, V., “The Austenite Phase Boundaries in Four Fe-Ti-X System” in
Prog. Metall. Res.: Fundam. Appl. Aspects, Proc. Int. Conf., Mehrotra, S.P.,
Ramachandran, T.R., Eds., Tata McGraw-Hill, New Delhi, 403-408 (1986) (Review,
Thermodyn., 11)
[1986Len] Lendval, A., “Phase Diagram of the Al-Fe System up to 45 mass% Iron”, J. Mater. Sci. Lett.,
5, 1219-1220 (1986) (Equi. Diagram, Experimental, 7)
[1986Zwi] Zwicker, U., “Investigations on the TiAl5Fe2.5 Alloy as Implant Material” (in German),
Z. Metallkd., 77, 714-720 (1986) (Experimental, 26)
[1987For] Fortnum R.T., Mikkola D.E., “Effects of Molybdenum, Titanium and Silicon Additions on
The D03 Reversible B2 Transition-Temperature for Alloys Near Fe3Al”, Mater. Sci. Eng..,
91, 223-231 (1987) (Crys. Structure, Experimental, 37)
[1987Kal] Kaluzhnyi V.V., Matysina Z.A., Milyan M.I., “Ordering of Atoms in Ternary Alloys with
Hexagonal Close-Packed Structure of D019 Type” (in Russian), Izv. V.U.Z. Fiz., 30(3),
70-77 (1987) (Theory, 17)
[1987Men] Mendiratta, M.G., Ehlers, S.K., Lipsitt, H.A., “D03-B2- Phase Relations in Fe-Al-Ti
Alloys”, Metall. Trans. A, 18A, 509-518 (1987) (Equi. Diagram, Experimental, #, *, 12)
[1987Rag] Raghavan, V., “The Al-Fe-Ti (Aluminum-Iron-Titanium) System” in Phase Diagrams of
Ternary Iron Alloys, Part I, ASM International and The Indian Inst. Metals, 9-21 (1987)
(Equi. Diagram, Review, #, *, 23)
[1988Kum] Kumar, K.C.H., Raghavan, V.,"BCC-FCC Equilibrium in Ternary Iron Alloys”, J. Alloy
Phase Equilibria., 4(1), 53-71 (1988) (Equi. Diagram, Thermodyn., 27)
[1989Maz] Mazdiyasni, S., Miracle, D.B., Dimiduk, D.M., Mendiratta, M.G., Subramanian, P.R.,"High
Temperature Phase Equilibria of the L12 Composition in the Al-Ti-Ni, Al-Ti-Fe and
Al-Ti-Cu Systems”, Scr. Metall., 23, 327-331 (1989) (Equi. Diagram, Experimental, #, 10)
[1990Car] Carlsson, A.E., Meschter, P.J., “Relative Stabilities of L12 and D022 Structures in Ternary
MAl3-base Aluminides”, J. Mater. Res., 5, 2813-2818 (1990) (Equi. Diagram, Theory, 15)
[1990Kum] Kumar, K.S., “Ternary Intermetallics in Aluminium-refractory Metal-X Systems (X = V,
Cr, Mn, Fe, Co, Ni, Cu, Zn)”, Int. Mat. Rev., 35, 293-327 (1990) (Review, 158)
[1991Car] Carlsson, A.E., Meschter, P.J., “Ab Initio Calculations of Structural Energetics of
Transitional-Metal Aluminides and Silicides”, Mater. Res. Soc. Symp. Proc.: High-Temp.
Ordered Intermetallic Alloys IV, 213, 19-23 (1991) (Calculation, Thermodyn., 10)
[1991Dur] Durlu, N., Inal, O.T., Yost, F.G., “L12-Type Ternary Titanium Aluminides of the
Composition Ti25X8Al67: TiAl3-Based or TiAl3-Based?”, Scr. Metall. Mater., 25(11),
2475-2479 (1991) (Crys. Structure, Review, 30)
[1991Ino] Inoue, H.R., Cooper, C.V, Favrow, L.H., Hamada, Y., Wayman, C.M., “Mechanical
Properties of Fe-Modified L12-Type Al3Ti”, Mater. Res. Soc. Symp. Proc.: High-Temp.
