Ion irradiation induced impurity redistribution in Pt/C multilayers
Transcript of Ion irradiation induced impurity redistribution in Pt/C multilayers
Nuclear Instruments and Methods in Physics Research B 212 (2003) 530–534
www.elsevier.com/locate/nimb
Ion irradiation induced impurityredistribution in Pt/C multilayers
S. Bera a, D.K. Goswami a, K. Bhattacharjee a, B.N. Dev a,*,G. Kuri b,1, K. Nomoto c, K. Yamashita c
a Institute of Physics, Sachivalaya Marg, Bhubaneswar 751005, Indiab Hamburg Synchrotron Radiation Laboratory (HASYLAB) at DESY, Notkestar 85, D-22603 Hamburg, Germany
c Department of Physics, Nagoya University, Nagoya 464-8602, Japan
Abstract
Ion irradiation induced modifications of a periodic Pt/C multilayer system containing Fe impurity have been ana-
lyzed by X-ray techniques suitable for exploring nanometer depth scales with sub-nanometer depth resolution. The
multilayer stack with 15 Pt/C layer pairs (period 4.23 nm, total thickness 63.45 nm) was fabricated on a glass substrate.
A 2 MeV Au2þ ion beam was rastered on the sample to obtain uniformly irradiated strips with fluences from 1� 1014 to
1� 1015 ions/cm2. These strips were analyzed with X-ray standing wave and X-ray reflectivity experiments. Ion induced
atomic displacements across multilayer interfaces are known [Appl. Phys. Lett. 79 (2001) 467]. Here additionally we
identify irradiation induced redistribution of Fe impurity atoms, which cannot be explained simply by atomic dis-
placements due to ion–atom collision. With increasing ion fluences more Fe atoms migrate from C- to Pt-layers. This
behaviour has been explained in terms of radiation induced enhanced diffusion and Fe–Pt and Fe–C phase diagrams.
� 2003 Published by Elsevier B.V.
PACS: 61.80; 68.65.A; 68.49.U
Keywords: Layered synthetic microstructures; X-ray standing wave; Ion-beam induced impurity redistribution
1. Introduction
The knowledge obtained from the studies of
ion–solid interactions has been utilized in many
applications, for example, surface chemical and
structural analysis, sputtering in production of
* Corresponding author. Tel.: +91-674-2301058; fax: +91-
674-2300142.
E-mail address: [email protected] (B.N. Dev).1 Present address: Paul Scherrer Institute, CH-5232 Villigen
PSI, Switzerland.
0168-583X/$ - see front matter � 2003 Published by Elsevier B.V.
doi:10.1016/S0168-583X(03)01508-8
thin films and surface cleaning, ion implantation,ion beam modification of structure and properties
etc. Currently exciting possibilities are emerging in
the area of ion beam modifications of layered
synthetic microstructures (LSM�s). LSM�s are
fabricated by depositing alternating layers of two
different materials on a substrate. The LSM�s havewide ranging applications. Properties of such
multilayers can be modified by introducing impu-rities or by other means, such as, exposure to en-
ergetic ion beams. Magnetic multilayers, e.g. Co/
Cu/Co/. . .. multilayers, have shown drastic change
in magnetic coupling and magnetoresistance in the
S S S
S
Si(Li)NaI
K
1
2
S0
1 2 3
4
A B C D E F
SA
Ge(111)
IC
DORIS
RingStorage
NaI
Ge(111)
SA
θ
θ
Fig. 1. Schematic experimental setup for XSW and XRR ex-
periments with synchrotron radiation. S0–S4: slits; IC: ioniza-
tion chamber; K: kapton foil; Ge(1 1 1): Ge double crystal
monochromator; SA: sample; NaI, Si(Li): detectors. Top view
of the irradiated sample configuration is shown in the inset.
S. Bera et al. / Nucl. Instr. and Meth. in Phys. Res. B 212 (2003) 530–534 531
presence of magnetic impurities (e.g. Ni) in the
nonmagnetic (Cu) layers [1]. Co/Pt/Co/. . . multi-
layers, when exposed to energetic ion beams, show
spin reorientation transition. Such systems aresuited for ultrahigh density recording media [2].
