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High tensile plasticity and strength of a CuZr-based bulk
metallic glasscomposite
Zhiliang Ning, Weizhong Liang, Mingxing Zhang, Zongze Li,
HaichaoSun, Ailian Liu, Jianfei Sun
PII: S0264-1275(15)30694-8DOI: doi:
10.1016/j.matdes.2015.10.117Reference: JMADE 856
To appear in:
Received date: 7 August 2015Revised date: 17 October
2015Accepted date: 20 October 2015
Please cite this article as: Zhiliang Ning, Weizhong Liang,
Mingxing Zhang, Zongze Li,Haichao Sun, Ailian Liu, Jianfei Sun,
High tensile plasticity and strength of a CuZr-basedbulk metallic
glass composite, (2015), doi: 10.1016/j.matdes.2015.10.117
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http://dx.doi.org/10.1016/j.matdes.2015.10.117http://dx.doi.org/10.1016/j.matdes.2015.10.117
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High tensile plasticity and strength of a CuZr-based bulk
metallic
glass composite
Zhiliang Ning,1*
Weizhong Liang,
2 Mingxing Zhang
3 Zongze Li,
2 Haichao
Sun,1
Ailian Liu2
, Jianfei Sun1
1. School of Materials Science and Engineering, Harbin Institute
of Technology, Harbin 150001,
China
2. Heilongjiang University of Science and Technology, Harbin,
150022, China
3. School of Mechanical and Mining Engineering, The University
of Queensland, St Lucia, QLD
4072, Australia
* Corresponding author: Tel.: +86-451-88418317; Fax:
+86-451-86413904
E-mail address: [email protected]
Abstract: A new approach to improve the tensile ductility of
CuZr-based bulk metallic glasses
without significant reduction in high strength is reported.
After doping of Nb into CuZr-based
alloy, a composite was formed with a combination of high
strength, large tensile plasticity and
strong work-hardening effect. The addition of Nb led to a
uniform distribution of single B2-CuZr
phase in the glassy matrix. The optimal tensile properties were
attributed to the
deformation-induced martensitic transformation of the B2-CuZr
phase, which in turn interacted
with the glassy matrix. In addition, the drastic adiabatic
heating on the fracture region also
contributed to the increase in tensile plasticity.
Keywords:Bulk metallic glass; Composite; Martensitic
transformation mediated plasticity; Tensile
properties
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1. Introduction
Due to the high strength and hardness, combined with high
corrosion resistance, bulk
metallic glasses (BMGs) have strong potential to be used as a
new type of structural and
functional materials [1-7]. Currently the bottleneck issues that
limit the engineering applications
of BMGs are the room temperature brittleness and strain
softening behaviors [8-12]. It has been
considered that development of BMGs composites (BMGCs) that
contain either in-situ formed or
externally added crystalline particles within the glassy matrix
is an emerging approach to solve
these problems [1-3, 13-17]. A notably tensile ductility
resultantly has been achieved in Ti-based
[18-19] and Zr-based [19-21] BMGCs. With increasing the
plasticity, the strength of BMGCs is
deteriorated simultaneously. However, the precipitation of the
B2-CuZr crystalline phase in the
glassy matrix in a CuZr-based BMGCs has led to concurrent
improvement of both tensile plastic
deformation ability and work-hardening capacity [22-24]. The
plastic-predeformation-induced
stress state resulted from the B2-CuZr phase in the metallic
glass was believed as the reason for
the higher tensile ductility and strain-hardening capability of
CuZr BMGCs [25]. However, it is
still unclear how to control the B2-CuZr precipitation, such as
the shape and size of the crystalline
particles, and therefore to maximize the advantage of this
phase. Up to date, the elucidation of the
correlation between CuZr phase features, and the tensile
properties for CuZr-based BMGCs
through controlling compositions is still remained unclearly
[24]. Hence, the present work aims to
seek an alternative approach to increase the ductility of a
CuZr-based BMGs without significant
reduction in strength through modification of its chemical
composition using Nb to partially
replace Cu and to understand the related mechanisms. The
selection of Nb as an alloy addition is
based on previous report [27]. That the ductility of BMGCs can
be improved by tailoring the
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stacking fault energy. Furthermore, the effects of the chemical
composition on the features of the
B2-CuZr crystalline precipitate and then on the tensile
properties are also investigated and
discussed.
