Atomic Simulation of the Melting and Mechanical Behaviors of Silicon Nanowires

: Molecular dynamics simulations using a three-body potential show that the melting and mechanical behaviors of silicon nanowires are strongly dependent on their cross-section area. For the wire with a small cross-section area, rearrangements of surface atoms greatly affect thermal stability in a relatively low temperature regime. For these wires with a relatively large area, while some surface atoms adjust their positions, most of the interior atoms hold their tetrahedra packing patterns. At a high temperature, the accumulation of structural disorder can quickly extend into the entire wire, which resembles the melting of the bulk phase. By applying the uniaxial tensile, these silicon nanowires present the typical mechanical behavior of plastic materials. The atomic local stress in the necking region is apparently larger than that outside of the necking region. As the cross-section area becomes large, both the yield strength and tensile strength increase. With the increasing temperature, the elasticity decreases signiﬁcantly.


Introduction
Silicon nanowires (Si NWs) present distinguished properties differing from their bulk counterparts owing to their high surface/volume ratio [1]. During the last two decades, the Si NWs have been widely considered as suitable units, which can be integrated in functional devices including biosensors [2,3], thermoelectrics [4,5], transistors [6], resonators [7] and electrode materials for energy storage devices [8]. When these nanowires are used in the nano-electromechanical system (NEMS) as active components, such as nanorelays, nanoresonators, or switches (ON-OFF devices), the mechanical properties play an essential role in the reliability and manufacturability of these nano-devices under processing and working conditions. Therefore, it has become increasingly important to understand the mechanical properties of these nanowires, and many investigations have been reported on mechanical behaviors, including the elasticity [9][10][11], anelasticity [12], plasticity [13,14] and strength [15] of these components.
Upon heating these nanowires, the transition information of structures or mechanical properties is provided in terms of changes in atomic packing, as well as atomic level stress. The tensile test is an effective approach to probing the mechanical properties of materials. Over the past decades, a large number of experimental studies have investigated the mechanical properties of silicon nanowires via tensile tests [16][17][18]. However, unlike the mechanical testing of bulk materials, the testing of NWs heavily depends on the experimental setup, and so there are significant challenges during manipulating, which makes accurately applying and measuring the external force of strains at the nano-scale extremely difficult. In addition, there are discrepancies between observations during the experimental process, especially in regard to the plastic behaviors of nanowires. Therefore, computational approaches can be used to calculate the mechanical properties of reasonably sized NWs [19][20][21]. Among these mechanical properties, Young's modulus has been measured to study the size and temperature effect on the structures of the nanowires by utilizing many experimental approaches based on the Atomic Force Microscope (AFM), Electron Microscope (EM) or Optical Microscope (OM) [22][23][24]. Moreover, theoretical modeling suggests that the Young's modulus of the Si NWs decreases when the diameter and temperature decreases [25][26][27].
Previous reports were concentrated on the Si NWs with different sizes. For instance, the molecular-doped Si NWs, which are integrated in solar cells, have diameters of up to 70 nm [28]. The Si NWs as a sensing nanomaterial have dimensions in the range of ≈1-100 nm, hence making them very comparable to and compatible with the dimensional scale of biological and chemical species [29]. Wang et al. covered the processing of Si NWsbased field-effect transistors (FETs), ranging from 10 to 20 nm wide [30]. In addition, doping provides an optimal performance of NWs. Keeping the size of the nanowire unchanged, by doping the nanowire with a controllable dopant distribution, the obtained doped nanowire can be tuned to have the characteristics of electrons in the laboratory. When comparing the local stress distribution of pure nanowires, the doped nanowires have local stress changes at the doped sites, which is critical for a device design with a reproducible electronic performance at the nanoscale [31]. However, as requirements increase significantly for the miniaturization and portability of devices, it becomes essential to investigate high-quality Si NWs with smaller-diameter cross sections. Such knowledge also helps us to improve our understanding of the relationship between the structure and properties of nano-objects with high surface/volume ratios. Therefore, a number of both theoretical and experimental investigations have been stimulated naturally to predict the structures and properties of smaller silicon nanowires. Yet, many reports on small-sized nanowires tend to examine the geometric structure and electronic properties of the Si NWs through first-principle calculations [26,32], which are a prohibited computational expense. At the nanoscale, as the number of atoms in a system increases, there is an exponential increase in computational cost, as well as an increase in data complexity. Computer simulations based on empirical potentials, such as molecular dynamics (MD), are particularly well-suited to characterizing microscopic details in these systems, involving the combined behaviors of atom movements and locally structural rearrangements, as well as stress changes at the atomic scale.