Ordered Intermetallic Alloys IV, 213, 493-498 (1991) (Experimental, Mechan. Prop., 10)
[1991Kum] Kumar, K.S., Dipietro, M.S., Whittenberger, J.D., “Compession Studies on Particulate
Composites of Ternary Al-Ti-Fe, and Quaternary Al-Ti-Fe-Nb and Al-Ti-Fe-Mn L12
Compounds”, Mater. Res. Soc. Symp. Proc.: High-Temp. Ordered Intermetallic Alloys IV,
213, 1039-1044 (1991) (Experimental, 11)
[1991Mis] Mishurda, J.C., Perepezko, J.H., “Phase Equilibria in Ti-Al Alloys”,
Microstructure-Property Relationships in Titanium Aluminides and Alloys, Kim. Y.W.,
Boyer, R.R., Ed., pp. 3-30 (1991) (Equi. Diagram, #, *, 75)
[1991Nic] Nic, J.P., Zhang, S. , Mikkola, D.E., “Alloying of Al3Ti with Mn and Cr to Form Cubic L12
Phases”, in Mater. Res. Soc. Symp. Proc.: High-Temp. Ordered Intermetallic Alloys IV, 213,
697-702 (1991) (Crys. Structure, Equi. Diagram, Experimental, Mechan. Prop., 12)
435
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
[1991Nwo] Nwobu, A., Maeda, T., Flower, H.M., West, D.R.F., “The Constitution of Ti Rich Alloys of
the Ti-V-Fe-Al System”, in Proceedings of User Aspects of Phase Diagrams, Institute of
Metals, London, pp. 102-111 (1991) (Experimental, Equi. Diagram, #, *, 15)
[1991Wu] Wu, Z.L., Pope, D.P., Vitek, V., “Mechanical Behavior of Single Crystalline
Al66.8Ti27.4Fe5.8”, Mater. Res. Soc. Symp. Proc.: High-Temp. Ordered Intermetallic Alloys
IV, 213, 487-492 (1991) (Crys. Structure, Experimental, Mechan. Prop., 9)
[1992Dur1] Durlu, N. , Inal, O.T, “Phase Relations in TiAl2-Based Ternary Titanium Aluminides of Iron
or Nickel”, Mater. Sci. Eng. A, 152(1/2), 67-75 (1992)
[1992Dur2] Durlu, N. , Inal, O.T., “L12-Type Ternary Titanium Aluminides as Electron Concentration
Phases”, J. Mater. Sci., 27(12), 3225-3230 (1992) (Assessment, Crys. Structure, 41)
[1992Gho] Ghosh, G., “Aluminium-Iron-Titanium”,”, MSIT Ternary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; Document ID: 10.16711.1.20, (1992) (Crys. Structure, Equi. Diagram,
Assessment, 31)
[1992Ma] Ma, Y., Gjonnes, J., “Ternary Atom Location in L12-Structured Intermetallic Phases:
Al62.5+xTi25-y(Fe, Ni or Cu)12.5-z Using ALCHEMI”, J. Mater. Res., 7(8), 2049-2058
(1992) (Calculation, Crys. Structure, Experimental, 30)
[1992Mor] Morris, D.G., Gunter, S., “Ordering Ternary Atom Location and Ageing in Ll2 Trialuminide
Alloys”, Acta Metall. Mat., 40(11), 3065-3073 (1992) (Experimental, 23)
[1992Win] Winnicka, M.B., Varin, R.A., “Microstructure and Ordering of L12 Titanium
Trialuminides”, Metall. Trans. A, 23A(11), 2963-2972 (1992) (Experimental, 24)
[1993Nak] Nakayama, Y., Mabuchi, H., “Formation of Ternary L12 Compounds in Al3Ti-Base
Alloys”, Intermetallics, 1, 41-48 (1993) (Crys. Structure, Equi. Diagram, Experimental,
Mechan. Prop., 40)
[1993Rag] Raghavan, V., “Al-Fe-Ti (Aluminum-Iron-Titanium).”, J. Phase Equilib., 14(5), 618-619
(1993) (Equi. Diagram, Review, 8)
[1994Sel] Sellers, C.H., Hyde, T.A., O’Brien, T.K., Wright, R.N., “Phase Transformations In
Fe3Al+Ti Alloys”, J. Phys. Chem. Solids, 55(6), 505-515 (1994) (Experimental, 30)
[1994Yan] Yang, T.Y., Goo, E.., “Al2Ti Precipitation in Al64Fe8Ti28 Alloy.”, Metall. Trans. A, 25A(4),
715-721 (1994)
[1995Ant] Anthony, L., Fultz, B., “Effects of Early Transition Metal Solutes in the D03-B2 Critical
Temperature of Fe3Al”, Acta Metall. Mater., 43, 3885-3891 (1995) (Crys. Structure,
Experimental, 35)
[1995Mah] Mahmood, S.H., Gharaibeh, M.A., Saleh, A.S., “Moessbauer and Structural Studies of
FeAl1-xTix”, Solid State Commun., 95(4), 263-266 (1995) (Crys. Structure, Experimental,
10)
[1995Pal] Palm, M., Inden, G., Thomas, N., “The Fe-Al-Ti System”, J. Phase Equilib., 16(3), 209-222
(1995) (Crys. Structure, Equi. Diagram, Experimental, #, *, 34)
[1995Yan1] Yang, T.Y, Goo, E., “Phase Stability and Microstructure of Al-Ti-Fe near Al3Ti”, Metall.
Mater. Trans. A, 26A(5), 1029-1033 (1995) (Equi. Diagram, Experimental, 26)
[1995Yan2] Yanson, T.I. , Manyako, N.B., Bodak, O.I., Cerny, R., Gladyshevskii, R.E., “Crystal
Structure of Fe4Ti0.93Al12.07, a Substitutional Variant of the Fe4Al13 Structure Type”,
J. Alloys Compd., 219, 135-138 (1995) (Crys. Structure, Experimental, 8)
[1996Mac] Machon, L., Sauthoff, G., “Deformation Behaviour of Al-Containing C14 Laves Phaes
Alloys”, Intermetallics, 4, 469-481 (1996) (Equi. Diagram, Experimental, 41)
[1996Pra] Prakash, U., Muraleedharan, K., “Effect of Titanium Substitution on the Structure and
Properties of Fe3Al-based Intermetallic Alloys”, J. Mater. Sci., 31, 1569-1573 (1996) (Crys.
