Simulations of stress-induced twinning and de-twinning: A phase field model

Twinning in certain metals or under certain conditions is a major plastic deformation mode. Here we present a phase field model to describe twin formation and evolution in a polycrystalline fcc metal under loading and unloading. The model assumes that twin nucleation, growth and de-twinning is a process of partial dislocation nucleation and slip on successive habit planes. Stacking fault energies, energy pathways (γ surfaces), critical shear stresses for the formation of stacking faults and dislocation core energies are used to construct the thermodynamic model. The simulation results demonstrate that the model is able to predict the nucleation of twins and partial dislocations, as well as the morphology of the twin nuclei, and to reasonably describe twin growth and interaction. The twin microstructures at grain boundaries are in agreement with experimental observation. It was found that de-twinning occurs during unloading in the simulations, however, a strong dependence of twin structure evolution on loading history was observed.     

Exploring the Formation Mechanism of Deformation Twins in CrMnFeCoNi High Entropy Alloy

The deformation twins initiated in CrMnFeCoNi high entropy alloy at cryogenic temperature are experimentally studied. Under the external loading, a three-dimensional shear stress concentration originating from dislocation tangling at both the grain boundaries and twin boundaries could be formed, which promotes emission of partial dislocations from the planar defects and is thus considered to be the key factor for twin formation. A sympathetic nucleation mechanism is proposed to describe the nucleation behaviors of twins.     

Types of twins and the dislocation structure of α uranium in the initial and explosion-deformed states

Transmission electron microscopy is used to study and analyze the twin and dislocation structures of commercial-purity uranium samples in the initial (undeformed) state and after severe deformation induced by shock loading by plane waves with various intensities. As the shock loading intensity increases, the density of chaotically distributed dislocations and twins first increases, and, then, polygonization processes develop and result in a subgrain structure. Crystallographic analysis of the initial and deformation twins in uranium reveals predominant twins of the compound type {130} and rare {172} and {176} second-type twins.     

EFFECT OF STACKING－FAULT ENERGY ON RESIDUALSUBSTRUCTURE OF EXPLOSIVE SHOCK LOADED METALS

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生物医用316L奥氏体不锈钢的形变组织

借助扫描电镜、电子背散射衍射和透射电镜组织观察,对生物医用奥氏体不锈钢316L的形变组织进行了多尺度深入研究,其工程应变量范围为2%~40%。结果表明,当应变>20%时,316L奥氏体不锈钢中的<001>和<111>取向平行于拉伸方向,即出现了大量的变形孪晶和马氏体。从微米尺度和纳米尺度对孪晶和马氏体相变做详细分析发现,形变首先诱发形成变形孪晶,由于孪晶界减小了位错平均自由程而引起位错塞积,进一步诱发马氏体的转变。随着变形量的增加出现了更多的孪晶和α-马氏体,马氏体相变的过程只有γ→α转变,α马氏体主要分布在孪晶界附近,特别是孪晶交叉的位置。其中,奥氏体基体和α-马氏体之间的取向关系为:[011]_γ//[011]_α,(420)_γ//(123)_α。     

Lattice correspondence during twinning in hexagonal close-packed crystals

The correspondence of the dominant slip modes in parent and twin structures in hexagonal closed-packed crystals is considered within the framework of the theory of deformation twinning. The correspondence matrices, which provide a link between the parent and twin lattices, have been worked out for compound twinning modes and selected metals. Geometrical considerations suggest that in most cases deformation twins should inherit a harder dislocation substructure than that of the corresponding parent. Possible mechanisms of twin hardening are discussed.     

初始织构对AZ31镁合金孪生和织构演化的影响

为研究AZ31镁合金变形孪晶和塑性各向异性,基于率相关晶体塑性本构理论,采用有限元方法建立了具有不同初始织构的镁合金模型（包含滑移和孪生变形机制）,并引入孪晶体积分数,研究其压缩过程中织构演变、孪生和力学性能之间的关系。结果表明：晶体的塑性行为在很大程度上取决于初始织构,初始织构的差异导致了压缩行为的明显各向异性,轴向屈服强度和抗拉伸强度高,径向屈服强度和抗拉伸强度低。压缩塑性变形过程中随着变形量的增加,激活孪晶体积分数增高,且径向压缩激活孪晶体积分数越高,轴向压缩激活孪晶体积分数越低。模拟中出现明显孪晶的点与应力突变的点相吻合,当孪晶体积分数达到一定值时,应力发生突变,此时晶体取向发生显著变化,新的滑移系启动,反映了滑移和孪晶机制耦合对AZ31镁合金力学性能的影响。     

锆合金在应变速率1000s~(-1)下动态压缩显微组织的演化规律(英文)