The present work is focused on changes in the packing configurations and mechanical behaviors of [001]-oriented nanowires with diameters of 0.693 nm, 0.859 nm and 1.034 nm, by using atomic simulations under the tension of the heating process. The effects of crosssection area and temperature on thermal stability and mechanical behaviors were mainly observed through the analysis of energy; atomic level stress; pair distribution function; and the relationship between moduli, stress and strain, as well as atomic packing images.

Simulation Approach
The interactions among the atoms are described by the Stilinger-Weber (SW) potential [33,34]. This potential has been widely used to predict the molecular structure and the mechanical properties of silicon nanomaterials. The total potential energy of an N-atom system takes the following form: where φ ij and ϕ ijk represent the potential energy of two bodies and three bodies, respectively, which can be calculated by the following form: where ε and σ are the dimensional parameters of energy and length, and f 2 and f 3 are functions of two-body and three-body potentials related to distance, respectively: and the angle-related function is: where θ jik is the angle between the r i and r k subtended vertex i, etc. The values of σ, ε, A, B, λ, Γ, p, q and a are adjustment parameters. The value of a is chosen so that the potential is truncated between the first-nearest-neighbor and the second-nearest-neighbor distances. These parameters in the empirical potential are obtained by using the experimental and quantum mechanics calculations, as listed in Table 1. Initially, we built three Si NWs with different diameters in circle cross-sections, which were labeled as SiNW1, SiNW2 and SiNW3, respectively. The orientation and the cross-section of these silicon nanowires are depicted in Figure 1   To observe and analyze the atomic packing structures of these Si NWs, the pair distribution function g(r) provides the probability of finding the atom pairs within a distance r in the system: where n is the number of atoms of the nanowires in simulation, and 〈〉 denotes the average value for the statistical time step. Figure 2 shows the g(r) curves of these constructed initial structures. As shown in this To observe and analyze the atomic packing structures of these Si NWs, the pair distribution function g(r) provides the probability of finding the atom pairs within a distance r in the system: where n is the number of atoms of the nanowires in simulation, and denotes the average value for the statistical time step. Figure 2 shows the g(r) curves of these constructed initial structures. As shown in this figure, the first peak is at 0.2370 nm, corresponding to the position of the first neighboring atom in the crystals, which is also the bond length of the crystalline silicon. The positions of the other peaks correspond to the second, third, and fourth neighbors in these nanowires, respectively. The differences in peak heights indicate that the number of paired atoms is different at this distance between a pair of atoms. The high peak indicates the large number of the paired atoms, and the low peaks represent the small numbers. The g(r) curves in this figure suggest the same packing patterns of the atoms in these initial nanowires [32]. The simulations, which employed the General Utility Lattice Program (GULP) software package [35], were performed by starting with the optimal structure at 300 K, then gradually increasing the temperature to 1600 K at an increment of 50 K in the NVT ensemble [36], where an Andersen thermostat was used to control temperature. By solving Newton's motion equations, we could obtain the positions and velocities of each atom, and a predictor-corrector algorithm was used to integrate equations of motion. At each temperature, the runs took 60,000 time steps, and the last 30,000 time steps recorded the atomic trajectories and energy, that is, they were used to calculate the statistical average values for these nanowires. Throughout simulations, a time step of 1 fs was used.
The potential energy per atom at each temperature is defined below: 1 (8) where N is the number of atoms in the system. As given in Equation (1), both the two-body potential energy and three-body potential energy contributes to the total potential energy of the simulated system. If the structures of the atomic packing change, the distance and angles among the atoms change accordingly, resulting in changes to the two-or three-body potential energies. Figure 3 shows a similar behavior regarding the changes of the potential energy for these nanowires at room temperature. Initially, the energy has very high values. The reason for this phenomenon is that the atoms in an original structure are packed into the same structure The simulations, which employed the General Utility Lattice Program (GULP) software package [35], were performed by starting with the optimal structure at 300 K, then gradually increasing the temperature to 1600 K at an increment of 50 K in the NVT ensemble [36], where an Andersen thermostat was used to control temperature. By solving Newton's motion equations, we could obtain the positions and velocities of each atom, and a predictor-corrector algorithm was used to integrate equations of motion. At each temperature, the runs took 60,000 time steps, and the last 30,000 time steps recorded the atomic trajectories and energy, that is, they were used to calculate the statistical average values for these nanowires. Throughout simulations, a time step of 1 fs was used.