Structure, Experimental, 9)
[1997And] Anderson, I.M., “Alchemi Study of Site Distributins of 3d-Transition Metals in B2-Ordered
Iron Aluminides”, Acta Mater., 45(9), 3897-3909 (1997) (Calculation, Crys. Structure,
Experimental, Theory, 26)
436
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
[1997Nis1] Nishino, Y., Kumada, C., Asano, S., “Phase Stability of Fe3Al with Addition of 3d
Transition Elements”, Scripta Mater., 36, 461-466 (1997) (Crys. Structure, Equi. Diagram,
Experimental, 26)
[1997Nis2] Nishino, Y., Asano, S., Ogawa, T., “Phase Stability and Mechanical Properties of Fe3Al
with Addition of Transition Elemnets”, Mater. Sci. Eng. A, A234-236, 271-274 (1997)
(Crys. Structure, Equi. Diagram, Experimental, 18)
[1998Akd] Akdeniz, M.V., Mekhrabon, A.O., “The Effect of Substitutional Impurities on the Evolution
of Fe-Al Diffusion Layer”, Acta Mater., 46(4), 1185-1192 (1998) (Theory, Thermodyn., 55)
[1998Leo] Leonov, A.V., Fadeeva, V.I., Gladilina, O.E (in English)MatyjA, H., “Structure of
Al50Ti50-xFex Alloys Prepared by Mechanical Alloying and Subsequent Annealing”,
J. Alloys Compd., 281, 275-279 (1998) (Crys. Structure, Equi. Diagram, Experimental, 13)
[1998Ohn] Ohnuma, I., Schoen, C.G., Kainuma, R., Inden, G., Ishida, K., “Ordering and Phase
Separation in the b.c.c. Phase of the Fe-Al-Ti System”, Acta Mater., 46(6), 2983-2094
(1998) (Calculation, Crys. Structure, Equi. Diagram, Experimental, Thermodyn., #, *, 22)
[1999Gor] Gorzel, A., Palm, M., Sauthoff, G., “Constitution-based Alloy Selection for the Screening
of Intermetallic Ti-Fe-Al Alloys”, Z. Metallkd., 90(1), 64-70 (1999) (Crys. Structure, Equi.
Diagram, Experimental, #, *, 36)
[1999Hao] Hao, Y.L., Xu, D.S., Cui, Y.Y., Yang, R., Li, D., “The Site Occupancies of Alloying
Elements in TiAl and Ti3Al Alloys”, Acta Mater., 47(4), 1129-1139 (1999) (Crys.
Structure, Experimental, 41)
[1999Lee] Lee, S.M., Perng, T.P., “Correlation of Substitutional Solid Solution with Hydrogenation
Properties of TiFe1-xMx (M = Ni, Co, Al) Alloys”, J. Alloys Compd., 291, 254-261 (1999)
(Crys. Structure, Equi. Diagram, Experimental, 18)
[1999Lev] Levin, L., Tokar, A., Talianker, M., Evangelista, E., “Non-Equilibrium Microstructures in
TiAl-2Fe Alloy”, Intermetallics, 7, 1317-1322 (1999) (Crys. Structure, Experimental, 14)
[1999Li] Li, J., Zong, Y., Hao, S.H., “Effects of Alloy Elements (C, B, Fe, Si) on the Ti-Al Binary
Phase Diagram”, J. Mater. Sci. Technol., 15(1), 58-62 (1999) (Equi. Diagram,
Experimental, *, 13)
[1999Mek] Mekhrabov, A.O., Akdeniz, M.V., “Effect of Ternary Alloying Elements Addition on
Atomic Ordering Characteristics of Fe-Al Intermetallics”, Acta Mater., 47(7), 2067-2075
(1999) (Calculation, Theory, Thermodyn., 63)
[1999Yam] Yamamoto, Y., Hashimoto, K., Kimura, T., Nobuki, M., Kohno, N., “L12 Single Phase
Region in Al-Ti Base Ternary and Quaternary Systems at 1450K” (in Japanese), J. Jpn. Inst.
Met., 63(10), 1317-1326 (1999) (Crys. Structure, Equi. Diagram, Experimental, 15)
[2000Kai1] Kainuma, R., Fujita, Y., Mitsui, H., Ishida, K., “Phase Equilibria Among (hcp), (bcc)
and (L1o) Phases in Ti-Al Base Ternary Alloys”, Intermetallics, 8, 855-867 (2000) (Crys.
Structure, Equi. Diagram, Experimental, #, *, 29)
[2000Kai2] Kainuma, R., Ohnuma, I., Ishukawa, K., Ishida, K., “Stability of B2 Ordered Phase in the
Ti-Rich Portion of Ti-Al-Cr and Ti-Al-Fe Ternary Systems”, Intermetallics, 8, 869-875
(2000) (Crys. Structure, Equi. Diagram, Experimental, #, *, 19)
[2000Koi] Koike, J., Shimoyama, Y., Ohnuma, I., Okamura, T., Kainuma, R., Ishida, K., Maruyama,
K., “Stress-Induced Phase Transformation During Superplastic Deformation in Two-Phase
Ti-Al-Fe”, Acta Mater., 48, 2059-2069 (2000) (Calculation, Crys. Structure, Equi. Diagram,
Experimental, Thermodyn., 26)
[2000Mab] Mabuchi, H., Nagayama, H., Tsuda, H., Matsui, T., Mori, K., “Formation of Ternary L12
Intermetallic Compound and Phase Relation in the Al-Ti-Fe System”, Mater. Trans. , JIM,
41(6), 733-738 (2000) (Crys. Structure, Equi. Diagram, Experimental, #, *, 50)
[2000Ohn] Ohnuma, I., Fujita, Y., Mitsui, H., Ishikawa, K., Kainuma, R., Ishida, K., “Phase Equilibria
in the Ti-Al Binary System”, Acta Mater., 48, 3113-3123 (2000) (Calculation, Equi.
Diagram, Experimental, Thermodyn., #, *, 37)
[2000Sha] Shan, A., Lin, D., “Low Temperature Superplasticity in Fe3Al Alloy”, Key Engineering
Materials, 171-174, 349-354 (2000) (Experimental, Mechan. Prop., 11)
437
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
[2000Yan] Yang, R., Hao, Y., Song, Y., Guo, Z.X., “Site Occupancy of Alloying Additions in Titanium
Aluminides and its Application to Phase Equilibrium Evaluation”, Z. Metallkd., 91(4),
296-301 (2000) (Crys. Structure, Equi. Diagram, Review, 38)
[2001Ish] Ishikawa, K., Hashi, K., Suzuki, K., Aoki, K., “Effect of Substitutional Elements on the
Hydrogen Absorption-Desorption Properties of Ti3Al Compounds”, J. Alloys Compd., 314,
257-261 (2001) (Equi. Diagram, Experimental, 9)
[2000Izu] Izumi, T., Yoshioka, T., Hayashi, S., Narita, T., “Sulfidation Properties of TiAl-2 at.% X
(X=V, Fe, Co, Cu, Nb, Mo, Ag and W) Alloys at 1173 K and 1.3 Pa Sulfur Pressure in an
H2S-H2 Gas Mixture”, Intermetallics, 8, 891-901 (2000) (Crys. Structure, Experimental,
42)
[2001Pra] Prakash, U., Sauthoff, G., “Structure and Properties of Fe-Al-Ti Intermetallics Alloys”,
Intermetallics, 9, 107-112 (2001) (Crys. Structure, Equi. Diagram, Experimental, Mechan.
