孪生诱发塑性对V-5Cr-5Ti合金应变硬化行为的影响

钒合金(V-Cr-Ti)作为潜在重要的聚变反应堆用结构材料, 近年来受到广泛的关注. 为了研究 V-5Cr-5Ti 合金不同应变率压缩下的应变硬化行为, 特别是孪生对塑性变形的影响, 以位错密度和孪晶演化为基础, 建立了该合金的应变硬化模型. 模型中考虑了孪晶中的位错滑移对材料塑性应变的贡献. 模拟结果表明, 由于孪生诱发塑性, 从而使动态压缩时的位错密度小于准静态加载时的, 这使得 V-5Cr-5Ti 合金在动态压缩时的应变硬化率比准静态加载时的小. 当孪晶形成后, 位错滑移引起的塑性应变率随应变增大而增大, 并逐渐接近加载应变率, 而孪生引起的塑性应变率则随应变增大而减小.      

镁合金塑性机制研究综述

纯镁具有丰富的微观塑性机制，尤其是孪晶，导致其塑性变形错综复杂，力学性能也与常见的面心及体心立方金属有显著差异。由于现今学界对位错滑移与孪晶变形等塑性机制缺乏充分认识，镁合金性能调控效果尚不理想，与铝合金相比，镁合金的力学性能还有很大的提升空间。基于此背景，本文首先回顾了镁合金的发展历史与应用现状。然后介绍了镁中位错滑移与孪晶变形等塑性机制的研究进展，重点阐述位错、孪晶、晶界、析出相、溶质原子等重要的微结构，并简要介绍了计算机模拟方法。最后展望了强韧性能方面值得重视的若干研究方向。     

镁单晶变形行为的原子模拟

应用分子动力学方法模拟镁单晶在单向拉伸作用下的力学性能和微观结构演化过程.不同应变和不同温度下的模拟结果中都观测到{1011},{1012}型李晶.表明这两种孪晶是镁单晶拉伸变形的主要机制.其中{1012}型挛晶的产生伴随新晶粒生成,并且随应变增加孪晶的数量增加.此外,随着温度的增加,原子热激活效应显著.镁单晶的最大弹性形变减小,最大应力值亦变小.     

内部爆炸作用下20钢柱壳的变形及相变

研究冲击波作用下金属微观组织变化对于理解柱壳结构在高应变率下的变形及破坏极为重要。实验通过对20钢金属柱壳在内部爆炸载荷作用下的爆炸回收碎片截面进行微观分析,探讨冲击波作用下材料的组织演化、相变特征,同时使用有限元方法对柱壳膨胀断裂过程中的热力学特征进行分析。研究发现:20钢柱壳近内表面满足α→ε相变热力学条件的有限深度区域内,α晶粒内可见明显的平行滑移线分布特征;电子背散射衍射揭示了平行滑移线区域内组织碎化,且存在{112}<111>和{332}<113>两种孪晶,同时平行滑移线的碎化组织区域中存在密排六方晶格(HCP)的ε相结构,而试样原始组织及爆炸后除试样壁厚内部(0～3.0 mm)区域外均未见ε相结构残留。分析认为:冲击过程中发生了α→ε相变;相变引发的材料性能改变将可能影响断裂破坏过程;考虑冲击波作用下金属材料动态相变对结构变形与破坏的影响,对这类柱壳变形及破坏的精密物理模拟具有重要意义,有必要开展进一步研究。     

bcc-Fe刃型位错偶极子的动力学过程模拟

用分子动力学方法模拟了bcc单晶铁中滑移面为(011)晶面、柏氏矢量b-=±[100]的刃型位错偶极子吸引至湮灭的动力学过程.模拟结果显示:沿[100]晶向滑移的正刃型位错穿越Peierls势垒的方式为滑移面上方芯原子沿[111]晶向滑移,滑移面下方芯原子沿[111]晶向滑移;芯原子滑移方向分别偏转为[111]和[111]晶向,同时芯能量以格波形式释放.统计了位错运动速度和Peierls势垒随时间或两位错距离的变化.     

镁合金晶体塑性本构模型与非均匀孪生变形分析

微结构演化对镁合金材料力学性能有着显著的影响，为了揭示镁合金宏观塑性各向异性特性与非均匀孪生变形的关系，开展了不同路径下的单轴加载试验以及采用含滑移、孪生机制的晶体塑性本构模型对试验条件下的镁合金变形行为进行数值模拟研究。文中本构模型描述了滑移与孪生变形机制以及晶格转动的机制，同时研究采用三维微结构代表性有限元模型，其包含晶粒尺寸、晶向和晶界倾角等微结构参数。研究结果表明，轧制镁合金具有强烈的宏观塑性各向异性行为，并对这种镁合金塑性各向异性行为的模拟结果以及多晶织构的模拟演化结果与试验测量进行对比，结果都基本吻合。对孪生非均匀变形模拟分析表明，镁合金宏观塑性各向异性行为与滑移、孪生变形机制的不同启动组合紧密相关，同时多晶体内应力的非均匀分布受到孪生变形的严重影响。而不同晶粒尺寸的晶粒所发生的孪生变形有比较大的差异，造成孪晶变体在晶粒内的分布极不均匀。本研究可为通过微结构的合理配置来设计和控制材料的力学性能提供理论依据.     