2. Experimental Procedures
Button ingots of Cu48-xZr48Al4Nbx (x=0, 1, 3, 3.7, 5 at. %)
alloys were fabricated by arc
melting of mixtures of the composing element (99.9% purity) in a
Ti-gettered argon atmosphere.
All ingots were re-melted four times to ensure chemical
homogeneity by applying arc-melting
current of 200 A. Cylindrical rods with 3 mm in diameter and 45
mm long were synthesized by
drop-casting into a copper mould in a purified argon atmosphere.
The phase structures were
characterized by X-ray diffraction (XRD) with Cu-Kα radiation
(λ=1.5405Å) using a D/MAX-RB
diffractometer and Microarea X-ray diffraction (MAXRD).
Microstructures of the cast samples
were examined using a Carl Zeiss optical microscope (OM) and a
JEM 2010F field emission
transmission electron microscopy (TEM). Thermal analysis was
carried out by a Pyris-1
differential scanning calorimetry (DSC) at a heating rate of
0.33K/s. Tensile tests on the BMGCs
with different Nb content were performed using a dog-bone shape
samples in an INSTRON-5569
testing machine with a strain rate of 3.5× 10-4
s-1
. The fracture surfaces of the tensile samples were
observed in a HITACHI S-4700 scanning electron microscope (SEM).
In order to investigate the
Young’s modulus and hardness of both the crystals and glassy
matrix in the cast samples,
nanoindentation tests were conducted on a TriboIndenter in-situ
Nanomechanical test system with
a maximum load of 10 mN.
3. Results and discussion
Fig.1 shows the XRD spectra taken from 3-mm-diameter cylindrical
rods of CuZrAl
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BMGCs with various concentrations of Nb doping. Without addition
of Nb, both Al2Zr and
B2-CuZr crystalline phases were detected, which is consistent
with the previous report [23]. For
the alloy containing 1% Nb, the XRD spectrum shows one broad
diffuse peak around the
diffraction angle of 38o without any apparent crystallization
peaks, indicating full glassy structure.
The larger mixing degree of CuZrAl ternary system induced by the
small amounts addition of Nb
is responsible for the increase of glass-forming ability (GFA).
Similar results were reported
previously [28-29]. Further increasing the Nb content from 3% to
5%, an extra peak that
corresponds to the B2-CuZr phase appears on the top of the
diffuse peak, suggesting that the
addition of 3-5% Nb promoted the formation of the B2-CuZr phase
in the glassy matrix. With
increase in Nb content, the intensity of the B2-CuZr peak
increases, indicating higher volume
fraction of the B2-CuZr crystalline phase at higher Nb content.
In addition, higher Nb content also
suppressed the formation of the Al2Zr phase as a result of the
competitive formation mechanism of
Al3Nb phase during solidification [23, 26]. It is not
contradictive that the different amounts of Nb
promote the GFA and the precipitation of B2 CuZr. Minor addition
of Nb promotes the GFA due
to increasing mixing degree of CuZrAl system, while the large
amount of addition of Nb acts as
the nucleus of B2 CuZr, resulting in the precipitation of B2
CuZr.
