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As is well known, iron plays an important role in the fields of national defense and industry, so it is of great significance to study its behavior under dynamic high pressure. As one of the most common defects in metals in nature, grain boundaries have an important influence on the mechanical properties and deformation of materials under shock. This work intends to use large-scale non-equilibrium molecular dynamics simulation to study the influence of iron anisotropy on the phase transition in bicrystal under shock loading. By tracking the local structure, shear stress distribution and morphology characteristics after shock on both sides of the grain boundaries, the factors affecting the response on both sides of the grain boundary are analyzed. Our research result shows that shocking along the non-centrosymmetric grain direction can cause significant differences in the phase transition threshold, path and mode on both sides of the symmetric grain boundary. Especially, the different phase transition dynamic processes on both sides of the sigma11 grain boundary are discussed in detail in this work, which have been rarely discussed in previous studies. Considering the symmetry of the microstructure on both sides of this type of grain boundary, the result of asymmetric shock response is different from people’s inertial cognition. Finally, it is found that the atoms in both models will shift along the direction perpendicular to the shocked direction under shock, indicating that the shock wave generated by the piston method should no longer be simply regarded as one-dimensional when shocked along the non centrosymmetric crystal direction, and the displacement of atoms along the direction perpendicular to the shocked direction is closely related to the symmetry of the crystal, which causes significant differences in shear stress on both sides of the grain boundary and ultimately affects the shock response. This study reveals that the anisotropy of lattice has an important effect on the phase transition on both sides of grain boundaries under shock loading, which can provide theoretical support for the experimental studies of polycrystalline metals and alloys under shock.
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Keywords:
- non equilibrium molecular dynamics /
- phase transition /
- grain boundary
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图 1 模型示意图 (a) 包含sigma5晶界的模型1; (b) 包含sigma11晶界的模型2
Figure 1. Model schematic figures: (a) Model 1 containing sigma5 grain boundaries; (b) model 2 containing sigma11 grain boundaries.
图 2 冲击加载下含sigma5晶界的模型1在24 ps时刻的(a)微观结构图, 红色表示HCP结构的原子, 蓝色表示BCC结构的原子, 绿色表示FCC结构的原子, 白色代表无序原子, 晶界的位置可以通过观察白色原子的位置得到; (b)剪切应力分布图; (c) 温度分布图
Figure 2. (a) Microstructure figures of the model 1 containing sigma5 grain boundaries under shock loading at 24 ps, where red represents HCP structure atoms, blue represents BCC structure atoms, green represents FCC structure atoms, and white represents disordered atoms, the position of the grain boundaries can be obtained by observing the position of white atoms. (b) The shear stress distribution; (c) the temperature distribution.
图 3 冲击加载下含sigma11晶界的模型2在20 ps时刻的(a) 微观结构图, 颜色标示同图2(a); (b) 剪切应力分布图; (c) 温度分布图
Figure 3. (a) Microstructure of the model 2 containing a sigma11 grain boundary under shock loading at 20 ps, and the color marking is the same as that of Figure 2(a); (b) the shear stress distribution of the model 2; (c) the temperature distribution of the model 2.
图 4 BCC-HCP相变的示意图, 不同颜色的原子属于不同的层
Figure 4. Schematic diagram of BCC-HCP phase transition, where atoms of different colors belong to different layers.
图 5 模型2中sigma11晶界两侧发生相变后分别选取的一个HCP晶胞的原子形貌图 (a) 左侧; (b) 右侧
Figure 5. Atomic morphology of an HCP cell selected after phase transition on both sides of grain boundary in model 2: (a) On the left; (b) on the right.
图 6 展示了冲击过程中晶界两侧的晶格参数(lattice parameter)随时间的变化 (a) 对应晶界左侧; (b) 对应晶界右侧. 图中a和b已经被归一化处理了
Figure 6. Variation of lattice parameters on the (a) left and (b) right sides of grain boundaries over time during the shock process, where a and b have been scaled.
图 7 活塞速度为0.5 km/s的加载下, 模型1在12 ps时内部原子的(a)位置偏差和(b)剪切应力随时间的变化
Figure 7. Time dependent variation of (a) position deviation and (b) shear stress of atoms in model 1 under loading with a piston speed of 0.5 km/s at 12 ps.
图 8 活塞速度为0.2 km/s的加载下, 模型2在17.5 ps时原子的(a)位置偏差和(b)剪切应力随时间的变化
Figure 8. Time dependent variation of (a) position deviation and (b) shear stress of atoms in model 2 at 17.5 ps with a piston speed of 0.2 km/s.