研究锆合金在应变速率1000s-1动态压缩条件下的显微组织演化规律。基于相同应变速率下多次撞击的方法实现锆合金动态压缩下4个不同的应变水平。在不同的应变水平下,应力—应变曲线具有明显的应变硬化效应,几乎观察不到明显的热软化效应。标定的晶粒边界图像表明,在不同的应变水平下,在变形组织内均可观察到大量的小角晶界,同时,小角晶界的数量和密度随着应变的增加而增多。除了在晶粒边界图像中观察到的小角晶界和大角晶界外,在不同的应变水平下还可观察到孪晶界。孪晶界的类型主要包括{10 1 2}、{11 2 1}拉伸孪晶和{11 2 2}压缩孪晶,且大多数孪晶界为{10 1 2}拉伸孪晶。随着应变水平的增加,变形组织中孪晶界的密度变化不明显。基于不同应变水平下变形组织的表征,提出了动态载荷下锆合金变形和演化过程。显微硬度测试表明,撞击试样的硬度随着应变的增加而逐渐增大,这主要与位错塞积引起的应变硬化有关。     

Strength, strain-rate sensitivity and ductility of copper with nanoscale twins

We present a comprehensive computational analysis of the deformation of ultrafine crystalline pure Cu with nanoscale growth twins. This physically motivated model benefits from our experimental studies of the effects of the density of coherent nanotwins on the plastic deformation characteristics of Cu, and from post-deformation transmission electron microscopy investigations of dislocation structures in the twinned metal. The analysis accounts for high plastic anisotropy and rate sensitivity anisotropy by treating the twin boundary as an internal interface and allowing special slip geometry arrangements that involve soft and hard modes of deformation. This model correctly predicts the experimentally observed trends of the effects of twin density on flow strength, rate sensitivity of plastic flow and ductility, in addition to matching many of the quantitative details of plastic deformation reasonably well. The computational simulations also provide critical mechanistic insights into why the metal with nanoscale twins can provide the same level of yield strength, hardness and strain rate sensitivity as a nanostructured counterpart without twins (but of grain size comparable to the twin spacing of the twinned Cu). The analysis also offers some useful understanding of why the nanotwinned Cu with high strength does not lead to diminished ductility with structural refinement involving twins, whereas nanostructured Cu normally causes the ductility to be compromised at the expense of strength upon grain refinement.     

Effects of Silicon on the Microstructure and Mechanical Properties of 15-15Ti Stainless Steel

Effects of silicon on the microstructure and mechanical properties of 20% cold-worked 15-15Ti austenitic stainless steels are systemically investigated by uniaxial tensile tests, scanning and transmission electron microscope observations, and strength calculations. The results reveal that a large number of deformation twins are formed in the 20% cold-worked steels with various silicon additions. The volume fraction of deformation twins and the density of dislocations increase with silicon content, while the twin thickness slightly decreases. A better strength-ductility combination is achieved by silicon addition, since the yield strength of the steel with 2% silicon is 61 MPa higher than that of the steel with 1% silicon, while their uniform elongations are almost both equal to 16%. The yield strength of the 15-15Ti stainless steels is predominantly contributed by the solid solution, dislocation and deformation twin strengthening effects, which can be enhanced by silicon addition.     

拉伸取向控制对AZ31镁合金孪生和织构演化的影响

以室温单轴拉伸实验与晶体塑性有限元相结合的方法,通过拉伸取向控制,研究了AZ31镁合金拉伸变形过程中孪生行为、织构演化规律、塑性各向异性之间的关系。基于率相关晶体塑性本构理论,建立了滑移和孪生机制耦合的具有不同取向的晶体塑性本构模型,引入孪晶体积分数研究孪生对AZ31镁合金塑性变形过程中织构演变和力学性能的影响。结果表明,2种不同取向的样品在塑性变形过程中呈现出明显不同的织构演变规律,表现出明显的各向异性。轴向拉伸时孪生被抑制,孪晶激活体积分数低,径向拉伸时孪晶极易产生,孪晶激活体积分数高。轴向试样在整个塑性变形过程中{0001}极图偏移较小,径向试样因大量拉伸孪晶的开启,使得{0001}棱柱面织构的极密度逐渐向RD的正反方向发生明显偏移。     

Deformation twinning mechanisms from bimetal interfaces as revealed by in situ straining in the TEM

During in situ transmission electron microscopy indentation of layered Cu/Nb composites fabricated by accumulative roll bonding, we observed the nucleation and growth of deformation twinning in Cu. Combining dislocation theory and interface defect structure analysis, we propose that the processes of nucleation and thickening of deformation twins proceed as follows: (1) nucleation and emission of a nanometer thick twin nucleus due to the dissociation of interfacial misfit dislocations or the interaction between a run in Nb slip dislocation and the interface or both; (2) emission of a second twin nucleus by the same mechanism, but at some distance along the interface from the first; (3) in the region in-between them, twin thickening occurs by relatively rapid emission of oppositely signed twinning dislocations in order to reduce the backstresses due to the twins in processes 1 and 2; and finally (4) the continuation of this “alternating emission” growth mechanism such that eventually the entire domain in-between the two initially separated fine twin nuclei transforms into a thick twin.     