The potential energy E av per atom at each temperature is defined below: where N is the number of atoms in the system. As given in Equation (1), both the two-body potential energy and three-body potential energy contributes to the total potential energy of the simulated system. If the structures of the atomic packing change, the distance and angles among the atoms change accordingly, resulting in changes to the two-or three-body potential energies. Figure 3 shows a similar behavior regarding the changes of the potential energy for these nanowires at room temper-ature. Initially, the energy has very high values. The reason for this phenomenon is that the atoms in an original structure are packed into the same structure as in the bulk crystalline, possessing a high energy. However, because the surface atoms of nanowires are less bound by their surrounding atoms than these in the interior, they only need a small amount of energy to rearrange their packing patterns. Then, in rows of buckled dimers observed on the surfaces of Si NWs, the energy drops abruptly, and enters into the oscillating regime, implying that the nanowire is in equilibrium. Table 2 lists the surface/volume ratio for each simulated nanowire, which is calculated from the atom number in the surface divided by the total number of atoms in one nanowire. As the diameters of the cross-sections for these nanowires increase, the ratio of surface/volume decreases. Therefore, the SiNW1 with the smallest diameter has the highest value because of a high proportion of atoms in the surface, and the energy decreases as the diameter increases.  In applying the strain for the nanowires, the cell length along the [001] axial direction of the nanowires, increases by 1% of the initial length at every 1 ps, corresponding to a strain rate of 1 × 10 10 s −1 .
The local stress tensors of each atom i is given in the following equation: where is the volume of atoms, is the energy of the i th atom, and and are the Cartesian components of the vector in which a and b stand for x, y, and z. Furthermore, the isotropic atomic pressure is related to the as given by the following form: The elastic properties of materials can be represented by Young's modulus. The modulus is derived from the slope in the elastic stage of a stress-strain curve.

Results and Discussion
Changes of potential energy indicate changes in the packing structure in the simu-   In applying the strain for the nanowires, the cell length along the [001] axial direction of the nanowires, increases by 1% of the initial length at every 1 ps, corresponding to a strain rate of 1 × 10 10 s −1 .
The local stress tensors σ i of each atom i is given in the following equation: where V i is the volume of atoms, E i is the energy of the i th atom, and r ij a and r ij b are the Cartesian components of the vector r ij in which a and b stand for x, y, and z. Furthermore, the isotropic atomic pressure P i is related to the σ i as given by the following form: The elastic properties of materials can be represented by Young's modulus. The modulus is derived from the slope in the elastic stage of a stress-strain curve.

Results and Discussion
Changes of potential energy indicate changes in the packing structure in the simulated systems. A difference value of atomic potential energy is introduced in the present work, which is defined as the value obtained from the difference between the energy of two adjacent temperatures divided by the temperature difference. Figure 4 shows the variation of the difference value in the temperatures for these three nanowires upon heating. As shown in this figure, the Si NWs with smaller diameters (SiNW1) possess the most apparent oscillation changes compared with other nanowires at lower temperatures, implying apparent changes in the atomic packing of this wire. At higher temperatures, there is a sharp increase in the energy difference, specifically at temperatures of 1200 K, 1300 K, and 1500 K, and the abrupt change at the highest temperature for the SiNW3 indicates the need to absorb the most heat. For the SiNW1, a large proportion of the atoms occupy surface positions, which present movements with only a small amount of energy. Therefore, the position adjustments of these surface atoms significantly affect the changes in the energy differences, as shown in Figure 4. In a temperature regime from 650 K to 850 K, the difference value enters into a plateau, implying that the atoms hold their packing patterns formed at 650 K. As the temperature increases, the different values change in an oscillating mode, and then in the temperature range from 1100 K to 1200 K, increases significantly, suggesting that the atomic packing becomes disordered. For the SiNW2, until 600 K, most of the atoms hold their packing patterns. Then, the oscillating changes imply that some atoms continuously adjust their positions as the temperature increases. At high temperatures, the oscillating amplitude increases. At 1300 K, the jump peak suggests that the atoms pack disorderly after absorbing enough heat. In the case of SiNW3, most atoms hold their packing patterns