六方金属在疲劳过程中的位错组态演化──兼论位错理论和协同论在材料强度学中的应用

简述了位错理论发展及在中国传播的历史、位错理论的应用领域、金属中常见的位错组态;介绍了协同论在位错研究中的应用,并据此分析讨论了在钛、锆等六方金属中所获得的某些实验结果。      

六方金属在疲劳过程中的位错组态演化──兼论位错理论和协同论在材料强度学中的应用

简述了位错理论发展及在中国传播的历史、位错理论的应用领域、金属中常见的位错组态；介绍了协同论在位错研究中的应用，并据此分析讨论了在钛、锆等六方金属中所获得的某些实验结果。     

镁单晶低温压缩形变机制的原子模拟

应用分子动力学方法模拟镁单晶在单向压缩作用下的力学性能和微观结构演化过程.在镁单晶低温(5K)压缩的模拟结果中可以同时观察π2面上两种弗兰克柏氏矢量的滑移,即1/6[0223]和1/6[2203].两种滑移的同时启动使得晶体在完成滑移后又恢复到完整的密排六方(hcp)晶体结构,只在滑移区的端部形成内部缺陷和表面形成滑移台阶.     

磁控溅射Ag膜磨斑微结构与耐磨机理研究

在铜基底上制备了磁控溅射银膜,采用激光共聚焦显微镜(LSCM)、透射电镜(TEM)、扫描电子显微镜(SEM)及电子背散射衍射(EBSD)等分析技术对载流摩擦试验后的磨斑微结构进行了分析. 结果表明:磨斑表面较平滑,可见犁沟、微坑及塑性流动等形貌,磨斑边缘存在堆积和剥落. 磨斑表面颗粒形态为短棒状和球状,颗粒尺寸为20~150 nm. 磨斑微结构中存在(012)和有利的(111)择优取向,晶粒平均粒度为582 nm,多数晶粒极细小,起到细晶强化作用. 在磨斑微结构中发现大量孪晶,(111)取向孪晶占比达到93.5%,这种高密度孪晶夹杂非孪晶的微结构,有利于材料内部的滑移和提高耐磨性. 在孪晶界发现存在大量{111}晶面族层错结构,有利于材料晶粒间滑移并提升宏观摩擦性能.      

Texture gradient simulations for extrusion and reversible rolling of FCC metals

A texture simulation method is described for some complex plane strain deformation paths during hot shaping of FCC metals. The method employs both finite element calculations and a polycrystal plasticity model based on the Relaxed-Constraints (RC) Taylor hypothesis and a viscoplastic constitutive law. We have considered the {111}<110> slip systems and the {100}, {110}, {112} <110> non-octahedral slip systems. The finite element codes simulate the strain paths of material flow during a shaping process. The local velocity gradients, expressed in the macroscopic reference coordinates, are rewritten in the local flow line coordinates using a kinematic analysis for steady-state flow. Secondly, for the different deformation paths, the RC polycrystal plasticity model is used to numerically simulate the local deformation texture evolutions as a function of depth. Texture simulations are carried out for two deformation processes combining hot compression and shear: extrusion and reversible rolling. For extrusion, the simulated pole figures and ODFs show the typical texture variations through the thickness of an extruded 6082 aluminium alloys, i.e. (β-fibre in the centre and a TD rotated copper component near the surface. It is shown that hot reversible rolling should develop a strong pure shear texture {001}<110> near the surface.     

Influence of deformation path on the strain hardening behavior and microstructure evolution in low SFE FCC metals

Following our recent studies of the influence of mechanical twinning on the strain hardening of low SFE FCC metals deformed by simple compression, the investigation was extended to two different deformation modes. These were plane strain compression and simple shear carried out on 70/30 brass, which exhibits only strain hardening, and on MP35N, a Co–Ni based alloy that also shows secondary hardening by deformation promoted precipitation. It was found that the magnitude of the primary strain hardening in both alloys, and the secondary hardening in MP35N, was dramatically reduced under simple shear compared to the other deformation paths. This reduced hardening in simple shear appears to be a consequence of the bulk of the deformation twins, and also the secondary hardening precipitates, forming on planes that were parallel to the primary {111} slip planes in this deformation path. These hypotheses are supported by deformation path change tests in which the shear samples that show low flow stress under continued shear, when subjected to simple compression showed a significant increase (jump) in the flow stress, reaching values that are similar to those of the alloy continuously compressed to the same equivalent strain. That is, the reduced strain hardening in shear deformation is due not to reduced twinning, but to the twins produced by shear providing only limited barriers to continued strain by simple shear. Shear banding was found to be more marked in plane strain compression than in simple compression after cold working, and particularly after the additional secondary hardening in MP35N.     