To understand the effect of Nb addition on the phase structure
evolution of the CuZrAl
BMGCs, DSC analysis was carried out on the Cu48-xZr48Al4Nbx
(x=0, 1, 3, 3.7, 5 at.%) alloys
during continuously heating process. The DSC curves that record
information of phase
transformations are shown in Fig.2. It can be seen that the
transformation in all alloys contains a
glass transition process followed by an exothermic heat
characteristic for crystallization. The
ternary Cu48Zr48Al4 alloy without Nb doping exhibits a smaller
heat release than that of the alloy
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doped by different Nb contents. The heat released due to the
crystallization of these BMGCs
decreases gradually with the increase in Nb concentration from
1% to 5%. This means that the
volume fraction of the amorphous matrix is reduced due to the
increase of the volume fraction of
the crystalline phase at higher Nb addition. The volume
fractions of the crystalline phase are
estimated to be 8%, 24%, 28% and 40%, for 1%, 3%, 3.7% and 5%
Nb-added 3 mm diameter
samples, respectively. This deduced result is consistent with
that from XRD analysis. However,
both the glass transition temperature (Tg) and the onset
crystallization temperature (Tx), decrease
with increasing Nb concentration. This once again evidences that
the addition of Nb promoted the
formation of the B2-CuZr phase in the CuZr-based BMGCs.
Figure.3 presents the optical metallographs of the
cross-sectional microstructures of the
Cu48-xZr48Al4Nbx (x=0, 1, 3.7, 5 at. %) alloys. In the Nb-free
sample, a larger volume fraction of
the B2-CuZr and Al2Zr phases with various morphologies can be
observed in the glassy matrix,as
shown in Fig. 3a. For the alloy with 1% Nb addition (Fig. 3b),
only a few small spherical B2-CuZr
particles are found, which agrees with the XRD results.
Increasing the Nb content to 3.7%, much
more spherical B2-CuZr particles with a size ranged from ~30 to
~60 μm homogeneously
distributed in the glassy matrix (see Fig. 3c), which likely
gives rise to enhanced tensile ductility
because the size of the particles is very close to the plastic
zone of the glassy matrix [7]. However,
in the 5% Nb sample, a few B2-CuZr particles with heterogeneous
distribution and non-uniform
sizes embedded into the glassy matrix. According to the
metallography, it is clear that 3.7% Nb
addition promoted the uniform nucleation of the B2-CuZr
particles during the rapid solidification
process. The distribution of B2 CuZr crystals depends on the Nb
content, which may be explained
by the nucleation and growth kinetics of the Nb added samples.
It is speculated that Nb may act as
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heterogeneous nucleation sites for B2-CuZr phase because the
body-centered cubic structure of
Nb (with a lattice parameter of a = 3.3004 Å) is very similar to
that of the B2-CuZr phase (a =
3.2562 Å). In addition, the finer B2-CuZr particles in the
3.7%Nb sample is possibly attributed to
the slow growth rate of this particles resulted from the
sluggish growth kinetics. Similar effect was
reported for Ta atom in the Cu-Zr-Al alloy, where the growth of
B2-CuZr phase was suppressed
by 0.9% Ta addition [5].
The tensile true stress-strain curves of the Cu48-xZr48Al4Nbx
(x=0, 1, 3, 3.7, 5 at. %) alloys
are plotted in Fig. 4. The ternary Cu48Zr48Al4 alloy without
Nb-doping exhibited typical brittle
fracture with lower fracture strength of 1510 ± 65 MPa without
distinct yielding. This implies that
the non-uniformly distributed B2-CuZr and Al2Zr particles in the
glassy matrix did not contribute
to both strengthening and enhancement of ductility. 1% to 5%
Nb-doping led to increase in the
fracture strength up to 1810 ± 50 MPa at of 3.7% Nb, but only
the CuZr-based BMGCs doped by
3.7% Nb exhibited a significantly plastic deformation with the
ductility of 7% and a prominent
work-hardening behavior before fracture. 1%, 3% and 5% Nb-added
alloys do not show any
significant tensile plasticity, which display the fracture
strength of 1700 ± 40, 1782 ± 15 and 1600
± 60 MPa, respectively. It is evident that the larger fracture
strength can be achieved in the
CuZr-based BMGCs due to the enhanced glassy forming ability by
doping of Nb into CuZr-based
alloy. The addition of 3.7% Nb promoted the martensitic
transformation of the reinforcing
B2-CuZr crystals, which was confirmed by the HRTEM image of the
3.7% Nb-added cast sample
shown in Fig.5. Some stacking faults inside the B2 crystals were
observed, as indicated by the
white arrow in Fig.5, which is consistent with the features of
the B2 crystals in the Co-containing
alloy [10]. These stacking faults greatly promoted the
martensitic transformation, thus notably
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improved tensile plasticity of the 3.7% Nb-added alloy.