Prop., 7)
[2001Sun] Sun, F.-S., Cao, C.-X., Kim, S.-E., Lee, Y.-T., Yan, M.-G., “Alloying Mechanism of Beta
Stabilizers in a TiAl Alloy”, Metall. Mater. Trans. A, 32A, 1573-1589 (2001) (Crys.
Structure, Equi. Diagram, Experimental, Mechan. Prop., 37)
[2001Tok] Tokar, A., Berner, A., Levin, L, “The Origin of a New Phase Observed During Quenching
of a TiAl-2Fe Alloy”, Mater. Sci. Eng. A, 308, 13-18 (2001) (Crys. Structure, Equi.
Diagram, Experimental, 22)
[2002Aze] Azez, K.A., AlL-Omari, I.A., Shobaki, J., Hasan, M.K., Al-Zoubi, G.M., Hamdeh, H.H.,
“Moessbauer Spectroscopic and Crystal Structure Investigation of the Fe0.7-xTixAl0.3 Alloy
System”, Physica B, 321(1-4), 178-182 (2002) (Crys. Structure, Experimental, Moessbauer,
16)
[2002Bra] Brandt, C., Inal, O.T., “Mechanical Properties of Cr, Mn, Fe, Co, and Ni Modified Titanium
Trialuminides”, J. Mater. Sci., 37(20), 4399-4403 (2002) (Crys. Structure, Experimental,
Mechan. Prop., 17)
[2002Ish] Ishikawa, K., Kainuma, R., Ohnuma, I., Aoki, K., Ishida, K., “Phase Stability of the X2AlTi
(X:Fe, Co, Ni and Cu) Heusler and B2-Type Intermetallic Compounds”, Acta Mater., 50,
2233-2243 (2002) (Calculation, Equi. Diagram, Experimental, Thermodyn., 12)
[2002Rag] Raghavan, V., “Al-Fe-Ti (Alimunum-Iron-Titanium)”, J. Phase Equilib., 23(4), 367-374
(2002) (Equi. Diagram, Review, *, 20).
[2003Duc] Ducher, R., Stein, F., Viguier, B., Palm, M., Lacaze, J., “A Re-examination of the Liquidus
Surface of the Al-Fe-Ti System”, Z. Metallkd., 94(4), 396-410 (2003) (Equi. Diagram,
Experimental, #, *, 34)
[2003Gry] Grytsiv, A., Ding, J.J., Rogl, P., Weill, F., Chevalier, B., Etourneau, J. , Andre, G., Bouree,
F., Noel, H., Hundegger, P., Wiesinger, G., “Crystal Chemistry of the G-phases in the
Systems Ti-{Fe,Co,Ni}-Al with a novel filled variant of the Th6Mn23-type”, Intermetallics,
11, 351-359 (2003) (Experimental, Crys. Structure, 26)
[2003Pis] Pisch, A., “Al-Fe (Aluminum-Iron)”, MSIT Binary Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart; to be published, (2003) (Equi. Diagram, Crys. Structure, Assessment, 58)
[2003Sch] Schmid-Fetzer, R., “Al-Ti (Aluminium-Titanium)”, MSIT Evaluation Program, in MSIT
Workplace, Effenberg, G. (Ed.), MSI, Materials Science International Services GmbH,
Stuttgart, to be published, (2002) (Equi. Diagram, Assessment, 86)
[2003Ste] Stein, F., Schneider, A., Frommeyer, G., “Flow Stress Anomaly and Order-Disorder
Transition in Fe3Al-Based Fe-Al-Ti-X Allos with X = V, Cr, Nb, or Mo”, Intermetallics,
11(1), 71-82 (2003) (Crys. Structure, Experimental, Mechan. Prop., 53)
438
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
Table 1: Crystallographic Data of Solid Phases
Phase/
Temperature Range
[°C]
Pearson Symbol/
Group Space/
Prototype
Lattice Parameters
[pm]
Comments
(Al)
< 660.452
cF4
Fm3m
Cu
a = 404.96 at 25°C [Mas2]
( Fe)(h2)
1538-1394
cI2
Im3m
W
a = 293.15 [Mas2]
( Fe)(h1)
1994-912
cF4
Fm3m
Cu
a = 364.67 [Mas2]
( Fe)(r)
< 912 °C
cI2
Im3m
W
a = 286.65 pure Fe at 20°C [V-C]
( Ti)(h)
1670-882
cI2
Im3m
W
a = 330.65 [Mas2]
( Ti)(r)
< 882
hP2
P63/mmc
Mg
a = 295.06
c = 468.25
pure Ti at 25°C [Mas2]
TiAl3 1393
tI8
I4/mmm
TiAl3
a = 384.9
c = 860.9
a = 384.8
c = 859.6
a = 384.7
c = 860.2
[2003Sch]
[2000Mab], at Al-25 at.% Ti
[1995Pal], contains 1.2 at.% Fe
Ti2Al51416-990
tP28
P4/mmm
Ti2Al5
a = 390.53
c = 2919.63
a = 387.5
c = 3348.4
a = 392.0
c = 2919.4
[2003Sch]
[1995Pal]
[2000Mab], Al-28.5 at.% Ti.