until 1200 K. Then, a certain number of the atoms begin to change their positions, and at 1500 K, the wire melts. It can also be seen from the Figure 4, the bulk_Si hold their packing patterns in the range from 300 K to 1600 K. is a sharp increase in the energy difference, specifically at temperatures of 1200 K, 1300 K, and 1500 K, and the abrupt change at the highest temperature for the SiNW3 indicates the need to absorb the most heat. For the SiNW1, a large proportion of the atoms occupy surface positions, which present movements with only a small amount of energy. Therefore, the position adjustments of these surface atoms significantly affect the changes in the energy differences, as shown in Figure 4. In a temperature regime from 650 K to 850 K, the difference value enters into a plateau, implying that the atoms hold their packing patterns formed at 650 K. As the temperature increases, the different values change in an oscillating mode, and then in the temperature range from 1100 K to 1200 K, increases significantly, suggesting that the atomic packing becomes disordered. For the SiNW2, until 600 K, most of the atoms hold their packing patterns. Then, the oscillating changes imply that some atoms continuously adjust their positions as the temperature increases. At high temperatures, the oscillating amplitude increases. At 1300 K, the jump peak suggests that the atoms pack disorderly after absorbing enough heat. In the case of SiNW3, most atoms hold their packing patterns until 1200 K. Then, a certain number of the atoms begin to change their positions, and at 1500 K, the wire melts. It can also be seen from the Figure 4, the bulk_Si hold their packing patterns in the range from 300 K to 1600 K.  As shown in Figure 5, the g(r) has a characteristic of discrete peaks with a certain width, resulting from the thermal movement of atoms around their equilibrium position. It should be noted that the highest position of the first peak of the distribution function of the wires with different sizes at different temperatures, is about 0.235 nm, corresponding to the bond length between atoms in the silicon tetrahedra. Compared with the g(r) of the initial structures, peak width occurs because of the intensified thermal motion of the silicon nanowires in these atoms. When the distances between the atoms exceed the limited distance, the packing patterns change, resulting in the differences of these peak positions. Meanwhile, since the coordination number of surface atoms is lower than that of internal atoms, nearly all rearrangement occurs in the surface atoms in relatively low temperature regimes. As the temperature is in the high-temperature regimes, some distinct peaks of the nanowires disappear, indicating that the transition from the ordered structure to the disordered structure occurs. As shown in Figure 5, the g(r) has a characteristic of discrete peaks with a certain width, resulting from the thermal movement of atoms around their equilibrium position. It should be noted that the highest position of the first peak of the distribution function of the wires with different sizes at different temperatures, is about 0.235 nm, corresponding to the bond length between atoms in the silicon tetrahedra. Compared with the g(r) of the initial structures, peak width occurs because of the intensified thermal motion of the silicon nanowires in these atoms. When the distances between the atoms exceed the limited distance, the packing patterns change, resulting in the differences of these peak positions. Meanwhile, since the coordination number of surface atoms is lower than that of internal atoms, nearly all rearrangement occurs in the surface atoms in relatively low temperature regimes. As the temperature is in the high-temperature regimes, some distinct peaks of the nanowires disappear, indicating that the transition from the ordered structure to the disordered structure occurs.  Figure 6 shows the packing patterns of the three nanowires at different temperatures. At relatively low temperatures, a general scene is that only a few of surface atoms adjust their positions, and most of the atoms in these three nanowires can hold their packing patterns in large temperature ranges. As the temperature increases, more surface atoms change their positions, which results in the views of these three nanowires from the axis direction getting closer to a circle, whereas most of the interior atoms are in the lattice positions. As shown by the images of the lateral section along the [001] direction, as the temperature increases, some surface atoms rearrange their packing patterns. For SiNW1, a certain number of red surface atoms are in a suspended state at 350 K, whereas at 400 K, these suspended atoms form dimers, resulting in the release of energy as illustrated by the apparent decrease in Figure 3. With the increase in temperature from 500 K to 550 K, some dimers formed on the surface are broken, resulting in an increase in energy. Similarly, apparent surface reconstruction can be observed in SiNW2 and SiNW3 in the relatively high temperature regimes, whereas most atoms hold their packing patterns until melting at 1300 K and 1500 K.  