Previous studies [7, 20] indicated that matching of soft
reinforcing particle size to the
characteristic length scale pR can suppress shear band extension
and therefore enhances the
plasticity. pR is a materials scale related to fracture
toughness in tension, it can be expressed as:
2 2/ 2p IC YR K (1)
where ICK is fracture toughness, and Y is yield strength [20,
24]. For the 3.7% niobium alloy,
pR can be estimated to be 175um by adopting ICK =50MPa m1/2
and Y =1500 MPa. Therefore,
the crystal size of the 3.7% niobium sample matches to the order
of magnitude of pR . As a result
the tensile ductility was enhanced.
The fractography of the Cu48-xZr48Al4Nbx (x=0, 3.7, 5at. %)
alloys is shown in Fig.6. Fig.6a
exhibits a shear fracture along a shear angle of 35º and a small
number of shear bands on the
lateral surface of the Nb-free sample (pointed by the white
arrow). In the enlarged area circled by
a white box in Fig. 6a, it can be seen that a spherical B2-CuZr
phase inhibits the propagation of
multiple shear bands, as shown in the inset of Fig. 6a. Some
dendrites-like patterns and a few
melting drops were observed to appear on the fracture surface of
the Nb-free sample, as shown in
Fig. 6b. The shear fracture occurs along a shear angle of 34º
for the 5% Nb-added sample, and a
few slender shear bands come out on its lateral surface, as
shown in the inset of Fig. 6c. Some
typical round-core patterns appear on the fracture surface with
obvious melting character for the
5% Nb-added sample (Fig. 6c). Fig.6d shows that shear fracture
occurs along a shear angle of 50º,
larger than 45º,and many short shear bands appear on the lateral
surface of the 3.7% Nb-added
sample. The amplificatory image of the area circled by a white
box in Fig. 6d shows the distorted
martensite phases with slat structures (see the inset of Fig.
6d), which is the important evidence of
a phase transformation-mediated plasticity. Afterwards, further
observations show that some
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vein-like patterns and martensite phases indicated by an oval
appear on the fracture surface with a
drastically melting character (Fig.6e). In addition, it is
interesting to find a peculiar feature with
the stripped marks near the interface between the martensite
particles and the glassy matrix, as
indicated by the black arrow in Fig.6f. The parallel slats of
the martensite particles are pointed by
the white arrow in Fig.6f.
For the Cu48-xZr48Al4Nbx (x=0, 3.7, 5 at. %) BMGCs samples, due
to the difference in their
microstructures, shear deformation occurs along the different
shear angles when subjected to a
tensile load. Their plastic deformation behaviors are mainly
controlled by the B2-CuZr phases.
How to understand why the 3.7% Nb-added sample displays a very
high tensile plasticity of 7%?
There are martensite phases on the side surface and fracture
surface, which implies that the
propagation of the main shear crack may be hindered by the
martensite particles in the glassy
matrix. To further confirm this hypothesis, i.e., the tensile
deformation-induced martensitic
transformation of the B2-CuZr phase, the Microarea-XRD patterns
of the fractured 3.7%
Nb-added sample are obtained and shown in Fig.7. As compared
with the XRD pattern taken from
the as-cast 3.7% Nb-added sample, reflection of the B19’ phase
appears in different areas on the
tensile fractured surface. Area I and area II are marked in the
inset of Fig.7, which correspond to
the beginning position and the concluding position of the shear
fracture process.