Deformation twins in nanocrystalline body-centered cubic Mo as predicted by molecular dynamics simulations

This work studies deformation twins in nanocrystalline body-centered cubic Mo, including the nucleation and growth mechanisms as well as their effects on ductility, through molecular dynamics simulations. The deformation processes of nanocrystalline Mo are simulated using a columnar grain model with three different orientations. The deformation mechanisms identified, including dislocation slip, grain-boundary-mediated plasticity, deformation twins and martensitic transformation, are in agreement with previous studies. In 〈1 1 0〉 columnar grains, the deformation is dominated by twinning, which nucleates primarily from the grain boundaries by successive emission of twinning partials and thickens by jog nucleation in the grain interiors. Upon arrest by a grain boundary, the twin may either produce continuous plastic strain across the grain boundary by activating compatible twinning/slip systems or result in intergranular failure in the absence of compatible twinning/slip systems in the neighboring grain. Multiple twinning systems can be activated in the same grain, and the competition between them favors those capable of producing continuous deformation across the grain boundary.     

Role of deformation twins in static recrystallization kinetics of high-purity alpha titanium

The importance of deformation twins in static recrystallization kinetics of high-purity alpha titanium was investigated by carrying out thermal annealing tests of deformed materials in combination with electron-backscatterdiffraction- based microstructural analysis. Prior to thermal annealing, the material was compressed to a true strain of 0.22 along three directions to introduce different twinning characteristics. Our results showed that deformation twins substantially promoted the static recrystallization process by deepening the microstructural inhomogeneity induced by the formation of twin boundaries and twinning-induced crystallographic lattice reorientation. Twin morphology was also observed to be important because it influenced the extent of microstructural inhomogeneity. Intersecting twin morphology, caused by the activation of multiple twin variants, was more effective than parallel twin morphology, caused by the activation of a single twin variant (or a twin variant pair), because it gave rise to more twin boundaries, more twin boundary junctions (intersections, triple junctions, etc.), and greater in-grain crystallographic orientation spread.     

Deformation twinning at aluminum crack tips

Recent experimental evidence has shown that even fcc materials that are not normally associated with deformation twinning, such as aluminum, will twin given a sufficiently high stress concentration such as at a crack tip. In this paper we present a computational study of the atomic structures that form at the tips of atomically sharp cracks in aluminum single crystals under loading. The simulations were carried out using the quasicontinuum method—a mixed continuum and atomistic approach. A variety of loading modes and orientations were examined. It was found that for certain combinations of loading mode and orientation, deformation twinning does occur at aluminum crack tips in agreement with experimental observation. For other configurations, either dislocation emission or in one case the formation of an intrinsic–extrinsic fault pair was observed. It was also found that the response at the crack tip can depend on the crack-tip morphology in addition to the applied loading and crystallographic orientation.     

A MICROMECHANICAL MODEL FOR γ-TiAl BASE PST CRYSTALS

An analytical micromechanical method is proposed to examine the dependence of plastic deformation on the microstructure for a PST crystal. The sub-domain rnicrostructure of the γ phase and the effect of the α2 phase are taken into account by a proper micromechanical formulation,the dislocation slip and twinning deformation mechanisms are considered in the context of crystal plasticity. The model can well predict the dependence of stress-strain relations on loading angle with respect to the microstructure. The influence of the twinning and lamellar spacing on the deformation behavior and biaxial yield surfaces for PST crystals are also examined.     

A MICROMECHANICAL MODEL FOR γ-TiAl BASE PST CRYSTALS

An analytical micromechanical method is proposed to examine the dependence of plastic deformation on the microstructure for a PST crystal. The sub-domain microstructure of the γ phase and the effect of the α2 phase are taken into account by a proper micromechanical formulation, the dislocation slip and twinning deformation mechanisms are considered in the context of crystal plasticity. The model can well predict the dependence of stress-strain relations on loading angle with respect to the microstructure. The influence of the twinning and lamellar spacing on the deformation behavior and biaxial yield surfaces for PST crystals are also examined.     

镁合金塑性变形力学行为与微观组织研究进展

介绍了镁合金在单轴压缩、单轴拉伸、轧制和挤压条件下塑性变形的力学行为及微观组织结构演变规律。简述了镁合金中二次拉伸孪生现象以及各种变形条件下孪生与孪生变体类型的选择规律。基于对镁合金位错滑移、机械孪生及动态回复与再结晶行为的认识,对镁合金力学行为的各向异性、轧制与挤压成型能力的影响规律进行了探讨,强调了初始织构对变形机制、动态再结晶及成型能力的重要影响。最后讨论了析出强化镁合金塑性变形与强韧化机理。