Heat treated at 1150°C for 24 h followed
by water quench
TiAl2 1205
tI24
I41/amd
HfGa2
a = 397.0
c = 2497.0
a = 397.1
c = 2432.0
[2003Sch]
[2000Mab], at Al-35 at.% Ti.
Heat treated at 1000°C for 48 h followed
by water quench. Single phase alloy.
439
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
TiAl
1463
tP4
P4/mmm
AuCu
a = 400.0
c = 407.5
a = 398.4
c = 406.0
a = 399.5
c = 408.0
a = 399.6
c = 407.7
a = 400.7
c = 404.9
a = 400.5
c = 404.7
[2003Sch], at 50 at.% Ti.
Solid solubility ranges
from 33.5 to 53.3 at.% Ti [2003Sch].
[2003Sch], at 38 at.% Ti.
[2000Mab], at Al-47 at.% Ti.
Heat treated at 1000°C for 48 h followed
by water quench.
[1999Gor], at Al47.9Fe1.71Ti50.4
[1999Gor], at Al46Fe2.2Ti51.8
[1999Gor], at Al45.6Fe1.31Ti53.1
Ti3Al
1164
hP8
P63/mmc
Ni3Sn
a = 580.6
c = 465.5
a = 574.6
c = 462.4
a = 576.1
c = 462.4
[2003Sch], at 78 at.% Ti.
Solid solubility ranges
from 61.8 to 80 at.% Ti [2003Sch].
[2003Sch], at 62 at.% Ti.
[1999Gor], at Al36.3Fe0.93Ti62.8
1, Fe3Al
552.5
cF16
Fm3m
BiF3
a = 578.86 to 579.3 [2003Pis], solid solubility ranges
from 22.5 to 36.5 at.% Al.
Labelled as D03 (L21) in isothermal
sections.
2, FeAl
1310
cP2
Pm3m
CsCl
a = 289.76 to 290.78
a = 318.5
a = 318.5
[2003Pis], at room temperature
solid solubility ranges from 22.0 to
54.5 at.% Al.
Labelled as B2 in isothermal sections.
[1999Gor], at Al33.5Fe5.6Ti60.9
[1999Gor], at Al33.1Fe9.5Ti57.4
, Fe2Al31102-1232
cI16? a = 598.0 [2003Pis], solid solubility
ranges from 54.5 to 62.5 at.% Al
FeAl2 1156
aP18
P1
FeAl2
a = 487.8
b = 646.1
c = 880.0
= 91.75°
= 73.27°
= 96.89°
a = 487.2
b = 645.9
c = 879.4
= 91.76°
= 73.35°
= 96.89°
[2003Pis], at 66.9 at.% Al
solid solubility ranges
from 65.5 to 67.0 at.% Al
[1995Pal], contains ablout 1.8 at.% Ti
Phase/
Temperature Range
[°C]
Pearson Symbol/
Group Space/
Prototype
Lattice Parameters
[pm]
Comments
440
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
, Fe2Al5 1169
oC24
Cmcm
Fe2Al5
a = 765.59
b = 641.54
c = 421.84
a = 766.5
b = 640.9
c = 422.1
a = 765.6
b = 646.3
c = 422.9
[2003Pis], at 71.5 at.% Al
solid solubility ranges
from 71.0 to 72.5 at.% Al.
[1995Pal], contains 1.5 at.% Ti
[1995Pal], contains 2.5 at.% Ti
Fe4Al13
1160
mC102
C2/m
Fe4Al13
a = 1552.7 to 1548.7
b = 803.5 to 808.4
c = 1244.9 to 1248.8
= 107.7 to 107.99°
a = 1549.2
b = 807.8
c = 1247.1
= 107.69°
a = 1548.9
b = 808.3
c = 1247.6
= 107.72°
a = 1565.3
b = 805.2
c = 1243.0
= 107.58°
[2003Pis], 74.16 to 76.7 at. % Al
solid solubility ranges
from 74.5 to 75.5 at.% Al
[2003Pis], at 76.0 at.% Al
[1995Pal], contains about 6.5 at.% Ti
with Al being replaced
[1995Yan2], at Fe4Al12.07Ti0.93
TiFe2
1427
hP12
P63/mmc
MgZn2
a = 478.7
c = 781.5
a = 495.6
c = 803.2
solid solubility ranges
from 24.0 to 36.0 at.% Ti [V-C]
[1996Mac], at Ti33.1Fe33.9Al33
TiFe
1317
cP2
Pm3m
CsCl
a = 297.6 solid solubility ranges
from 49.8 to 51.8 at.% Ti [V-C]
* 1, TiFe2Al cF16
Fm3m
AlCu2Mn
a = 414.0
a = 587.9
[1981Sei]
[1983Bus]
* 2’, Ti52Fe10Al38 t? a = 1150.0
c = 1380.0
[2001Tok], in a Ti-1.9 at.% Fe-49.6 at.%
Al alloy heat treated at 1200°C for 8 h
followed by water quench.
