Transgranular slip and fracture across an interface in α-β brass two-phase bicrystals

The passage of slip and the transgranular fracture across the interface of - brass two-phase bicrystals were investigated in connection with the orientation relationships of the bicrystals. The passage of slip across the interface was observed in the slip systems with misorientation less than 10 degrees. These results were related to the interface dislocation created when a dislocation propagates across the interface. The twist disclination model proposed by Marcinkowski for the passage of a dislocation across the twist boundary was recognized at the interface of the present two-phase bicrystals. The initiation and the propagation of the transgranular crack was seen at the interface where the passage of slip was investigated. It was noted that this transgranular crack was caused by the high stress field around the deformation ledge created when many dislocations passed through the interface.On leave from the Department of Mechanical Engineering, Faculty of Engineering, Al-Azhar University, Cairo, Egypt.     

Cyclic Deformation and Fatigue Damage Behavior of Cu Monocrystals, Bicrystals and Tricrystals

1.IntroductionMostofmechanisticstudiesoncyclicdeformationhavebeencarriedoutonCucrystalsinsingle-slipori-entations.ThereareseveralexcellentreviewarticleswhichemphasizeddifferentaspectsofthesubjectI1~6].Whenawell-annea1edCucrystalsuitablyorientedforsingleslipissubjectedtocyclicdeformationbetweenconstantplasticstrainamplitudelimits7platroomtemperatureinair,itwillhardenundertheactionofcyclicstraining.Thepeakstressincreasesrapidlyatfirstandthenmoreslowly,approachingavalue,thesaturationstressTs.Ap…     

铜三晶体的循环形变行为及位错组态

采用逐级增幅方法研究了「０１１」同轴铜三晶体及一种非同轴取向平行三晶交线铜三晶体的循环形变行为,并观察了三晶交点和晶界附近的位错组态。为了对比,也研究了两种取向三晶体的组元晶粒双晶体和单晶体试样的循环形变行为。对于「００１」同轴取向平行三晶交线三晶体及其组元双晶体和单晶体,其循环硬化曲线几乎重合,其循环饱和应力应变曲线（ＣＳＳＣ）也相差不大,由于各滑移系之间的位错反应生成Ｌｏｍｅｒ－Ｃｏｔｔｅｌ锁,阻碍位错运动,所以三晶交线和晶界对轴向饱和应力几乎没有强化作用。对于「００１」取向晶体,在（００１）观察面上,可以看到很多较短的一段一段的位错墙结构,各段之间互不连通,这是各滑移系之间的错反应强烈,生成不动的位错锁的结果。这也是三晶交线和晶界无明显强化作用的原因。对于非同轴取向铜三体及组元晶粒双晶体、单晶体的循环形变     

Reactions of slip dislocations with twin boundary in Fe-Si bicrystals

Specimens for in situ TEM straining were prepared from Fe-5.5 at.%Si Σ 3 bicrystals with {112} grain boundary plane. They were strained under three different directions of the stress at the boundary with respect to the orientation of the grains. Transfer of slip across the boundary was analysed. In one case, the transfer of slip was realized by a transformation of the slip dislocation in one grain into the slip dislocation in the other grain. Low energy dislocation was created in the GB in accordance with general transfer criteria. In the second case, the incoming and outgoing slip systems were in direct contraction to the general transfer criteria. In the third case, oriented for common slip system in both grains, the trapped incoming slip dislocations dissociated into twinning dislocations which created twins on the other side of the boundary.     

Investigation of small crack behaviour under cyclic loading in a dual phase steel with an FIB tomography technique

Damage accumulation is investigated in the early stage of fatigue life in a ferritic martensitic dual phase steel. Microcrack initiation and propagation are influenced by microstructure, such as grain boundaries, grain orientation and/or phase distribution morphology. The dominant crack initiation pattern is one in which microcracks are generated in a ferrite grain along slip bands inclined at a certain angle with respect to the loading direction. Subsurface observation with a focused ion beam (FIB) device and additional crystallographic characterization by means of the electron backscatter diffraction (EBSD) technique show that a slip system having a high Schmid factor value is activated and results in a crack nucleus. The FIB tomography technique with the help of EBSD measurement allows a three‐dimensional investigation of small crack behaviour to be performed.     

Microstructure and tensile behaviour of pure titanium produced after high-energy shot peening

In this study, the microstructure and tensile behaviour of pure titanium processed by means of high-energy shot peening have been studied. The results show that a nanocrystalline surface layer is prepared on the surface of pure titanium. During severe deformation, the dislocations, twins and slip bands with single orientation are formed first, then the intersections of twins and slip bands are observed, and then the subgrains appear near or in the slip bands and finally the randomly oriented nano-grains are formed due to the further breakdown. After high-energy shot peening, the ultimate tensile strength and the yield strength increase by 27 and 40%, while the elongation decreases by 64% after treatment, due to the increasing dislocation density, micro-strain and the grain refinement.     

