Applications of Phase Equilibria in Aluminium Alloy Products and ...
Transcript of Applications of Phase Equilibria in Aluminium Alloy Products and ...
tsc
Applications of Phase Equilibriain Aluminium Alloy
Products and Processes
P.V. Evans and R.A. RicksTechnology Strategy Consultants
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tsc Introduction
Aluminium alloys are generally not used in a state of thermodynamic equilibrium� many contain metastable precipitates or intermetallic phases
� with process routes designed to avoid attainment of equilibrium
Even alloys relying on solid solution strengthening are usually in a metastable state at their operating temperatures
However equilibrium can be of relevance during earlier stages of production, and at high temperature stages
G.A. Edwards et al. Acta Mat. 46, p3893 (1998)
Bright field TEM image of metastable β’’ precipitates in AA6061 (Al-Mg-Si alloy)
High resolution image down β’’ needle
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tsc Equilibrium during processing aluminium
In some cases the thermodynamic understanding is embedded in the practices…
…in other cases it comes back to haunt us!
We will consider a few of examples drawn from the aluminium process stream1. virtually all aluminium undergoes some form of treatment whilst molten
– measurement and removal of dissolved hydrogen can be problematic
2. extrusion: a process stream designed around attainment of equilibrium in situ
3. rolled product development: a case of being wise after the event
melttreatment
casting
rolling(plate, sheet)
extrusion
othersemi-fab
fabrication
smeltermetal
secondarymetal
(recycled)
re-melting
shapecasting
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tsc 1) Hydrogen in aluminium
Aluminium melt treatment generally focuses on improving 3 quality attributes� dissolved hydrogen, inclusions, alkali metals
Hydrogen is the major contaminant controlled by equilibrium considerations
Hydrogen is far more soluble in liquid aluminium cf. solid aluminium� solidification of a melt containing too much hydrogen results in porosity
example of internal porosity visible on machined engine face
surface blistering after homogenisation
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tsc Effects of porosity
Fatigue life is also reduced as porosity increases
dendrite 47 µm
dendrite 22 µm
fatigue life variation with pore size
Y.X. Gao et al., Fatigue Fract. Eng. 27, p559 (2004)
fatigue failure surfaceand pore initiation
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tsc
50µm
Porosity in wrought alloys
Porosity also causes problems during subsequent fabrication in wrought alloys, e.g. hot mill edge cracking
hot mill edge cracking
original ingot porosity (AA5182)
20 mm
reroll (gauge ~10mm)
slab
25mm
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tsc Hydrogen solubility
The solubility of hydrogen in pure liquid aluminium is now well established� dating back to pioneering work of Ransley, Talbot and others
� note hydrogen concentration usually expressed as ml. H2 per 100g aluminium
Data shown for solubility in contact with an atmosphere of pure hydrogen
liquid
solid
D.E.J. Talbot“The Effects of Hydrogenin aluminium and its alloys”Maney (2004).
T(°C)
-3.0
-2.5
-2.0
-1.5
-1.0
-0.5
0.0
0.5
1.0
7 9 11 13 15
104/T (K-1)
log
10(S
) (m
l/100
g)
5006608001000 400
0.1
10
1.0
hydrogen(ml/100g)T
SL
270072.2log10 −=
0.01
TSS
332022.2log10 −=
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tsc Expected relationship
Equilibrium constant for the reaction between gaseous hydrogen and hydrogen dissolved in molten aluminium
So we expect the following form for hydrogen solubility:
)(2)(2 metal in solutiongas AlHH ⇔
2
2
Heq p
SK =
22 HoHeq pSpKS ==
where S is Hydrogen concentration in ml / 100g, partial pressure is in atmospheres
S = activity ~ concentration of hydrogen (ml/100g)= partial pressure hydrogen2Hp
equilibriumconstant
So is the equilibrium solubility in contact with pure hydrogen
(Sieverts’ Law)
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tsc What about alloying additions?
Some elements influence the solubility of hydrogen in liquid aluminium� relatively sparse data available, and even fewer for the effect in solid aluminium
Magnesium, titanium and lithium increase hydrogen solubility in liquid aluminium...