Phase/
Temperature Range
[°C]
Pearson Symbol/
Group Space/
Prototype
Lattice Parameters
[pm]
Comments
441
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
* 2, TiFeAl2 cF116
Fm3m
Th6Mn23
filled Th6Mn23
filled Th6Mn23
tetragonal
a = 1199.0
a = 1182.0
a = 1211.0
a = 1203.8
a = 1207.6
a = 1209.9
a = 1189.0
a = 1209.2
a = 1211.0
a = 1197.3
c = 1276.83
a = 1195.9
c = 1274.59
a = 1197.0
c = 1276.0
[1967Mar, 2000Mab]
[1981Sei]
[1995Pal], at Al24.6Fe24.5Ti50.9
[1995Pal], at Al47.8Fe21.4Ti30.8
[1999Gor], at Al38.6Fe23Ti38.4
[1999Gor], at Al34.7Fe23.1Ti42.2
[2003Gry] at Al56Fe23.7Ti20.3
[2003Gry] at Al34.7Fe23.3Ti42
[1999Lev]
[1995Pal], at Al49Fe27Ti24
[1995Pal], at Al53.6Fe25.1Ti21.3
[1999Lev]
* 3,
Ti8Fe3Al22
cP4
Pm3m
AuCu3
a = 394.3
a = 394.3
a = 394.44
a = 393.5
[1991Nic], at Al22Fe3Ti8[1995Pal], at Al63.9Fe7.5Ti28.6
[1995Pal], at Al66.6Fe7.6Ti25.8
[2000Mab], at Al64Fe8Ti28
Phase/
Temperature Range
[°C]
Pearson Symbol/
Group Space/
Prototype
Lattice Parameters
[pm]
Comments
442
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
Fig
. 1a:
R
eact
ion s
chem
e of
the
Al-
Fe-
Ti
syst
em
Al-
Fe
Fe-
Ti
A-B
-C
L (
αFe)
+T
iFe 2
13
05
e 1l
+ T
iFe 2
TiF
e
13
17
p5
L T
iFe 2
+ τ3
12
75
e 3
Al-
Fe-
Ti
L+
TiA
l+T
i 2A
l 5τ 3
ca.1
380
P1
Al-
Ti
l +
(βT
i) (
αTi)
14
90
p1
l+(α
Ti)
TiA
l
14
63
p2
l +
TiA
l T
i 2A
l 5
14
16
p3
l +
Ti 2
Al 5
TiA
l 3
13
93
p4
l (
αFe)
+ T
iFe 2
12
93
e 2
L+
Ti 2
Al 5
TiA
l 3+
τ 3ca
.13
70
U1
L+
(αT
i) (
βTi)
+T
iAl
>1300
U2
L +
τ3
TiA
l +
TiF
e 21
270
U3
L +
TiA
l (
βTi)
+T
iFe 2
12
35
U4
L+
(αF
e)+
TiF
e 2
(αT
i)+
(βT
i)+
TiA
l
L+
TiA
l 3+
τ 3
L+
(αF
e)+
TiF
e 2
p5
L+
TiF
e 2+
τ 3
L+
TiF
e 2+
τ 3L
+(β
Ti)
+T
iFe 2
(βT
i)+
TiF
e 2+
TiA
l
L+
(βT
i)+
TiA
l
L+
TiA
l+τ 3
TiA
l 3+
Ti 2
Al 5
+τ 3
TiA
l+T
i 2A
l 5+
τ 3
P1
L+
Ti 2
Al 5
+τ 3
TiA
l+T
iFe 2
+τ 3
L+
TiA
l+T
iFe2
U1
e 1
U2
U3
U1
443
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
Fig
. 1b
:
Rea
ctio
n s
chem
e of
the
Al-
Fe-
Ti
syst
em
Al-
Fe
Fe-
Ti
A-B
-C
l +
(αF
e)ε
12
32
p6
(αT
i) T
i 3A
l +
TiA
l
11
18
e 6
ε (
αFe)
+ F
eAl 2
11
02
e 7
Al-
Fe-
Ti
L+
TiF
e 2+
τ 3τ 2
'1
225
P2
Al-
Ti
TiA
l+T
i 2A
l 5T
iAl 2
12
05
p7
Lε
+ F
e 2A
l 5
11
65
e 4
L F
e 2A
l 5+
Fe 4
Al 13
ca.1
160
e 5
ε +
Fe 2
Al 5
FeA
l 2
11
56
p8
L +
TiF
e 2 (
βTi)
+ T
iFe
ca.1
220
U5
TiA
l +
Ti 2
Al 5
τ 3 +
TiA
l 2ca
.12
00
U6
L +
TiF
e 2 (
αFe)
+ τ2'
11
40
U7
L +
(αF
e)τ 2
' + ε
ca.1
120
U8
(αT
i)+
TiA
l(β
Ti)
+ T
i 3A
lca
.11
10
U9
TiF
e 2+
(βT
i)T
iFe+
TiA
lca
.11
00
U10
p5
TiA
l+T
i 2A
l 5+
τ 3
U1
L+
TiF
e 2+
τ 3U3
(βT
i)+
TiF
e 2+
TiA
l
TiF
e 2+
τ 2'+
τ 3L
+τ 2
'+τ 3
L+
TiF
e 2+
τ 2'
e 1
(βT
i)+
TiF
e+T
iFe 2
Ti 2
Al 5
+T
iAl 2
+τ 3
L+
(βT
i)+
TiF
e
TiA
l+T
iAl 2
+τ 3
L+
(αF
e)+
τ 2'
U9
TiF
e 2+
TiF
e+T
iAl
(αT
i)+
(βT
i)+
Ti 3
Al
L+
ε+τ 2
'
U2
(αF
e)+
TiF
e 2+
τ 2'
(αF
e)+
ε+τ 2
'
U1
U8U9
(βT
i)+
TiF
e+T
iAl
U10
U6
P2
U1
U8
U6
U3
U1
U5 P2
e 3U4
L+
(βT
i)+
TiF
e 2
U4
(βT
i)+
TiA
l+T
i 3A
l
444
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
Fig
. 1c:
Rea
ctio
n s
chem
e of
the
Al-
Fe-
Ti
syst
em
Al-
Fe
Fe-
Ti
A-B
-C
l (
βTi)
+ T
iFe