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[1] Bancroft D, Peterson E L, Minshall S 1956 J. Appl. Phys. 27 291
Google Scholar
[2] Barker L M, Hollenbach R E 1974 J. Appl. Phys. 45 4872
Google Scholar
[3] Smith R F, Eggert J E, Bolme C A, Collins G W 2011 J. Appl. Phys. 110 123515
Google Scholar
[4] de Rességuier T, Hallouin M 1998 J. Appl. Phys. 84 1932
Google Scholar
[5] Levitas V I, Javanbakht M 2015 J. Mech. Phys. Solids 82 287
Google Scholar
[6] Javanbakht M, Levitas V I 2015 J. Mech. Phys. Solids 82 164
Google Scholar
[7] Talonen J, Hänninen H 2007 Acta Mater. 55 6108
Google Scholar
[8] Nagy E, Mertinger V, Tranta F, Sólyom J 2003 Mater. Sci. Eng. , A 378 308
Google Scholar
[9] Li N, Wang Y D, Liu W J, An Z N, Liu J P, Su R, Li J, Liaw P K 2014 Acta Mater. 64 12
Google Scholar
[10] Levitas V I, Ozsoy I B 2009 Int. J. Plast. 25 239
Google Scholar
[11] Zarechnyy O M, Levitas V I, Ma Y 2012 J. Appl. Phys. 111 023518
Google Scholar
[12] Hawreliak J A, Eldasher B, Lorenzana H, Kimminau G, Higginbotham A, Nagler B, Vinko S M, Murphy W J, Whitcher T, Wark J S 2011 Phys. Rev. B 83 144114
Google Scholar
[13] Magee C L 1970 Phase Transformations (Metals Park, Ohio: American Society for Metals
[14] Wu L, Wang K, Xiao S, Deng H, Zhu W, Hu W 2016 Comput. Mater. Sci. 122 1
Google Scholar
[15] Huang Y, Xiong Y, Li P, Li X, Xiao S, Deng H, Zhu W, Hu W 2019 Int. J. Plast. 114 215
Google Scholar
[16] 马文, 祝文军, 张亚林, 经福谦 2011 物理学报 60 066404
Google Scholar
Ma W, Zhu W J, Zhang Y L, Jing F Q 2011 Acta Phys. Sin. 60 066404
Google Scholar
[17] 张军, 陈文雄, 郑成武, 李殿中 2017 物理学报 66 070701
Google Scholar
Zhang J, Chen W X, Zheng C W, Li D Z 2017 Acta Phys. Sin. 66 070701
Google Scholar
[18] Zong H, Ding X, Lookman T, Sun J 2016 Acta Mater. 115 1
Google Scholar
[19] Gunkelmann N, Bringa E M, Kang K, Ackland G J, Ruestes C J, Urbassek H M 2012 Phys. Rev. B 86 144111
Google Scholar
[20] Gunkelmann N, Bringa E M, Urbassek H M 2015 J. Appl. Phys. 118 185902
Google Scholar
[21] Gunkelmann N, Tramontina D R, Bringa E M, Urbassek H M 2014 New J. Phys. 16 093032
Google Scholar
[22] Wang K, Xiao S, Deng H, Zhu W, Hu W 2014 Int. J. Plast. 59 180
Google Scholar
[23] Wang K, Chen J, Zhang X, Zhu W 2017 J. Appl. Phys. 122 105107
Google Scholar
[24] Wang K, Zhu W, Xiao S, Chen K, Deng H, Hu W 2015 Int. J. Plast. 71 218
Google Scholar
[25] Gunkelmann N, Bringa E M, Tramontina D R, Ruestes C J, Suggit M J, Higginbotham A, Wark J S, Urbassek H M 2014 Phys. Rev. B 89 140102
Google Scholar
[26] Zhang X, Wang K, Zhu W, Chen J, Cai M, Xiao S, Deng H, Hu W 2018 J. Appl. Phys. 123 045105
Google Scholar
[27] Zhang X, Chen J, Hu W, Zhu W, Xiao S, Deng H, Cai M 2019 J. Appl. Phys. 126 045901
Google Scholar
[28] Germann T C, Holian B L, Lomdahl P S, Ravelo R 2000 Phys. Rev. Lett. 84 5351
Google Scholar
[29] Zhakhovsky V V, Migdal K P, Inogamov N A, Anisimov S I 2015 19th Biennial American-Physical-Society (APS) Confe rence on Shock Compression of Condensed Matter (SEEM) Tampa, FL, USA, June 14–19, 2017 p070003
[30] Zong H, He P, Ding X, Ackland G J 2020 Phys. Rev. B 101 144105
Google Scholar
[31] Zhang X, Deng Y, Chen J, Hu W 2021 Mater. Today Commun. 29 1028932
Google Scholar
[32] Plimpton S 1995 Comput. Mater. Sci. 4 361
Google Scholar
[33] Stukowski A 2010 Modell. Simul. Mater. Sci. Eng. 18 015012
Google Scholar
[34] Thompson A P, Plimpton S J, Mattson W 2009 J. Chem. Phys. 131 154107
Google Scholar
[35] Luo S N, An Q, Germann T C, Han L B 2009 J. Appl. Phys. 106 253
Google Scholar
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