...whilst iron, copper, silicon and zinc reduce the solubility levels
pure aluminium
data from P.N. Anyalebechi,Scripta Met and Mater., 33 (8), p1209 (1995)
So Mg containing alloyspick up hydrogen more readily……and harder to degas
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Element wt.%
Hyd
roge
n so
lubi
lity
(ml/1
00g)
magnesium
titanium
zinc
silicon
copper
iron
pure aluminium
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tsc Alloy correction factors
The simple solubility equation for hydrogen in liquid aluminium needs to be corrected for the alloy composition� generally use interaction coefficients for excess solution free energy
Published experimental data extensively reviewed � some first order coefficients reliable, second order more variable
– some concern over Mg data
� temperature dependence not available for all elements� P.N. Anyalabechi, Light Metals, p827 (1998)
Alloy hydrogen solubility treated with a correction factor Calloy = 1/fH
2Hoalloyalloy pSCS =
...
...)log(
2222ZnZnSiSiCuCuMgMg
ZnZnSiSiCuCuMgMgH
WkWkWkWk
WkWkWkWkf
′′+′′+′′+′′+
′+′+′+′= fH = hydrogen activity coefficientWx = wt.% of xk’ = 1st order interactionk” = 2nd order interaction
C.H.P. Lupis, in “Liquid Metals Chemistry and Physics”,ed. S.Z. Beer (Marcel Dekker, 1972) G.K. Sigworth & T.A. Engh,
Met Trans B, 13B, p447 (1982)
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tsc But where does hydrogen come from?
The solubility of hydrogen is expressed on the basis of equilibrium between the melt in contact with H2 gas� but the partial pressure of hydrogen in the atmosphere is vanishingly small
Water vapour provides the source of hydrogen� aluminium can react with water vapour to form alumina and dissolved hydrogen
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0.100.15
0.200.25
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Temperature (C)
Hyd
roge
n (m
l/100
g)
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water vapour pressure (atm.)
5ºC, 50%RH
35ºC, 90%RHincreasingwater vapour
example conditions
25ºC, 80%RH
45ºC, 80%RH
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tsc Molten aluminium will pick up hydrogen from atmospheric humidity
But melting furnaces are usually gas-fired
Combustion products comprise ~15% water vapour H2O (allowing for excess air)
OHCONOCHN 222242 25.725.7 ++→++
furnace : combustion water vapour
summer : 45°C, 80% humidity
winter : 20ºC, 50% humidity
It gets worse…
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650 700 750 800
Furnace temperature (C)
Hyd
roge
n le
vel (
ml/1
00g)
furnace
summer
winter
holding furnacetemperatures
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tsc Typical hydrogen levels exiting a furnace
Example shows measured hydrogen levels in melt (ml/100g) exiting furnace, sampled over many hundreds of casts� commercial purity aluminium, furnace running at 725-750ºC
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cast #
H (m
l/100
g)
Generally found that hydrogen levels in melting and holding furnaces are dominated by equilibrium with furnace atmospheres
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tsc How much hydrogen can we live with?
Furnaces are quite turbulent environments
The melt rapidly achieves equilibrium with the local atmosphere
For nearly all applications, the level of dissolved H2 exiting furnace is too high…
…and must be reduced before casting
H2(ml/100g)
demanding products
typical commodity wrought products
aerospace products
holding furnace hydrogen levels
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melting furnace hydrogen levels
The acceptable level of hydrogen varies � depends on product and application
“Degassing” is the process by which the melt is treated to lower H2 levels
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tsc Hydrogen removal: batch degassing
The degassing process bubbles a dry inert gas through the melt� the melt tries to reach equilibrium with the gas by mass transfer of hydrogen
The kinetics are controlled by local equilibrium at the bubble-melt interface
H atom in liquid AlH2 molecule gas bubbleAr atom in gas bubbleextent of boundary layerFoseco batch degassing unit
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tsc Mass transfer between the melt and the bubbles
Hydrogen is transferred into gas bubbles, recombining as H2 molecules� partial pressure of hydrogen in the bubble stays in local equilibrium…
� …with concentration of hydrogen in the boundary layer around the bubble, Hi
This establishes a difference in hydrogen concentration between
� the bulk liquid, Hb and the boundary layer, Hi
which then drives mass transfer from the bulk melt to the bubbles
hydrogen partial pressurein bubble (atm.)