Orientation dependence of fracture in copper bicrystals with symmetric tilt boundaries

Experimental results (Wang and Anderson (1991), Acta Metall. 39, 779–792) show that the fracture behavior of Σ9 copper bicrystals depends on the cracking direction. Near-interface transgranular fracture surfaces were observed in the case of the crack growing in the [ 14] direction, with an essentially ductile failure mode, while the case of the crack growing in the [1 ] direction showed far less toughness and had an intergranular fracture surface with cleavage tongues. Asymptotic and finite element models for stationary cracks in ideally plastic and strain hardening materials have been used to examine this cracking direction dependency from a small strain continuum mechanics point of view. The tensile stress ahead of the crack tip was found to be essentially identical for the two growth directions, with the brittle orientation resulting in only slightly higher stress values at small distances from the crack tip. However, the strain field was found to be different for the two orientations, with the overall plastic zone size being much larger in the ductile case. Also, the orientations of the zones of concentrated shearing ahead of the crack, observed in the ideally plastic model, suggest two different dislocation shearing mechanisms. In the ductile case, this zone is parallel to the slip plane, resulting in a regular shearing mechanism in which dislocations can be nucleated at the crack tip and glide on the (111) slip plane. In contrast, this zone is perpendicular to the (111) slip plane in the brittle case, resulting in a kinking shear mode in which dislocations from other external sources expand in a dipole mode to produce macroscopically concentrated shearing. Thus, apart from the dislocation nucleation considerations, continuum mechanics does not seem to be able to fully explain this difference in directional dependency of fracture in the Σ9 copper bicrystals.     

Grain Boundary Sliding in Aluminum Nano‐Bi‐Crystals Deformed at Room Temperature

Room‐temperature uniaxial compressions of 900‐nm‐diameter aluminum bi‐crystals, each containing a high‐angle grain boundary with a plane normal inclined at 24° to the loading direction, revealed frictional sliding along the boundary plane to be the dominant deformation mechanism. The top crystallite sheared off as a single unit in the course of compression instead of crystallographic slip and extensive dislocation activity, as would be expected. Compressive stress strain data of deforming nano bicrystals was continuous, in contrast to single crystalline nano structures that show a stochastic stress strain signature, and displayed a peak in stress at the elastic limit of ～176 MPa followed by gradual softening and a plateau centered around ～125 MPa. An energetics‐based physical model, which may explain observed room‐temperature grain boundary sliding, in presented, and observations are discussed within the framework of crystalline nano‐plasticity and defect microstructure evolution.     

Initiation of corrosion fatigue cracks at defined grain boundaries in bicrystals

The fatigue tests in air show that persistent slip bands (PSB's) and cracks nucleate very early at special grain boundaries. At stress amplitudes for which no persistent slip band nucleation was observed in single crystals and which were oriented for single slip, cracks still nucleate at grain boundaries. The endurance limit for special bicrystals lay 50% below the endurance limit of polycrystals. In air, the cracks nucleate at the boundary but propagate within the PSB. From the stress amplitudes at which PSB's nucleate in single crystals and in bicrystals, which have one grain with the same orientation as the single crystals, the additional shear stress due to elastic anisotropy was measured to be 55 MPa. These tests yield an understanding of the behavior of short cracks, which nucleate at special boundaries but cannot propagate further, if they hit an unfavorably oriented boundary for which higher local stresses for propagation were needed.With the same bicrystals, corrosion fatigue tests were carried out in ammonium carbonate solutions. In the solution, crack nucleation was found to depend on frequency and amplitude. Contrary to the behavior in air, the cracks nucleate at and propagate along the grain boundary. Specimens which last for 10⁵ cycles in air only survive 6·10³ cycles at the lowest frequencies tested. In addition, if the stress amplitude is reduced by 27%, it was observed that, for a given frequency, the fatigue life is reduced by more than 90% relative to the fatigue life in air at the same stress level. The susceptibility of special boundaries against corrosion fatigue combined with the observed dependencies on stress amplitude and frequency could be understood on the basis of the slip step dissolution model for SCC.     