10
85
e 9
Lτ 3
+ F
e 4A
l 13
ca.1
100
e 8
Al-
Fe-
Ti
L+
τ 3τ 2
'+ F
e 4A
l 13
10
95
U11
Al-
Ti
L+
τ 3 T
iAl 3
+F
e 4A
l 13
10
92
U12
L+
ε τ 2
'+F
e 2A
l 51
088
U13
L F
e 4A
l 13+
τ 2'+
Fe 2
Al 5
10
85
E1
TiA
l+T
iFe+
TiF
e 2τ 2
10
75
P3
TiA
l+τ 3
TiF
e 2+
TiA
l 2ca
.10
70
U14
ε+F
e 2A
l 5τ 2
'+F
eAl 2
ca.1
070
U15
(βT
i)+
TiA
lT
iFe+
Ti 3
Al
ca.1
050
U16
ε (
αFe)
+F
eAl 2
+τ 2
'1
041
E2
L+
τ 2'+
Fe 4
Al 13
L+
TiA
l 3+
τ 3
ε+τ 2'+
Fe 2
Al 5
e 4 p8
L+
Fe 2
Al 5
+τ 2'
Fe 4
Al 13+
τ 2'+
Fe 2
Al 5
TiA
l+T
iFe+
τ 2T
iAl+
TiF
e 2+
τ 2T
iFe+
TiF
e 2+
τ 2
e 5
TiA
l+T
iFe 2
+T
iAl 2
TiF
e 2+
TiA
i 2+
τ 3
FeA
l 2+
ε+τ 2
'
(βT
i)+
TiF
e+T
iAl
U9
(βT
i)+
TiF
e+T
i 3A
lT
iAl+
TiF
e+T
i 3A
le 7
U8
P2
U5
L+
TiA
l 3+
Fe 4
Al 13
Fe 4
Al 13+
τ 2'+
τ 3
TiA
l 3+
Fe 4
Al 14+
τ 3
Fe 2
Al 5
+F
eAl 2
+τ 2
'
(αF
e)+
FeA
l 2+
τ 2'
L+
τ 2'+
τ 3
TiA
l+T
iAl 2
+τ 3
U6
U3
U1
U10
U9
U8
U6
U1
P2
U12
U9
P3'
U16
U14
P3
U10 T
iFe 2
+T
iFe+
TiA
l
445
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
Fig
. 1d
:
Rea
ctio
n s
chem
e of
the
Al-
Fe-
Ti
syst
em
Al-
Fe
Fe-
Ti
A-B
-C
l(A
l)+
Fe 4
Al 13
65
5e 11
(βT
i) (
αTi)
+ T
iFe
58
3e 12
l +
TiA
l 3 (
Al)
66
4p9
Al-
Fe-
Ti
τ 3+
Ti 2
Al 5
TiA
l 2+
TiA
l 3ca
.99
5U17
Al-
Ti
Ti 2
Al 5
TiA
l 3+
TiA
l 2
99
0e 10
τ 3+
TiF
e 2τ 2
'+T
iAl 2
ca.9
70
U18
TiA
l 2+
TiF
e 2τ 2
'+T
iAl
ca.9
40
U20
TiA
l+T
iFe
τ 2+
Ti 3
Al
ca.9
50
U19
L+
TiA
l 3 (
Al)
+F
e 4A
l 13
65
8U21
(βT
i)(α
Ti)
+T
iFe+
Ti 3
Al
ca.5
80
E3
TiA
l 3+
Ti 2
Al 5
+τ 3
Ti 2
Al 5
+T
iAl 2
+τ 3
TiA
l 2+
TiA
l 3+
τ 3
TiF
e 2+
τ 2'+
τ 3
TiF
e 2+
TiA
l 2+
τ 3
TiA
l 2+
τ 2'+
τ 3 TiF
e+T
iAl 2
+τ 2
'
Ti 3
Al+
TiF
e+τ 2
TiA
l+T
i 3A
l+τ 2
TiA
l+F
eTi+
Ti 3
Al
TiA
l+T
iFe+
τ 2
TiA
l+T
iFe 2
+T
iAl 2
TiA
l+T
iAl 2
+τ 2
'
C1(<
94
0)
TiA
l+T
iFe 2
+τ 2
'
L+
TiA
l 3+
Fe 4
Al 13
(Al)
+F
eAl+
TiA
l 3
(βT
i)+
TiF
e+T
i 3A
l
(αT
i)+
TiF
e+T
i 3A
l
U16
U12P3
U14
U16 U14
U1
U6
P3'U9
(αT
i)+
(βT
i)+
Ti 3
Al
446
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
20
40
60
80
20 40 60 80
20
40
60
80
Ti Fe
Al Data / Grid: at.%
Axes: at.%
TiFe2
(αFe)
1600
1500
1400
1300 12
0012
00
FeTi
(βTi)
U7
(αTi)
Ti2Al5
Fe4Al13
Fe2Al5
U8
U13
τ
E1
U11
U12
1200
11001000
U2
e5
e4
p6
e11
p1
p2
TiAl3
U5
U4
U3
τ3
1300
1400
1400
1400
1500
1300
1300
p9
ε
U21
e8
e3
p3
p4
(Al)
TiAl
P1
U1
P2
e1
e2p5e9
Fig. 2: Al-Fe-Ti.
The liquidus surface
50
60
70
10 20
30
40
50
Ti 75.00Fe 0.00Al 25.00
Ti 45.00Fe 30.00Al 25.00
Ti 45.00Fe 0.00Al 55.00 Data / Grid: at.%
Axes: at.%
(αTi)
(αTi)+TiAl
(βTi)
(αTi)+(βTi)+TiAl
(αTi)+(βTi)
TiAl
Fig. 3: Al-Fe-Ti.
Partial isothermal
section at 1300°C
447
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
50
60
70
10 20
30
40
50
Ti 75.00Fe 0.00Al 25.00
Ti 45.00Fe 30.00Al 25.00
Ti 45.00Fe 0.00Al 55.00 Data / Grid: at.%
Axes: at.%
TiAl
(βT
i)+T
iAl
(αTi)+(βTi)+TiAl
(αTi)+(βTi)
(αTi)+TiAl
(αTi)
(βTi)
10
20
30
40
10 20 30 40
60
70
80
90
Ti 50.00Fe 0.00Al 50.00
Ti 0.00Fe 50.00Al 50.00
Al Data / Grid: at.%
Axes: at.%
τ3
L+τ3
TiAl
TiAl2
TiAl3
L+τ3+TiAl3
L+TiAl3
TiAl+τ3+TiFe
L
TiAl+TiAl2+τ3
TiAl2+Ti2Al5+τ3
Ti2Al5+TiAl3+τ3
Ti2Al5
Fig. 4: Al-Fe-Ti.