hydrogen concentrationin boundary layer
hydrogen concentrationin bulk liquid
)( ibii HHAk −=flux hydrogen
ki = hydrogen mass transfer coefficient (m/s)Ai = surface area of bubble
2Hp2Hoi PSH =
bH
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tsc Batch degassing kinetics
The mass transfer and associated local equilibrium boundary conditions, along with re-absorption from the atmosphere, is built into process models� quantitative understanding of local equilibrium at the bubble-melt interface is crucial
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0 200 400 600
Fluxing Time (seconds)
H (m
l/100
g)
model
#764
Comparison of kinetic modelwith trial degassing Al-9% Si
Web base degassing model developed for Foseco
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tsc Large furnaces… the need for in-line degassing
Batch degassers work well for small melts (e.g. < 1 tonne)
But modern wrought plants cast from 30-130 tonne furnaces� casts can take 1-2 hours duration
� ample time for the melt to up-gas once more in the furnace
� furnace degassing has become ineffectual and largely abandoned
M. B. Taylor, Aluminium 79, (1/2), p44, (2003)
Degassing and up-gassing kinetics in a holding furnace
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tsc In–line degassing
Wrought aluminium plants generally use in-line degassers� just before casting, allows no time to up-gas before solidification
Continuous process where metal flows through a reaction chamber� characterised by an average residence time (chamber volume/metal flow rate)
In line SNIF degasserwww.pyrotek.com
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tsc Just how do we measure hydrogen?
The levels of hydrogen we are dealing with in solution are rather low� 0.1 ml/100g ~ 0.09 ppm or ~ 0.1 gram of hydrogen per tonne of aluminium
And yet these levels are measured on line, in real time: all rely on equilibrium
A small volume of carrier gas re-circulates through a porous probe in the melt � hydrogen diffuses to the gas and recombines as H2 reaching equilibrium
www.abb.com
AlSCAN hydrogen measurement
Original Telegas system (Alcoa)
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tsc Data processing
All on-line hydrogen measurement methods entail measuring the partial pressure of hydrogen in equilibrium with the melt� we are not measuring hydrogen in the melt directly
In order to estimate the concentration of hydrogen dissolved in the melt:1. temperature used to calculate the equilibrium solubility for H2 in pure Al
2. measured used to calculate the H level in the melt (assuming pure Al)
3. calculated concentration corrected for effect of alloying elements on H solubility2Hp
0.05 atm. H2 pressure converts to three different H levels,depending on the melt composition
…so measurement devices relyentirely on knowledge of equilibrium H solubility, and its variation with alloy0.0
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0.6
0 0.05 0.1 0.15 0.2
PH2 (atmospheres)
H m
l/100
g
2Hp
Al
Al-5Mg
Al-10Si
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tsc Current issues: aluminium and hydrogen
Uncertainty over interaction parameters affects our ability to both measure gas levels on line reliably, and control degassing processes� the effect of magnesium is probably the most worrying
There are a reasonable amount of data concerning hydrogen solubility in pure liquid aluminium, and some data for a selection of binary alloys…� but hardly any for fully commercial alloys
Binary interaction coefficient contributions are assumed additive…� very limited evidence suggests this may not always be the case:
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700 750 800 850 900
Temperature (C)
Hyd
roge
n so
lubi
lity
(ml/1
00g)
7050 exp
7050 predicted
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700 750 800 850 900
Temperature (C)
Hyd
roge
n so
lubi
lity
(ml/1
00g)
Al-4Cu-0.9Mg-0.5Siexp
Al-4Cu-0.9Mg-0.5Sipredicted
P.N. Anyalebechi,Scripta Met and Mater., 33 (8), p1209 (1995)
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tsc 2) Extrusion processing
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tsc Extrusion alloys (6xxx)
0
0.2
0.4
0.6
0.8
1
1.2
1.4
0 0.2 0.4 0.6 0.8 1 1.2 1.4
wt% Si
wt%
Mg
150MPa 200MPa 250MPa300MPa
350MPa
AA6082
AA6005
AA6063
AA6060
“balanced” alloys
AA6061
Most common extrusion alloys are based on the Al-Mg-Si system (AA6xxx)� often with additions of Cu, Mn
Precipitation hardening system, based on the Al-Mg2Si pseudo-binary
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tsc Al-Mg-Si phase diagrams
The area of interest is the aluminium rich corner of the Al-Mg-Si system
0.2 0.4 0.6 0.8 1.0 1.2 1.4 1.6 1.8 2.0Al
wt.% silicon
0.2
0.4
0.6
0.8
1.0
1.2
1.4
1.6
1.8
2.0
550ºC500ºC
400ºC
“balanced”alloys
J. Zhang et al, Mat. Sci. Tech. 17, p494 (2001)
Pseudo-binary sectionAluminium solid solution isotherms
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tsc
0
100
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400
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600
700
0 0.2 0.4 0.6 0.8 1 1.2 1.4 1.6 1.8 2
Tem
pera
ture
(°C
)
wt% Mg2Si
AA6060 AA6063
AA6061
Al solidsolution
Extrusion process route: homogenisation
Extrusion logs are homogenised after casting, typically >570ºC� dissolution of soluble Mg2Si eutectic (quick)
� formation of Mn dispersoids, and phase transformation of cast intermetallics (slow)