AZ31镁合金室温拉伸微观变形机制EBSD原位跟踪研究

利用电子背散射衍射(EBSD)技术,原位跟踪AZ31镁合金轧制板材室温下沿轧向拉伸时的晶粒取向变化。对变形过程的滑移系和孪晶启动机进行分析。结果表明:变形过程主要由〈a〉基面和柱面滑移系开动而实现,晶粒取向无明显变化,大量〈a〉位错滑移的产生,使得变形后小角度晶界增加明显。晶粒中拉伸孪晶是试样在拉伸变形过程中产生的,而非在试样拉伸后的卸载过程中产生。     

D6A钢在轧制过程中的强韧化机理EI北大核心CSCD

通过轧制-热处理工艺能够使D6A钢的强度显著提高。为了探究其强韧化机理,本实验采用热轧及两相区温轧退火工艺,获得微米级D6A合金钢样品,微观组织为铁素体基体及粒状渗碳体。通过室温拉伸实验、SEM、X射线衍射、EBSD等手段对实验钢的显微组织和力学性能进行表征,结果表明:随着变形量的增加,晶粒尺寸由4.5μm细化为1.5μm,渗碳体的含量逐渐增加,小角度晶界的比例升高,屈服强度和抗拉强度不断增加,伸长率略有降低,说明轧制过程使亚晶粒的尺寸不断降低,晶界面积增加,位错滑移受到的阻力增大。同时,本研究对不同轧制变形量实验钢的位错密度进行计算,当轧制变形量为88%时,位错密度最高,此时加工硬化的程度最高。随着变形量的增加,第二相强化和晶粒细化引起的强度增量呈不断上升的趋势,位错强化引起的强度增量先升高后降低,D6A钢的主要强化方式为第二相强化、细晶强化及位错强化。     

Effect of grain size on grain boundary strengthening of copper bicrystals under cyclic loading

Abstract

To clarify the strengthening effect of grain boundaries (GB), cyclic deformation behaviour of really grown [4¯79] ∥ [1¯25] copper bicrystals with different widths (4, 6, and 8 mm, denoted RB-4, RB-6, and RB-8) of com-ponent crystals and a combined copper bicrystal (denoted CB-6), obtained by sticking component single crystals G1 [4¯79] and G2 [1¯25] together, was investigated. The results showed that the cyclic saturation stresses increased in the order of bicrystals of CB-6 < RB-8 < RB-6 < RB-4. It is indicated that the GB effect caused different degrees of strengthening, which increased with the decreasing width of the RB bicrystals. By surface observation, it was found that only the primary slip system was activated in the combined bicrystal during cyclic deformation. However, an additional slip system appeared near the GB within the crystal G2 [1¯25] in the RB bicrystals (except in the primary slip system), and formed a GB affected zone (GBAZ). The width of the GBAZ was about 400 and 600 μm at plastic strain amplitudes of 0·1% and 0·2% respectively. Meanwhile, using an electron channelling contrast (ECC) technique in the SEM, the dislocation patterns near the GB and within the component crystals were observed. It was found that a two phase structure of persistent slip bands (PSBs) and matrix (or veins) can form in these bicrystals, similar to that in copper single crystals. But these PSBs cannot transfer through the GB during cyclic deformation. Based on the results above, the effect of grain size on GB strengthening of copper bicrystals was discussed.     

The study of grain boundary density effect on multi-grain thin film under tension

The grain-size effect on the yield strength and strain hardening of thin film at sub-micron and nanometer scale closely relates to the interactions between grain boundary and dislocation. Based on higher-order gradient plasticity theory, we have systematically investigated the size effect of multi-grain thin film arising from the grain boundary density under tensile stress. The developed formulations employing dislocation density and slip resistance have been implemented into the finite element program, in which grain boundary is treated as impenetrable interface for dislocations. The numerical simulation results reasonably show that plastic hardening rate and yield strength are linear to the grain boundary density of multi-grain thin film. The aspect ratio of grain size and orientation of slip system have distinct influence on the grain plastic properties. The research of slip system including homogeneous and nonhomogeneous distribution patterns reveals that the hardening effect of low-angle slip system is greater than that of high-angle slip system. The results agree well with the experimentally measured data and the solutions by discrete dislocation dynamics simulation.     

Study of Deformation Mechanisms in Titanium by Interrupted Rolling and Channel Die Compression Tests

The mechanisms of small plastic deformation of titanium (T40) during cold rolling and channel die compression by means of "interrupted in situ" EBSD orientation measurements were studied. These interrupted EBSD orientation measurements allow to determine the rotation flow field which leads to the development of the crystallographic texture during the plastic deformation. Results show that during rolling, tension twins and compression twins occur and various glide systems are activated, the number of grains being larger with twins than with slip traces. In channel die compression, only tension twins are observed in some grains, whereas slip traces can be spotted in almost all observed grains. The different stress conditions and different strain rates existing under the two modes of deformation lead to the activation of different deformation mechanisms.     

On the in situ relaxation of interphase interfaces

A previously used method for the study of twist boundaries in Au bicrystals is extended to interfaces in Au/AuPd and Au/Pd bicrystals. Transmission electron microscopy and electron diffraction results of the relaxation of small-angle boundaries, boundaries close to the coherent twin orientation and epitaxial layers are reported and interpreted in terms of dislocation networks with Burgers vectors of the typea/2 〈ˉ1 1 0〉 ofa/6 〈1 1 ˉ2〉.     