Figure ?? shows the packing patterns of the three nanowires at different temperatures. At relatively low temperatures, a general scene is that only a few of surface atoms adjust their positions, and most of the atoms in these three nanowires can hold their packing patterns in large temperature ranges. As the temperature increases, more surface atoms change their positions, which results in the views of these three nanowires from the axis direction getting closer to a circle, whereas most of the interior atoms are in the lattice positions. As shown by the images of the lateral section along the [001] direction, as the temperature increases, some surface atoms rearrange their packing patterns. For SiNW1, a certain number of red surface atoms are in a suspended state at 350 K, whereas at 400 K, these suspended atoms form dimers, resulting in the release of energy as illustrated by the apparent decrease in Figure 3. With the increase in temperature from 500 K to 550 K, some dimers formed on the surface are broken, resulting in an increase in energy. Similarly, apparent surface reconstruction can be observed in SiNW2 and SiNW3 in the relatively high temperature regimes, whereas most atoms hold their packing patterns until melting at 1300 K and 1500 K.  Figure 7 shows the stress-strain curves of these nanowires subjected to uniaxial tensile loading at room temperature. As shown in this figure, nanowires start with a linear relation between stress and small strain, indicating that the nanowires undergo elastic deformation, where the stress-strain relation follows Hook's law. The slope of the stressstrain curve near zero strain provides Young's modulus. As the strain increases with a nonlinear trend, the stress begins to decrease, suggesting that the nanowires enter into plastic deformation. Until the strain reaches 0.11, 0.11 or 0.12, the nanowire begins to yield, and the yield stress (σs) is 1.5721, 3.4126 or 3.8959 GPa. Correspondingly, the packing images show that some of the surface atoms begin to separate, and some interior atoms leave their origin lattice positions. When the strain reaches 0.135, 0.135 or 0.15, the stress of these nanowires reaches a maximum (σb) 1.74296, 3.77758 or 4.11558 GPa; when the stress reaches the tensile strength, the plastic deformation stage is terminated. Then, there is an abrupt decrease in stress. The atomic packing images show that a necking phenomenon occurs in these wires. As shown in Figure 8, these three nanowires appear more light green to yellow for the atoms in the necking area than those outside of the area. These suggest that the pressure values in the necking area are mostly positive and the magnitude is higher than that of other regions of the atoms, which means most of these atoms are subjected to the compression due to the disordered atomic packing. For SiNW1, the atoms in the part outside of the necking area are blue to dark blue. For the atoms outside of the necking areas of SiNW2 and SiNW3, light green to light blue occurs, and even yellow is observed in the SiNW3. Therefore, these atoms in the remaining part of SiNW1 are in a  Figure 7 shows the stress-strain curves of these nanowires subjected to uniaxial tensile loading at room temperature. As shown in this figure, nanowires start with a linear relation between stress and small strain, indicating that the nanowires undergo elastic deformation, where the stress-strain relation follows Hook's law. The slope of the stress-strain curve near zero strain provides Young's modulus. As the strain increases with a nonlinear trend, the stress begins to decrease, suggesting that the nanowires enter into plastic deformation. Until the strain reaches 0.11, 0.11 or 0.12, the nanowire begins to yield, and the yield stress (σ s ) is 1.5721, 3.4126 or 3.8959 GPa. Correspondingly, the packing images show that some of the surface atoms begin to separate, and some interior atoms leave their origin lattice positions. When the strain reaches 0.135, 0.135 or 0.15, the stress of these nanowires reaches a maximum (σ b ) 1.74296, 3.77758 or 4.11558 GPa; when the stress reaches the tensile strength, the plastic deformation stage is terminated. Then, there is an abrupt decrease in stress. The atomic packing images show that a necking phenomenon occurs in these wires. As shown in Figure 8, these three nanowires appear more light green to yellow for the atoms in the necking area than those outside of the area. These suggest that the pressure values in the necking area are mostly positive and the magnitude is higher than that of other regions of the atoms, which means most of these atoms are subjected to the compression due to the disordered atomic packing. For SiNW1, the atoms in the part outside of the necking area are blue to dark blue. For the atoms outside of the necking areas of SiNW2 and SiNW3, light green to light blue occurs, and even yellow is observed in the SiNW3. Therefore, these atoms in the remaining part of SiNW1 are in a stretched state, whereas a certain number of atoms in the remaining part of SiNW2 and SiNW3 are slightly compressed. stretched state, whereas a certain number of atoms in the remaining part of SiNW2 and SiNW3 are slightly compressed.  