Lawrence Livermore National Laboratory, Livermore, California, USA.
Technische Universität Darmstadt, Darmstadt, Germany.
Nature. 2017 Oct 26;550(7677):492-495. doi: 10.1038/nature23472. Epub 2017 Sep 27.
Ordinarily, the strength and plasticity properties of a metal are defined by dislocations-line defects in the crystal lattice whose motion results in material slippage along lattice planes. Dislocation dynamics models are usually used as mesoscale proxies for true atomistic dynamics, which are computationally expensive to perform routinely. However, atomistic simulations accurately capture every possible mechanism of material response, resolving every "jiggle and wiggle" of atomic motion, whereas dislocation dynamics models do not. Here we present fully dynamic atomistic simulations of bulk single-crystal plasticity in the body-centred-cubic metal tantalum. Our goal is to quantify the conditions under which the limits of dislocation-mediated plasticity are reached and to understand what happens to the metal beyond any such limit. In our simulations, the metal is compressed at ultrahigh strain rates along its [001] crystal axis under conditions of constant pressure, temperature and strain rate. To address the complexity of crystal plasticity processes on the length scales (85-340 nm) and timescales (1 ns-1μs) that we examine, we use recently developed methods of in situ computational microscopy to recast the enormous amount of transient trajectory data generated in our simulations into a form that can be analysed by a human. Our simulations predict that, on reaching certain limiting conditions of strain, dislocations alone can no longer relieve mechanical loads; instead, another mechanism, known as deformation twinning (the sudden re-orientation of the crystal lattice), takes over as the dominant mode of dynamic response. Below this limit, the metal assumes a strain-path-independent steady state of plastic flow in which the flow stress and the dislocation density remain constant as long as the conditions of straining thereafter remain unchanged. In this distinct state, tantalum flows like a viscous fluid while retaining its crystal lattice and remaining a strong and stiff metal.
通常,金属的强度和塑性特性由位错(晶格中的线缺陷)定义,其运动导致材料沿晶格平面滑移。位错动力学模型通常用作真实原子动力学的细观代理,而原子动力学的计算成本很高。然而,原子模拟可以准确地捕捉到材料响应的每一种可能机制,解析原子运动的每一个“抖动”,而位错动力学模型则不能。在这里,我们展示了体心立方金属钽的体单晶塑性的全动态原子模拟。我们的目标是量化达到位错介导的塑性极限的条件,并了解金属在超出任何此类极限时会发生什么。在我们的模拟中,金属在恒压、恒温和应变速率条件下沿着[001]晶体轴以超高应变速率压缩。为了解决我们所研究的长度尺度(85-340nm)和时间尺度(1ns-1μs)上晶体塑性过程的复杂性,我们使用了最近开发的原位计算显微镜方法,将我们模拟中生成的大量瞬态轨迹数据转化为可以被人类分析的形式。我们的模拟预测,当达到一定的应变极限条件时,位错本身就无法再减轻机械载荷;相反,另一种机制,称为变形孪晶(晶格的突然重新取向),作为主导的动态响应模式接管。在这个极限以下,金属呈现出一种与应变路径无关的稳定的塑性流动状态,只要此后的应变条件保持不变,流动应力和位错密度就保持不变。在这种明显的状态下,钽像粘性流体一样流动,同时保持其晶格,仍然是一种坚固而坚硬的金属。