H. Feufel et al, J. Alloys & Comp. 247, p31 (1997)
melttreatment
casting extrusionmeltinghomogenise
& coolpreheating agequench
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tsc Cooling after homogenisation
Note: no formal solution heat treatment stage in the process route
It might be thought quenching rapidly after homogenisation would be desirable� preserving Mg and Si in solid solution
� retaining it during extrusion and quenching, maximising the ageing response
Perhaps surprisingly, a slower cooling rate is usually deliberately applied� resulting in extensive fine re-precipitation of β’-Mg2Si needles
� (note these would be very over-aged in terms of final mechanical properties)
Quenched after homogenisation:Mg and Si retained in solid solution
Controlled cool after homogenisation (350°C/hr): nucleation of β’-Mg2Si needles
R.A. Ricks et al, Extrusion Technology 1992, pages 57 - 69
1µm
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tsc Preheating and extrusion
So what is the point of encouraging precipitation prior to extrusion?
The extruders have come up with a cunning plan:
Having the solute out of solution before extrusion lowers the flow stress� so they can extrude faster on a given extrusion press
But a correct selection of billet preheat temperature, combined with the heat of deformation, will carry the extrudate above the solvus� re-dissolving the precipitates, just before the extrudate is quenched
deformation heating occurs here
billetram
container
die
quench
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tsc Effect of cooling rate from homogenisation on flow stress
controlled cooling
waterquench
S. Zajac et al.,Mat. Sci. For. 396-402, p399 (2002)
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tsc In situ re-solutionising
This process allows maximum press productivity� whilst still ensuring maximum strengthening potential during subsequent ageing
Hence precipitates formed after homogenisation must not be too coarse� otherwise they won’t re-dissolve in short time available above the solvus
temperature rise due to deformation takes billet above solvus temperature for the alloy
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600630
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melting starts (solidus)
Mg and Si in solid solution (solvus)
induction furnace 100°C/min
criticalquench range
preheat
extr
usio
n
quench
Tem
pera
ture
(°C
)
Time (mins)
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tsc Potential problems (1)
The amount of deformation heating depends on the details of the extrusion� mainly the extrusion ratio (strain)
� and the strain rate (extrusion speed)
So operating practices need to be fine tuned for each product…� to ensure the extrudate achieves a temperature above the solvus…
� but below the solidus: otherwise incipient melting is observed
…and more concentrated alloys have a diminishing operating window:
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700
0 0.2 0.4 0.6 0.8 1 1.2 1.4 1.6 1.8 2
Tem
pera
ture
(°C
)
wt% Mg2Si
AA6060 AA6063
AA6061
Al solidsolution 50ºC
150ºC
surface melting(“speed cracks”)
N. C. Parson et al. Extrusion Technology 1992, p13
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tsc Potential problems (2)
Example of speed cracking, showing underlying re-melted eutectic colonies
O. Reiso,Mat. Forum 28, p32 (2004)
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tsc 3) Practical alloy development
Brazing sheet is a clad aluminium rolled product widely used heat exchangers � core typically AA3xxx, cladding typically Al-10%Si
A very elegant product, with one small problem…
www.aluminium-brazing.com
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tsc Scrap
What to do with the inevitable process scrap (ingot crops, edge trims, etc.) ?
The core and clad are metallurgically bonded: can’t separate� re-melted average composition typically : Al -1.4%Si -0.8%Mn-0.1%Mg
� this is x10 more Si than can be tolerated in most rolled products
The more successful the sales of brazing sheet, the more scrap created
Solution: register a new alloy designed to absorb the scrap: AA4015� typical application: low cost (painted) building sheet
Only problem: mechanical properties rather poor cf. normal building sheet
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tsc (Blind?) Alloy development
This is a cold rolled product, deriving its strength from a combination of work and solute hardening� not feasible to increase cold rolling reductions (start and end gauges fixed)
� only option: increase level of solid solution
Our client proposed increasing magnesium (and/or manganese) in the alloy� (wrought metallurgists rule of thumb: if in doubt, increase Mg for work hardening)
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350
0 0.5 1 1.5 2
cold rolling strain
yiel
d st
reng
th (
MP
a)
AA3004
AA4015
commercialreduction
The base alloy contains 0.1%Mgoff line process used to investigate:0.3% and 0.5%Mghoping to close the gap
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tsc Mechanical properties
Experimental alloys were cast up, homogenised, then hot and cold rolled
The results were surprisingly disappointing
Rolled to a common final gauge(strain), all A4015 variants showed~identical strength
And exactly the same behaviourseen on making Mn additions
We were invited to consider whether the client’s strategy made sense……and could we explain why it was all going wrong?
