# Size Effects: The Relation to the Percentage of Atoms That Participate in the Deformation of ZrCu Metallic Glass

Authors: L. K. Gao; F. L. Zhao; N. Xu; L. Qi; R. P. Liu
Journal: Journal of Spectroscopy
 (2014)

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## Abstract

Molecular dynamics simulations indicate that with the model diameter gradually decreasing the deformation mode of ZrCu metallic glass evolves from highly localized shear band formation to homogeneous deformation with obvious transition inD
=
7
–
9 nm. Through the statistic of atoms that sustain shear strain larger than 8% in the models with 8% strain along z-direction, we found that the main reason for the uniform deformation that occurs in the smallest size model is that there are 61% atoms involved in the deformation, which significantly decrease the strain assigned to individual atoms, avoiding large atomic rearrangement and making those atoms evenly distributed in the model matrix.


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## Body

## 1. Introduction

Metallic glasses (MGs) are a relatively new materials that have many excellent properties, such as high strength, high elastic limit, and high corrosion resistance [1]. But they almost have no plasticity under low temperature loads; this is mainly due to the highly spontaneous localization within a narrow shear band during the plastic deformation process, which rapidly expands along the shear plane and disables the material instantaneously [2]; this defect seriously affects the MGs as the application of engineering material. So how to improve the plasticity of MGs under low temperature loads became the focus of study. Similar to the crystalline alloy, reducing the size of the amorphous alloy is a kind of possible way to improve the plasticity [3, 4], but there are many controversies about size effects on amorphous alloy. (i) The preparation of micron or nanometer MGs usually uses focused ion beam (FIB) in experiments, the high-energy ion beam would damage the surface [5–7] and the fabricated sample generally exists 1°-2° deviation and forms a cone, and the cone sample inevitably induces complex stress states and deformation localization on the end of the sample [8]. (ii) With the decrease of the sample size, the change of deformation behavior is gradual or abrupt due to the difficulty to preparation of nanoscale sample, making the problem hard to get a system discussion and proof in experiment. So the size effects on the deformation behavior and deformation mechanism of MGs has always been a continuous explore problem.In this paper, we systematically study the size effects on the deformation behavior of the nanoscale MGs using molecular dynamics simulation. Molecular dynamics simulation can prepare perfect nanoscale cylindrical model, and the preparation process would not damage the surface state, so we can cleverly avoid some experiment shortages and play a supplement and guiding role in experimental study.


## 2. Model and Method

In our MD simulation, we studied the deformation behavior and the deformation mechanism of ZrCu metallic glass (MG) with different size models. ZrCu amorphous alloy is a binary alloy [9], since the binary alloys easier to model and analyse than the multielement alloys, it makes ZrCu an attractive MG to study theoretically. The simulations are carried out using the embedded atom method (EAM) potential, supplied in LAMMPS [10]. A small box of 10000 random configuration atoms with 3D periodic boundary conditions (PBCs) is first equilibrated at 2600 K for 50 ps, and then we cool the system from 2600 K down to 50 K in 50 K decrements at a constant quenching rate of 2 K/ps to the glass state (50 K), at zero external pressure as shown in Figure 1. Figure 1(a) is the RDF of the simulation model which indicates the amorphous structure. Figure 1(b) shows a typical bright-field TEM image of ZrCu alloy and its corresponding selected-area electron diffraction (SAED) pattern. It can be seen that a uniform image without any contrast and sharp electron diffraction rings were observed, indicating a typical amorphous structure. To get large samples, we replicate the 10000 atom configuration, which then annealed for 500 ps at 800 K to remove the increased surface energy and then relaxation under 50 K for 500 ps. By deleting the redundant atoms from cube configuration we get a series of diameters (D) from 3.6 nm to 20 nm amorphous cylindrical model with aspect ratio of 2 : 1. A constant strain rate of 1 × 108 s−1 along z-direction is used at low temperature of 50 K by moving the rigid atoms at one end along the z axis, while keeping the rigid atoms at the other end unchanged.(a) The amorphous alloy model and (b) TEM photo of the ZrCu alloy.
(a)
(b)