Ion beam is known to cause atomic displacements
across the interfaces of the multilayer system
(MLS) [3]. From these examples it is clear that
atomic distribution and ion beam induced redis-
tribution in multilayers are important aspects to be
investigated for an understanding of the multilayer
properties. However, wherever layer thicknesses ofthe order of 1 nm in a multilayer are involved there
are not many techniques available to study atomic
distribution over this depth scale. Combined X-ray
standing wave (XSW) and reflectivity (XRR)
analysis has been shown to be capable of deter-
mining this distribution [4]. In the present paper
we report the preliminary results of a combined
XSW and XRR analysis for the impurity (Fe) re-distribution in a Pt/C periodic MLS due to ion
irradiation. A Pt/C multilayer has been chosen as a
model system as the large electron density contrast
between Pt and C gives rise to strong Bragg dif-
fraction peaks from a periodic Pt/C multilayer.
This in turn generates a strong standing wave field
in the multilayer. Additionally, ion irradiated Pt/C
multilayers with Fe impurity may themselves showinteresting magnetic behaviour as there are possi-
bilities of formation of Fe–Pt magnetic alloys,
possibly as small clusters.
2. Experimental
Pt/C multilayers were fabricated on float glasssubstrates, kept at room temperature, by ion beam
sputtering. Samples were grown at a low Argon
pressure of 0.1 mbar. Fe impurity was introduced
in the multilayers during growth. The expected Fe
concentration in the C-layers was about 10 at.%.
The Pt/C multilayer sample with Fe incorporation,
used in this study, was prepared at Nagoya Uni-
versity. The sample specifications are: N ¼ 15 (thenumber of layer-pairs in the multilayer stack),
d ¼ 4:23 nm (multilayer period, i.e. the thickness
of a Pt/C layer-pair), C ¼ 0:38 (ratio of Pt layer
thickness to d). The total thickness of the multi-
layer stack is 63.45 nm. Different parts of a large
sample (30� 70) mm2 were irradiated with 2 MeV
Au2þ ions by rastering the ion beam on (30� 5)
mm2 strips at various fluences (ions/cm2) [A(vir-
gin), B(1� 1014), C(3� 1014), D(5� 1014),
F(1� 1015)] at Institute of Physics, Bhubaneswar.
The sample configuration (top view) is shownschematically in the inset of Fig. 1. The range of 2
MeV Au ions in the sample is such that the im-
planted ions are buried deep into the glass sub-
strate well past the multilayer stack. XSW and
XRR experiments were carried out at Hamburg
Synchrotron Radiation Laboratory (HASYLAB
at DESY), Hamburg, at the ROEMO-I beamline
using 14.0 keV monochromatized X-rays. Theexperimental setup is schematically shown in Fig.
1. Fe–K and Pt–L fluorescent photons were de-
tected by a Si(Li) detector and the reflectivity was
measured by a NaI(2) detector. Scattered X-rays
from a kapton foil (K) was monitored in a NaI(1)
detector for the normalization of incident X-ray
intensity. Slits S2 define the incident beam. S3 are
the antiscattering slits.
3. Results and discussion
Let us first discuss what is expected from dif-
ferent distributions of Fe in the Pt/C multilayers.
The inset in Fig. 2 shows the schematic cross-sec-
tional view of the periodic Pt/C MLS. The firstorder Bragg diffraction region from the Pt/C MLS
is shown in Fig. 2 along with some additional
theoretical plots. Standing waves of X-rays are
generated in the MLS when Bragg diffraction oc-
curs. As the angle of incidence ðhÞ of X-rays
0.54 0.64 0.740.74
0
0.2
0.4
0.6
0.8
A
B
C
D
Flu
ores
cenc
e Y
ield
(A
rbitr
ary
Uni
ts)
θ (degree)R
efle
ctiv
ity
F
Fig. 3. Experimental reflectivity and FY: the Bragg peak (––)
for the virgin sample (A) and the Fe–Ka FY (. . .) for the virgin
(A) and the irradiated samples (B–F). The FY curves have been
shifted vertically for clarity.
0.54 0.64 0.740
0.5
1
1.5
2
2.5
3
0
0.2
0.4
0.6
0.8
1
Glass
PtC
Flu
ores
cenc
e Y
ield
(N
orm
aliz
ed)
Ref
lect
ivity
(degree)θ
Fig. 2. Theoretical plots showing the first order Bragg peak and
Fe FY from a Pt/C multilayer for three cases. Reflectivity (––),
Fe in uniform depth distribution only in the C-layers (– – –), Fe
in uniform distribution in both Pt- and C-layers (. . .), Fe in
uniform distribution only in the Pt-layers (– - –). The cross-
sectional view of the multilayer is shown in the inset.