Moreover, Fig.6f shows that there are some stripped marks on the
fracture surface,
suggesting that the martensite particles interacted with the
glassy matrix under tensile loading,
similar to the report before [5]. How to further understand
clearly the interaction between the
glassy matrix and martensite particles? Nanoindentation tests on
the crystallites and glassy matrix
were performed on the Nb-free and 3.7% Nb-added samples,
respectively. The load-displacement
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(P-h) curves in load-control mode at different positions of the
two samples are shown in Fig.8.
The P-h curves present few displacement discontinuities marks
(pointed by arrows) at position
B2-CuZr phase (Fig.8e and 8d), implying the better plastic
deformation, and the yielding of the
B2-CuZr phase is suggested to correspond to the initiation of
the martensitic transformation [27].
However, at positions glassy matrix and Al2Zr phase, the shape
of the P-h curves became
smoother (Fig. 8a, 8b and 8c), indicating of the poorer plastic
deformation. The nanoindentation
results are given in Table 1. It is clear that the Young’s
modulus and hardness of the microsized
Al2Zr phase in the Nb-free samples are higher than those of the
glassy matrix and the B2-CuZr
phase. It can be deduced that the stress would concentrate on
the interface between the glassy
matrix and the Al2Zr phase, which leads to the shear fracture of
the Nb-free alloy without
plasticity under tension. In addition, the Young’s modulus and
hardness of B2-CuZr phase in 3.7%
Nb-added sample are lower than those of the glassy matrix. So,
the stress concentrate on the
crystal-glassy matrix interface will be released through the
plastic deformation of the B2-CuZr
phase before the yielding of the glassy matrix [5], which
eventually leads to the remarkable plastic
deformation of the 3.7% Nb-added alloy.
Accordingly, it is also considered that the deformation-induced
martensitic transformation
of the B2-CuZr phase and its interaction with the glassy matrix
may lead to the remarkable tensile
ductility in the 3.7% Nb-added sample. Furthermore, the dramatic
melting on the fracture region
also contributes to certain tensile plasticity by releasing more
elastic energy.
5. Conclusions
Through investigating the microstructures and tensile
deformation behaviors of rapid
solidified Cu48-xZr48Al4Nbx (x=0, 1, 3, 3.7, 5 at. %) alloys,
the relationship between
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microstructures and mechanical properties at different Nb-doping
levels was characterized. The
1-5% Nb additions suppressed precipitation of the Al2Zr phase
and induced the formation of single
B2-CuZr phase in the glass matrix, which increased the fracture
strength of the Cu48Zr48Al4 alloys.
The BMGCs with uniformly distributed single B2-CuZr phase was
obtained in the 3.7% Nb
addition alloy, which exhibited larger tensile ductility and
work-hardening capability as well as the
highest fracture strength. The deformation-induced martensitic
transformation of the B2-CuZr
phase and the interaction between the glassy matrix and the
martensite particle were responsible
for the improved tensile properties. The drastic melting on the
fracture region also contributed to
the increase in tensile plasticity. The results highlight that
the high strength and large plasticity in
BMGCs could be achieved simultaneously through dominating the
interaction between the glassy
matrix and the reinforcing phase tailored by proper
alloying.
Acknowledgements
The authors gratefully acknowledge the financial support by the
Foundation of Heilongjiang
Province Natural Science (A201103), the Foundation of
Heilongjiang Province Education
(12531585), and the National Natural Science of China (51371078)
and (51201062).
