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By Grant Steven, Qing Li, Zhongpu Zhang

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2). 81 nm. 5 * 1010 s-1 to the simulation volume along the y-axis, in order to facilitate very rapid dislocation nucleation [8]. The output was visualized in time increments of 50 femtoseconds with AtomEye [15], and the centro-symmetry parameter was used to distinguish defect atoms [16]. By reviewing the images produced, the time step was determined when atomic disruption was first observed at the void, indicating the initiation of dislocation nucleation. A simulation was then carried out, in which the strain rate was reduced to 0 s-1 after this time step.

O. J. Armstrong, A mathematical representation of the multiaxial Bauschinger effect, Mater. , 24 (2007) 11-26. [8] F. J. -G. F. Rauch, G. Vincze, An alternative to kinematic hardening in classical plasticity, Int. J. , 27 (2011) 1309-1327. P. Brahme, K. K. Mishra, S. Saimoto, The backstress effect of evolving deformation boundaries in FCC polycrystals, Int. J. , 27 (2011) 1252-1266. J. Weng, Kinematic hardening rule in single-crystals, Int. J. Solids. , 15 (1979) 861-870. S. Khan, P. 1. Theoretical developments, Int.

Li, L. Shen, G. S. Moy, G. Ranzi, A crystal plasticity representative volume element model for simulating nanoindentation of aluminium alloy 2024, Proceedings of the 4th International Conference on Computational Methods, Paper ID 133, (2012) 6 pages. [24] L. Li, L. Shen, G. S. Moy, G. Ranzi, Three-dimensional crystal plasticity finite element simulation of nanoindentation on aluminium alloy 2024, Mater. Sci. Eng. A, 579 (2013) 41-49. [25] R. Quey, P. Dawson, F. Barbe, Large-scale 3D random polycrystals for the finite element method: Generation, meshing and remeshing, Comput.

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