532 S. Bera et al. / Nucl. Instr. and Meth. in Phys. Res. B 212 (2003) 530–534
advances, in passing the Bragg peak, the periodic
antinodal planes move from the centre of the C-
layers to the centre of the adjacent lower Pt-layers
(through half the period distance d) over the wholedepth of the multilayer. Thus the impurity atoms(as well as host atoms) are exposed to a variation
of X-ray intensity as h changes. As the intensity of
emission of fluorescent photons from an atom in
the sample would be proportional to the field in-
tensity on that atom, the fluorescence yield (FY)
also would have a h-dependence. The h-depen-dence of the Fe FY would depend on the depth
distribution of Fe in the MLS. Some theoreticalplots of Fe FY as a function of h for specific Fe
distributions, following [4], are shown in Fig. 2.
The reflectivity and the field intensities (or FYs)
have been calculated for pure Pt- and C-layers.
These are used only as a guide to understand the
Fe FY variations in Fig. 3.
We notice from Fig. 2 that if Fe is uniformly
distributed only in the C-layers, Fe FY would peakon the rising edge of the Bragg peak. A uniform
depth distribution of Fe within both Pt- and C-
layers would still give rise to a Fe FY peak on the
rising edge of reflectivity, although with a lower
intensity. On the other hand, a uniform distribution
of Fe only in the Pt-layers would give rise to a Fe
FY peak at the falling edge of the Bragg peak. Thus
a simultaneous measurement of reflectivity and Fe
FY on samples irradiated with different ion fluences
would give information on Fe redistribution in the
MLS. XRR measurements were performed for the
h-range: 0–2.9� and simultaneous reflectivity and
FY (Fe–Ka;b, Pt-La;b;c) measurements were per-formed over the first order Bragg peak region. A
full quantitative analysis of data will be presented
elsewhere. Here we present a qualitative analysis
which is adequate to show impurity redistribution.
We may define a parameter a as the ratio of FY
peak intensity at the low-angle side of the Bragg
peak to that at the high-angle side. We notice from
Fig. 2 that a � 1, a > 1 and a < 1 represent thethree situations discussed above (Fe in C-layers, Fe
in both Pt- and C-layers, Fe in Pt-layers), respec-
tively. As more Fe migrates from C- to Pt-layers,
the Fe FY peak on the rising edge of the Bragg peak
gradually decreases and the FY peak on the falling
edge gradually increases. This corresponds to a
gradual decrease of the value of a. So we can now
discuss redistribution of Fe in terms of a.
S. Bera et al. / Nucl. Instr. and Meth. in Phys. Res. B 212 (2003) 530–534 533
The results of measurements of reflectivity over
the first order Bragg peak region and the corre-
sponding Fe–Ka FY for the strips A, B, C, D and
F are shown in Fig. 3. (The FY curves have beengiven the required corrections as discussed in [4].)
The first order Bragg reflection from the virgin
sample (A) is shown. The angular position of the
Bragg peak for irradiated samples are usually
somewhat different [3]. The details along with full
XSW and XRR analysis to extract various mul-
tilayer parameters will be presented elsewhere.
The Fe–Ka FY curves, shown in Fig. 3, do notexactly correspond to the angles shown in the
abscissa. They represent the FY variation with
respect to their corresponding Bragg peaks. We
notice for the virgin sample (A) that the Fe–Ka
FY peak at the low-angle side of the Bragg peak
is higher. The FY curve shows similarity to the
theoretical curve (Fig. 2) for uniform distribution
of Fe in both Pt-and C-layers. (The detailed dis-tribution may be somewhat different.) This cor-
responds to a > 1. From the fabrication of the
multilayer, although the Fe impurity was ex-
pected predominantly in the C-layers, it is clear
from the Fe–Ka FY curve A that there is already
a higher concentration of Fe in Pt-layers than in
C-layers in the virgin sample. FY data marked B–
F are for increasing ion fluences. (We have notmade measurements on the strip E.) In B, Fe FY
intensities at both edges of the Bragg peak are
approximately equal ða ’ 1Þ. For higher ion flu-
ences (C–F), the intensity is always higher on the
high-angle edge ða < 1Þ, corresponding to in-
creasing Fe concentration in the Pt-layers. This
indicates that on passing from A to F, Fe in the
Pt/C MLS has been considerably redistributedwith higher ion fluences, generating a higher
concentration of Fe in the Pt layers. In fact the
Fe FY shapes for the samples D and F nearly
correspond to the Pt–L FY shapes (not shown
here). Pt–La yield curves for all cases correspond
to a < 1. (The detailed distributions of Fe and
other parameters of the Pt/C multilayers, can be
obtained from a complete combined XSW andXRR analysis [3,4].)