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Figure captions
Fig.1 XRD patterns of the as-cast Cu48-xZr48Al4Nbx alloys with
different Nb additions
Fig.2 DSC traces of the as-cast Cu48-xZr48Al4Nbx alloys with
different Nb additions
Fig.3 Optical metallographs of the cross-sections
microstructures of the as-cast Cu48-xZr48Al4Nbx
alloys with different Nb additions, (a)x=0, (b) x=1, (c) x=3.7,
and (d) x=5
Fig.4 Tensile true stress-strain curves of the as-cast
Cu48-xZr48Al4Nbx alloys with different Nb
additions
Fig.5 HRTEM image of the B2 nanocrystal embedded in the
Cu44.3Zr48Al4Nb3.7 alloy
Fig.6 SEM images of the tensile fracture surface and its lateral
surface of the as-cast
Cu48-xZr48Al4Nbx alloys with different Nb additions (a) (b)x=0,
(c) x=5, (d) (e)and (f) x=3.7
Fig.7 MAXRD patterns of the 3.7% Nb-added sample fracture
surface
Fig.8 Load-displacement curves during Nanoindentation of the
Nb-free and 3.7% Nb-added
samples at different positions
20 30 40 50 60 70 80
Al2Zr
CuZrCu48-xZr48Al4Nbx
x=5x=3.7x=3
x=1x=0 Intensity(a.u.) 2θ(deg.)
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Table caption
Tab.1 Young’s modulus E and hardness H obtained from
nanoindentation of the Nb-free and 3.7%
Nb-added samples
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Fig.1
20 30 40 50 60 70 80
▲● ▲
●
●
●
●●
●●
Al2Zr ▲
▲ ▲
B2-CuZrCu
48-xZr
48Al
4Nb
x
x=5
x=3.7
x=3
x=1
x=0
Inte
nsi
ty (
a.
u.)
2θ (degree)
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Fig.2
600 700 800
Cu48-x
Zr48
Al4Nb
x
Tx
Tg
x=5
x=3.7
x=3
x=1
x=0
Ex
oth
erm
ic h
eat(
a.u
.)
Temperature(K)
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Fig.3
200um
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Fig.4
0
200
400
600
800
1000
1200
1400
1600
1800
2000
Cu48-x
Zr48
Al4Nb
x
1%
x=5x=3.7x=3x=1x=0
str
ess(M
Pa
)
strain(%)
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Fig.5
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Fig.6
(e)
35o
50o
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Fig.7
20 30 40 50 60 70 80
▲
II
I
▲
●B19
,-CuZr
B2-CuZr
▲
▲
●
●●
●
In
ten
sity
(a.
u.)
2θ (degree)
2.0mm ΙΙ Ι
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Fig.8
2000
4000
6000
8000
10000edcba
a Cu48
Zr48
Al4 Al
2Zr
b Cu44.3
Zr48
Al4Nb
3.7 amorphous
c Cu48
Zr48
Al4 amorphous
d Cu48
Zr48
Al4 B2
e Cu44.3
Zr48
Al4Nb
3.7 B2
Lo
ad
(u
N)
Displacement(nm)
150nm
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Tab.1
Position )(GPaE )(GPaH
Nb0 Nb3.7 Nb0 Nb3.7
B2 80.1±1.6 86.6±4.4 5.04±0.44 3.7±0.4
Al2Zr 92.4±2.6 7.76±0.34
Amorphous 83.4±4 109.0±1.0 6.08±0.28 6.1±0.3
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Graphical abstract
20 30 40 50 60 70 80
▲
II
I
▲
●B19
,-CuZr
B2-CuZr
▲
▲
●
●●
●
Inte
nsi
ty (
a.
u.)
2θ (degree)
2.0mm ΙΙ Ι
0
200
400
600
800
1000
1200
1400
1600
1800
2000
Cu48-x
Zr48
Al4Nb
x
1%
x=5x=3.7x=3x=1x=0
str
ess(M
Pa)
strain(%)
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Highlights
A metallic glass composite was found to exhibit high tensile
plasticity and work
hardening
The addition of Nb led to a uniform distribution of B2-CuZr
phase in the glassy matrix
The enhanced plasticity was attributed to the martensitic
transformation of B2-CuZr
phase
The interaction between martensite particle and glassy matrix
further enhanced
plasticity