Experimentelle Charakterisierung und zweidimensionale Simulation der mikrostrukturbestimmten Ermüdungsrissausbreitung in einer β‐Titanlegierung

In this project the initiation and propagation of short fatigue cracks in the metastable β‐titanium alloy TIMETAL®LCB is investigated. By means of an interferometric strain/displacement gauge system (ISDG) to measure the crack opening displacement (COD) and the electron back scattered diffraction technique (EBSD) to determine the orientation of individual grains the microstructural influence on short crack initiation and growth can be characterized. Finite element calculations show a high influence of the elastic anisotropy on the initiation sites of cracks. Crack propagation takes place transgranulary along slip planes as well as intergranulary along grain boundaries. The crack growth rate depends strongly on the active mechanism at the crack tip which in turn is influenced by crack length, the applied stress and the orientation of the grains involved. The value of the steady state crack closure stress changes from a positive value at low applied stresses (roughness induced) to a negative one at higher applied stresses (due to plastic deformations at the crack tip). The crack growth simulation is realised by a two‐dimensional boundary element technique, which contains the ideas of Navarro und de los Rios. The model includes the sequence of the applied stress amplitude as well as the experimental measured roughness induced crack closure.     

EBSD – orientation analysis of monocrystalline diamonds used for diamond metal composites – Influence of sample preparation

This paper focuses on a new field of application for the EBSD‐technique. Generally, EBSD‐mappings are performed on different metal alloys used for quality assurance and to get information about the microstructure regarding grain orientation, grain size and distribution. In contrast, the orientation determination of monocrystalline diamond grains with an EBSD system is not a conventional method. Thus, this work describes the EBSD testing sequence in detail and illustrates the preparation of orientation data for a statistical design. Furthermore, dependencies of the sample preparation, alignment to the detector, and the analyzed position on the diamond on the quality of the Kikuchi‐patterns, respectively on the indexing rates, have been scrutinized. Finally, the orientation obtained of each tested diamond sample has been utilized in a statistical design to show a direct influence of the crystal orientation on the wear behavior of the diamond grains.     

变形温度与应变速率耦合作用对TWIP效应Ti-15Mo合金力学性能的影响EI北大核心CSCD

变形温度和应变速率均影响β型钛合金的力学性能,且其影响均关联塑性变形过程中变形方式的变化。利用TEM,EBSD,SEM,XRD,OM和拉伸试验机研究变形温度和应变速率耦合作用对{332}〈113〉孪生诱发塑性效应Ti-15Mo合金力学性能的影响。结果表明:在298 K和573 K下,屈服强度均随应变速率的增加逐渐升高,即依赖于位错热激活过程,且573 K下显著的位错热激活作用使得屈服强度表现出更大的应变速率依赖性。不同于298 K下,Ti-15Mo合金在573 K下通过{332}〈113〉孪生和位错滑移耦合变形;构建的流变应力模型表明位错强化成为其主要强化方式。高应变速率下,塑性变形早期形成的更多孪晶虽然会抑制孪生的进一步产生降低加工硬化率,但同时有效降低位错不均匀分布引起的局部应力集中延缓颈缩的发生;两个方面的共同作用使得Ti-15Mo合金在变形温度和应变速率耦合作用下呈现出更小的应变速率依赖性。     

Deformation behaviors of Cu bicrystals with an inclined twin boundary at multiple scales

Cu bicrystals of different sizes with a sole twin boundary(TB) inclined at 45?with respect to the loading direction were deformed under unidirectional and cyclic loading, respectively. It is found that the slip bands(SBs) parallel to the TB can be activated near the TB at all scales without obeying the Schmid's law.It is concerned with the local stress enhancement in the macroscale while it is more closely related to the scarce dislocation sources in the microscale. Moreover, a wedge-shaped zone formed near the TB in the microscale ascribed to the limited specimen size.     

Microstructural influence on small fatigue cracks in a ferritic–martensitic steel

Microstructure effects on fatigue crack initiation and propagation in ferritic–martensitic dual phase steel were investigated. Slip bands were formed in ferrite grains after several thousand cycles with ensuing crack initiation due to dislocation pile-up. Subsurface observations using a focused ion beam (FIB) and crystallographic analyses using electron backscatter diffraction (EBSD) measurements showed that crack initiation occurred as a result of the activation of a slip system having a high Schmid factor. Surface crack nucleation occurred quite frequently at ferrite/martensite and ferrite/ferrite boundaries, with crack propagation in the ferrite grains. This initiation mode can be attributed to the mismatch stresses at ferrite/martensite phase boundaries and at high angle grain boundaries.