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150
200
250
300
AA3004 AA40150.1Mg
AA4015,0.3Mg
AA4015,0.5Mg
yiel
d st
reng
th (M
Pa)
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tsc The thermodynamic equilibrator
After homogenisation, slabs are hot rolled to ~ 3mm intermediate gauge
For this client, the final 3 passes are coil to coil� ~50% reductions, with many minutes between passes at ~350ºC
On reflection, you would be hard pressed to find a process better designed to drive an alloy to equilibrium in the solid state!
melttreatment
casting cold rollmelting homogenise hot roll
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tsc Al-Mg-Si again
The diagram shows the limit of solid solubility at 350ºC� data taken from Phillips (1961) and Feufel et al. (1997)
Increasing Mg in this alloy simply advanced into the 3 phase region at 350ºC� with a Mg solid solution level pegged to the corner of the triangle
0.2 0.4 0.6 0.8 1.0 1.2 1.4 1.6 1.8 2.0Al
wt.% silicon
0.2
0.4
0.6
0.8
1.0
1.2
1.4
1.6
1.8
2.0
350ºC
Al-Mg 2Si-Si
H. Feufel et al, J. Alloys & Comp. 247, p31 (1997)
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tsc What else can we add?
If Mn and Mg are ruled out because of the high Si in the alloy, what could we add (cheaply) that would be retained in solution?� Cu was a candidate, provided the Mg level was also kept low (avoiding Q phase)
� potentially could retain e.g. 0.4-0.8 %Cu in solution
calculations undertaken by Chart Associates (2005)
Al-0.1Mg-0.8Mn-1.4Si-0.8Cu
400 450 500 550 600 650 700
0.000
0.002
0.004
0.006
0.008
0.010
0.012
T/C
Cu Cu
Cu
Mg MgMn
Si
Si Si
mas
s fr
actio
n in
FC
C
Al-0.2Mg-0.8Mn-1.4Si-0.8Cu
400 450 500 550 600 650 700
0.000
0.002
0.004
0.006
0.008
0.010
0.012
T/C
CuCu
Cu
MgMg Mg Mn
Si
SiSi
mas
s fr
actio
n in
FC
C
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tsc Success?
Measured
Predicted
0
50
100
150
200
250
300
0 0.3 0.5 0.8Cu (wt %)
Yie
ld S
tren
gth
(MP
a)
predictedmeasured
A series of alloys were cast based on AA4015 with Cu additions� containing 0.3, 0.5 and 0.8 wt.% Cu
For a fixed strain, 0.8% Cu alloy achieved ~75MPa strength increase� in reasonable agreement with strain hardening prediction
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tsc Strength ok, but corrosion?
Not surprisingly, although Cu additions addressed the strength issue…
…they also degraded the corrosion resistance of the product
Not as much of an issue as might be expected: it is a coated product� but would limit its application as a bare product
0% Cu 0.3% Cu 0.5% Cu 0.8% Cu
corrosion test samples, 500 hours acidified salt spray (ASTM B287)(overlaid with image analysis of pitting corrosion)
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tsc Conclusions
� These application examples have been chosen to try and demonstrate the importance of setting phase equilibria predictions in a larger context
� There are times when thermodynamic equilibrium is achieved, either unavoidably or by design…
�…and other times when the process route has evolved to avoid equilibrium at all costs
� One of the most important application areas of phase equilibria relate to the provision of realistic local equilibrium boundary conditions� increasingly required by microstructural kinetic models during processing
� Understandably there are gaps in the availability of reliable experimental data concerning metastable phase equilibria…
�…but some equilibrium data also very sparse for molten aluminium alloys� e.g. relating to hydrogen in ternary or higher alloys
� e.g. interactions of molten salts with molten aluminium alloys (alkalis)
� e.g. solubility of carbon in molten aluminium, and precipitation of carbides