Reflectivity at the Bragg peak depends on the
electron density contrast between the two compo-
nents of a bilayer in a MLS and on interface
roughness. When C-layers are depleted of Fe, the
electron density contrast between the Pt- and the
C-layers is expected to increase. This would in turn
give rise to a more intense Bragg peak. Indeed thereflectivity at the Bragg peak for the sample D (not
shown here) is 0.69 and that for the virgin sample
(A) is 0.65 (shown in Fig. 3). For the virgin sample
the typical surface and interface roughnesses are
0.3–0.4 nm [3,4]. For higher ion fluences, intro-
duction of increasing interface roughness and re-
duction of electron density contrast, due to the
displaced atoms of one type into the other layerfrom ion induced collision cascades, lead to a
lower peak intensity. The peak reflectivity ob-
served for the sample F is 0.57.
Let us try to understand how and why Fe mi-
grates preferentially into the Pt-layers from the C-
layers. Energetic ion beams are known to cause
atomic displacements. A simulation of 2 MeV Au
ion bombardment of a Pt/C multilayer has earliershown displacements of C and Pt across the in-
terfaces producing a concentration of Pt in C-
layers and a concentration of C in Pt-layers [3]. In
the ion bombardment process Fe also would be
displaced. However, preferential Fe migration into
Pt-layers cannot be explained simply by the ion–
atom collision process. However, an enhanced
diffusion can set in due to ion irradiation causingFe migration. The preferential Fe migration per-
haps can be understood from the Fe–Pt [5] and
Fe–C [6] phase diagrams. FexPt1�x can exist
practically for any value of x. However for
FexC1�x, x can assume only large values. There are
no known phases of FexC1�x for x < 0:75. The
most carbon-rich phase is Fe3C. Thus with a small
quantity of Fe being present in the multilayer, Featoms would prefer to be in the neighbouring Pt
layers provided they have mobility to migrate from
the C-layers. In the Pt layers, a small amount of
Fe can form Pt-rich phases, e.g. FePt3. Fe in
Pt may exist in several possible phases or even as
Fe clusters. These aspects can be investigated by
exploring the local environment of Fe in extended
X-ray absorption fine structure experiments bytuning the antinodes of the standing wave field in
the Pt-layers. We have performed such experi-
ments. However, these aspects are beyond the
scope of this paper.
534 S. Bera et al. / Nucl. Instr. and Meth. in Phys. Res. B 212 (2003) 530–534
Formation of Fe clusters or Fe–Pt clusters
could be very interesting as there could be a drastic
variation of magnetic moments for clusters. For
example, the magnetic moment of a Rh atom is3lB/atom while bulk Rh is nonmagnetic. Rh
clusters containing between 9 and 100 atoms have
been found to be magnetic. Small Rh clusters such
as dimers (2lB/atom) and trimers (1lB/atom) carry
substantial moments [7]. In view of this and our
observation of ion beam induced Fe migration
into Pt layers in Pt/C(Fe) multilayers, we predict
that Pt/C(Fe) multilayers and ion irradiated Pt/C(Fe) multilayers would show very interesting
magnetic behaviour.
4. Conclusions
We have carried out irradiation of Pt/C multi-
layers, containing a small amount of Fe impurity,
with 2 MeV Au2þ ions at different ion fluences.
The samples were characterized by a combined
XSW and XRR analysis. Ion beam induced Fe
redistribution was observed. Higher ion fluenceslead to increasing Fe concentrations in the Pt-
layers due to migration of Fe from C-layers to Pt-
layers. This phenomenon cannot be explained
simply by the ion–atom collision process. The re-
sults have been explained in terms of radiation
enhanced Fe diffusion and Fe–Pt and Fe–C phase
diagrams.
Acknowledgements
We thank the technical staff of the Ion Beam
Laboratory of IOP, Bhubaneswar. BND ac-
knowledges the local hospitality from HASYLAB
during the experiments with synchrotron radia-
tion. The work was partly supported by ONR
Grant no. N00014-95-1-0130.
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