Partial isothermal
section at 1200°C
Fig. 5: Al-Fe-Ti.
Partial isothermal
section at 1200°C
448
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
60
70
80
90
10 20 30 40
10
20
30
40
Ti Ti 50.00Fe 50.00Al 0.00
Ti 50.00Fe 0.00Al 50.00 Data / Grid: at.%
Axes: at.%
L+TiFe
L+(βTi)+TiFe
L+(βTi)
L
(βTi)
(αTi)
(βTi)+Ti3Al
TiFe+(βTi)
(βTi)+TiFe+TiAl
TiAl
Ti3Al
TiFe
10
20
30
40
50
10 20 30 40 50
50
60
70
80
90
Ti 60.00Fe 0.00Al 40.00
Ti 0.00Fe 60.00Al 40.00
Al Data / Grid: at.%
Axes: at.%
τ2´TiFe2
L+τ2+τ3τ3
TiAl
L+τ 3
+TiA
l 3
TiAl3
L+TiAl3
Ti2Al5
L
TiAl2
L+τ3
Fig. 7: Al-Fe-Ti.
Partial isothermal
section at 1100°C
Fig. 6: Al-Fe-Ti.
Partial isothermal
section at 1150°C
449
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
20
40
60
80
20 40 60 80
20
40
60
80
Ti Fe
Al Data / Grid: at.%
Axes: at.%
L
Fe4Al13
Fe2Al5
FeAl2
B2
A2(αFe)
TiAl3
Ti2Al5
TiAl2
TiAl
Ti3Al
(αTi)
A2
B2
(βTi)
τ3
τ2´
τ2
TiFe
TiFe2B2+Ti3Al
A2+Ti3Al
A2+TiFe
B2+TiFeD03+B2
τ2´+B2τ2 ´+D03(L21)
B2+TiFe2
A2+TiFe2 (γFe)
D03(L21)
20
40
60
80
20 40 60 80
20
40
60
80
Ti Fe
Al Data / Grid: at.%
Axes: at.%
(αFe)A2
Fe4Al13
L
Fe2Al5
FeAl2
B2
TiFe TiFe2
(βTi)
(αTi)
Ti3Al
TiAl
TiAl2
TiAl3
τ3
τ2´
τ2
B2+τ2 ´D0
3 (L21 )
D03(L21)
B2+TiFe2
B2+D03(L21)
Fig. 8: Al-Fe-Ti.
Isothermal section at
1000°C
Fig. 9: Al-Fe-Ti.
Isothermal section at
900°C
450
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
20
40
60
80
20 40 60 80
20
40
60
80
Ti Fe
Al Data / Grid: at.%
Axes: at.%L
Fe4Al13
Fe2Al5
FeAl2
B2+τ2 ´
B2
(αFe)
TiFe2
TiFe(βTi)
(αTi)
Ti3Al
TiAl
TiAl2
TiAl3τ3
B2+D03(L21)D03(L21)
D03 (L2
1 )+τ2 'τ2
τ2´
60
70
80
90
10 20 30 40
10
20
30
40
Ti Ti 50.00Fe 50.00Al 0.00
Ti 50.00Fe 0.00Al 50.00 Data / Grid: at.%
Axes: at.%
(αTi)+TiFe
Ti3Al+(αTi)+TiFe
TiFe+Ti3Al
TiFe+TiAl+Ti3Al
TiAl+Ti3Al
Ti3Al
(αTi)+Ti3Al
(αTi) TiFe
TiAl
Fig. 10: Al-Fe-Ti.
Isothermal section at
800°C
Fig. 11: Al-Fe-Ti.
Partial isothermal
section at 550°C
451
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
10 20
500
750
1000
1250
Ti 0.00Fe 75.00Al 25.00
Ti 25.00Fe 50.00Al 25.00Ti, at.%
Tem
pera
ture
, °C
L
α2
(αFe)
α1
α1+α2
(αFe)+α1+α2
(αFe)+α1
(αFe)+α2
10 20
500
750
1000
1250
Ti 0.00Fe 77.00Al 23.00
Ti 25.00Fe 52.00Al 23.00Ti, at.%
Tem
pera
ture
, °C
α1+α2
(αFe)
α2
(αFe)+α2(αFe)+α1+α2
α1
(αFe)+α1
L
Fig. 12: Al-Fe-Ti.
Vertical section at a
constant Al-content of
25 at.%
Fig. 13: Al-Fe-Ti.
Vertical section at a
constant Al-content of
23 at.%
452
Landolt-BörnsteinNew Series IV/11A2
MSIT®
Al–Fe–Ti
20 30
500
750
1000
Ti 5.00Fe 79.00Al 16.00
Ti 5.00Fe 61.00Al 34.00Al, at.%
Tem
pera
ture
, °C
α2
(αFe)
(αFe)+α1
α1+α2
α1
1400
1200
1000
800
600
400
5 10 15 20 5101520
Fe Al3 Fe AlTi
2FeAl
L21
L L( Fe)�
�2
�1�1
��1+��
�� � �Fe)+ �1+
��Fe)+�1
�2
��Fe)+��
Temperature,°C
at.% Ti at.% Ti
Fig. 14: Al-Fe-Ti.
Vertical section at a
constant Ti-content of
5 at.%
Fig. 15: Al-Fe-Ti.
Conjoined vertical
sections along
Fe3Al-Fe2TiAl and
Fe2TiAl-FeAl