Effect of microstructure on the nucleation of deformation twins in polycrystalline high-purity magnesium: A multi-scale modeling study

A multi-scale, theoretical study of twin nucleation from grain boundaries in polycrystalline hexagonal close packed (hcp) metals is presented. A key element in the model is a probability theory for the nucleation of deformation twins based on the idea that twins originate from a statistical distribution of defects in the grain boundaries and are activated by local stresses at the grain boundaries. In this work, this theory is integrated into a crystal plasticity constitutive model in order to study the influence of these statistical effects on the microstructural evolution of the polycrystal, such as texture and twin volume fraction. Recently, a statistical analysis of exceptionally large data sets of {101?2} deformation twins was conducted for high-purity Mg (Beyerlein et al., 2010a). To demonstrate the significantly enhanced accuracy of the present model over those employing more conventional, deterministic approaches to twin activation, the model is applied to the case of {101?2} twinning in Mg to quantitatively interpret the many statistical features reported for these twins (e.g., variant selection, thickness, numbers per grain) and their relationship to crystallographic grain orientation, grain size, and grain boundary misorientation angle. Notably the model explains the weak relationship observed between crystal orientation and twin variant selection and the strong correlation found between grain size and the number of twins formed per grain. The predictions suggest that stress fluctuations generated at grain boundaries are responsible for experimentally observed dispersions in twin variant selection.     

Theoretical latent hardening in crystals—II. BCC crystals in tension and compression

The general latent hardening law of single slip derived in the first paper of this series (Havner, Baker and Vause, 1979) is applied to an analysis of “overshooting” phenomena in bcc crystals in tension and compression. This new law, which predicts anisotropic hardening of latent slip systems, is based upon the simple theory of finite distortional crystal hardening introduced by Havner and Shalaby (1977).Because of historical ambiguities regarding identification of the slip plane in bcc metals, parallel analyses are presented corresponding to two separate criteria: (i) slip on {110}, {112} and {123} crystallographic planes only; and (ii) slip on the plane of maximum resolved shear stress containing a 〈111〉 direction. It is established that the new hardening law is a theory of “overshooting” in bcc crystals according to either identification of the slip plane.A qualitative comparison between theoretical results and two experimental papers on Fe crystals is included. The general difficulties in making comparisons with the experimental literature on finite distortional latent hardening are briefly discussed.     

Detwinning of High-Purity Zirconium: <Emphasis Type="Italic">In-Situ</Emphasis> Neutron Diffraction Experiments

Twinning is an important deformation mode in hexagonal metals to accommodate deformation along the c-axis. It differs from slip in that it accommodates shear by means of crystallographic reorientation of domains within the grain. Such reorientation has been shown to be reversible (detwinning) in magnesium alloy aggregates. In this paper we perform in-situ neutron diffraction reversal experiments on high-purity Zr at room temperature and liquid nitrogen temperature, and follow the evolution of twin fraction. The experiments were motivated by previous studies done on clock-rolled Zr, subjected to deformation history changes (direction and temperature), in the quasi-static regime, for temperatures ranging from 76 K to 450 K. We demonstrate here for the first time that detwinning of { 10[`1] 2 } á 10[`1][`1] ñ\left\{ {10\overline 1 2} \right\}\left\langle {10\overline 1 \overline 1 } \right\rangle tensile twins is favored over the activation of a different twin variant in grains of high-purity polycrystalline Zr. A visco-plastic self-consistent (VPSC) model developed previously, which includes combined slip and twin deformation, was used here to simulate the reversal behavior of the material and to interpret the experimental results in terms of slip and twinning activities.     

Mechanical response and texture evolution of AZ31 alloy at large strains for different strain rates and temperatures

In order to study the behavior of material under finite deformation at various strain rates, the responses of AZ31 Mg sheet are measured under uniaxial (tension and compression) and multiaxial (simple shear) loadings along rolling direction (RD), 45° to rolling direction (DD), 90° to rolling direction (TD), and normal to the sheet (ND) to large strains. The material exhibits positive strain rate sensitivity (SRS) at room and elevated temperatures; the SRS is more pronounced at high temperatures and lower strain rates. The r-value of the material under tensile loading at room temperatures is higher in TD at lower strain rate. Texture measurements on several failed specimens are reported under tension and simple shear after finite plastic deformation of about 20% equivalent strain. The as-received material exhibits a strong fiber with equal fractions of grains having the c-axis slightly tilted away from the sheet normal towards both +RD and −RD. Pole figures obtained after tensile loading along the rolling direction (RD) show that the texture of the material strengthens even at low strains, with c-axis perpendicular to the sheet plane and prism planes lining up in a majority of grains. However, the tensile loading axis along TD does not lead to similar texture strengthening; the c-axis distribution appears to be virtually unchanged from the virgin state. The pole figures obtained after in-plane compression along RD brings the c-axes of the grains parallel to the loading direction. The pole figures after simple shear loading show that the c-axis rotates to lie on the sheet plane consistent with a compression axis 45° away on the sheet plane.