As illustrated, the Young's modulus of the nanowires vary with the temperature in Figure 9; all of the nanowires tend to decrease with the increase in temperature. Due to the rearrangements of the surface atoms at different temperatures, the atomic motions and packing structures greatly affect the elasticity for these nanowires. Here, the modulus of the nanowire with a large cross-section area has a larger value than the small area. To observe the elasticity converge toward the bulk material, we further increased the diameters of the nanowires. The diameters were 1.629 nm, 2.429 nm, 3.259 nm, and 3.541 nm, which were labeled SiNW4, SiNW5, SiNW6 and SiNW7. Then, the nanowires were also subjected to a tensile test to calculate the Young's modulus. It can be seen from Figure 9 that when the diameter of the nanowire reaches 3.541 nm, the Young's modulus still increases until it is close to the value of the bulk of Young's modulus, which is close to the value in about 109 GPa [23]. As illustrated, the Young's modulus of the nanowires vary with the temperature in Figure 9; all of the nanowires tend to decrease with the increase in temperature. Due to the rearrangements of the surface atoms at different temperatures, the atomic motions and packing structures greatly affect the elasticity for these nanowires. Here, the modulus of the nanowire with a large cross-section area has a larger value than the small area. To observe the elasticity converge toward the bulk material, we further increased the diameters of the nanowires. The diameters were 1.629 nm, 2.429 nm, 3.259 nm, and 3.541 nm, which were labeled SiNW4, SiNW5, SiNW6 and SiNW7. Then, the nanowires were also subjected to a tensile test to calculate the Young's modulus. It can be seen from Figure 9 that when the diameter of the nanowire reaches 3.541 nm, the Young's modulus still increases until it is close to the value of the bulk of Young's modulus, which is close to the value in about 109 GPa [23]. Crystals 2021, 11, x FOR PEER REVIEW 13 of 15 Figure 9. Young's modulus of Si NWs with different diameters and bulk Si varying from 300 K to 1000 K.

Conclusions
In this paper, we investigated the structural and mechanical properties of the singlecrystalline silicon nanowires by using MD simulations with SW potential. The descriptions of our simulated systems performed by molecular dynamics were related to the temperature and tensile strength. These observations found that the packing changes come from the movements and rearrangements of surface atoms in a large temperature range. The wire diameter greatly affects the melting and tensile behaviors of these nanowires. For the wires with small cross-section area, continuous position adjustments ran through the heating range, whereas the wires with a large area presented a similar melting with to the bulk at a high temperature. The packing of surface atoms affected the melting and mechanical behaviors of those nanowires, especially for the wires with a small cross-section area. By performing uniaxial tensile simulations, the Si nanowires presented a mechanical behavior of significant plasticity including elastic deformation, yield, strain strengthening, and necking. For these nanowires, the atomic local stress in the necking area presented significant differences from those in the part outside of this area. The Young's modulus was temperature-dependent and size-dependent; as the temperature increased, the nanowires become soft.

Si NW1
Si NW2 Si NW3 Si NW4 Si NW5 Si NW6 Si NW7 Bulk_Si Figure 9. Young's modulus of Si NWs with different diameters and bulk Si varying from 300 K to 1000 K.

Conclusions
In this paper, we investigated the structural and mechanical properties of the singlecrystalline silicon nanowires by using MD simulations with SW potential. The descriptions of our simulated systems performed by molecular dynamics were related to the temperature and tensile strength. These observations found that the packing changes come from the movements and rearrangements of surface atoms in a large temperature range. The wire diameter greatly affects the melting and tensile behaviors of these nanowires. For the wires with small cross-section area, continuous position adjustments ran through the heating range, whereas the wires with a large area presented a similar melting with to the bulk at a high temperature. The packing of surface atoms affected the melting and mechanical behaviors of those nanowires, especially for the wires with a small cross-section area. By performing uniaxial tensile simulations, the Si nanowires presented a mechanical behavior of significant plasticity including elastic deformation, yield, strain strengthening, and necking. For these nanowires, the atomic local stress in the necking area presented significant differences from those in the part outside of this area. The Young's modulus was temperature-dependent and size-dependent; as the temperature increased, the nanowires become soft.