## 3. Results and Discussion

Figure2 shows the relationship of the tensile strength and the reciprocal of diameter for different size models. We find that with the decrease of the model size the corresponding tensile strength increased significantly, and the smaller the model size the more significant increase of the tensile strength, suggesting the stronger ability to resist deformation of the model. It is worth noting that along the decreasing of model size the tensile strength is increased gradually.Figure 2
Tensile strength change curve with the decrease of the model size.Figure3 shows the typical stress-strain curves, from which we observe that in the smallest size model the stress-strain curve shows an obvious “rise and fall” phenomenon due to the stress is sensitive to the formation and propagation of individual plastic events in the small size model. In the D
=
7
–
9 nm model the wave amplitude and the number of fluctuation decreased greatly; this is mainly because with the increase of the model size, more local strain starts at the same time during the deformation process which weakens the mutation of stress and the wave amplitude of fluctuation. In the 20 nm cylindrical model the fluctuation phenomenon disappears completely and presents a smooth stress strain curve; however when the stress reaches its maximum then accompanied by shear softening occurs a sharply decline, heralding the formation of highly localized shear band along the shear plane [11].Figure 3
The typical stress-strain curves for different size models during the tensile process.In order to further understand the distribution of shear bands and the local strain along the decrease of model size during the deformation process, we use the local strainη
i
Misses to monitor the difference of the deformation [12]. η
i
Misses is measured by referenced to the relaxed glass prior to employing uniaxial tensile deformation along z-direction. The atoms in the Figure 4 are colored by the η
i
Misses which tend to blue representing the smaller local strain value and tend to red representing larger local strain value.The distribution of local strain along the diameter: (a)D
=
20 nm, (b) D
=
9 nm, (c) D
=
7 nm, and (d) D
=
3.6 nm.
(a)
(b)
(c)
(d)From Figure4(a) we can clearly see the shear band apparent on the direction of 45° and 135° and throughout the entire model, which can lead to shear instability with the increase of following strain. While Figures 4(b) and 4(c) present obvious transition process; 9 nm model appeared stress localization on the 45° and 135° direction, but without the formation of shear band, is a kind of transition to shear transformation process. The stress localization in D
=
7 nm model is distributed scatteredly on the surface and inside with blurred direction and Figure 4(d) model only with several obvious localization on the surface, with the internal strain values almost uniformly distributed. This shows that the size has a very large effect on the deformation behavior of ZrCu MGs, with the decrease of the size, ZrCu MGs have experienced from the highly localized shear band formation to the homogeneous deformation, and the deformation process exists with obvious transition in D
=
7
–
9 nm which demonstrate that the size decreased deformation mode is a gradual process instead of abrupt.Statistic has been further performed on the individual atom along thez-direction strained 8% of the model and found that the number of atoms that is under the same shear strain accounts for different percentages of the total atoms in different models; the atoms that sustain shear strain larger than 8% in 3.6 nm model account for about 61% of the total atoms, while in 20 nm are only 37% and in 7 nm and 9 nm are about 55% and 49%, respectively. To some extent, this illustrates that in the large size model, only a small fraction of the atoms are involved in deformation, while in small size model there are more atoms participating in deformation. We define those atoms as participating deformation atoms. How those atoms are distributed in the model is of great concern. So we divided each model into 0.1 nm along the loading axis and plot the average von Mises shear strain in Figure 5 as a function of position.Statistical distribution of individual atom with shear strain > 8% ((a), (b), (c), and (d) areD
=
20 nm, 9 nm, 7 nm, and 3.6 nm model, resp.).
(a)
(b)
(c)
(d)From Figure5 we can find that the maximum shear strain of schematic atoms decreases along the decrease of model size. And in the model in Figures 5(a) and 5(b) there are about 57% and 35% atoms, respectively, gathered in tensile end and sustained larger shear strain, which is a kind of unstable distribution state. While in the model in Figures 5(c) and 5(d) those atoms are basically evenly distributed in the matrix model, sharing the strain caused by the plastic deformation, making the model a high tensile strength and plastic deformation ability.Rearrangement would take place when local atomic strain beyond a certain critical threshold [13–15], which exhibits a strong autocatalytic behavior, is responsible for a considerable flow softening [16, 17]. That is larger local atomic strain more propensity of strain localization and the formation of shear band. In our study we find that in the smallest model there are 61% atoms that participate in deformation; thus the strain assigned to individual atom will significantly decrease, which avoids large atomic rearrangement during the deformation process, so these atoms basically diffuse in the model matrix. While there are only 37% atoms involved in the deformation of the D
=
20 nm model, the strain assigned to a single atom is greatly increased, so these atoms are more prone to restructuring. As a consequence, plastic deformation suffers a severe instability and forms the highly localized shear band. With the decrease of the model size, the fraction of atoms participating in deformation gradually increase, and this is the reason why the transition of the deformation mode is gradual instead of abrupt.


## 4. Conclusion

In summary, our MD simulations indicate that with the decrease of the model size the tensile strength of ZrCu metallic glass increases significantly and its deformation mode evolves from highly localized shear band formation to homogeneous deformation with obvious transition inD
=
7
–
9 nm. We further find that when the models strained 8% along the z-direction there are 61% atoms involved in the deformation in the smallest model and due to avoiding large atomic rearrangement those atoms evenly distributed in the matrix. While only 37% atoms participate in deformation in the D
=
20 nm model and because of an inevitable atomic rearrangement, the model exhibits a severe instability and forms the highly localized shear band.



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*Source: 627679-2014-06-15.xml*