Study on microtexture of laser welded 5A90 aluminium–lithium alloys using electron backscattered diffraction

Abstract

The microtexture features of Nd:YAG laser welded joints in 5A90 aluminium–lithium (Al–Li) alloys were examined using electron back scattered diffraction (EBSD). Microtexture was determined by means of the grain orientation image maps (OIM), pole figures (PF), misorientation angles and orientation distribution function (ODF) of the weld metal (WM), heat affected zone (HAZ) and unaffected base metal (BM) of the welded joint. The results show that there is a change of microtexture in the WM and HAZ of the welded joint in terms of the component and intensity of the texture. The HAZ of the welded joint inherits the texture characteristics of the BM, whereas the welding heat input has an important influence on the component C {112}<111>. The WM of the welded joint is composed of predominantly equiaxed grains with a random microtexture.     

Superplastic deformation mechanisms of high Nb containing TiAl alloy with (α2 + γ) microstructure

In this paper, superplastic deformation behaviour of a high Nb containing TiAl alloy with fine (α₂ + γ) microstructure, Ti–43.5Al–8Nb–0.2W–0.2B (at.%), has been examined and studied by means of hot tension from 850 °C to 1050 °C under an initial strain rate of 10⁻⁴ s⁻¹. The mechanical behaviour and microstructure evolution have been characterized and analyzed. Besides, to gain insight into deformation mechanisms, the texture evolution during deformation at ordinary (non-superplastic) and superplastic conditions has been systematically studied. The results showed that, the alloy exhibited impressive superplastic elongation at 1000 °C with a strain-rate sensitivity exponent (m) of about 0.5 and an apparent activation energy (Q_app) value of about 390 kJ/mol. The microstructural characterization showed that, when the alloy was deformed at ordinary condition (850 °C), severe grain refinement occurred and the fraction of low-angle grain boundary notably increased. Meanwhile, the textures were characterized by <100> and <111> double-fiber components parallel to the tensile direction. All these observations suggested a dislocation slip and twinning mechanism. However, if deformed at the superplastic condition (1000 °C), it was found that the microstructure was fairly stable in terms of grain size, morphology and grain boundary characteristics during tension, but a continuous weakening of the initial <110> fiber texture (resulted from canned-forging) was observed. This was believed to be an indication of grain boundary sliding mechanism. Moreover, the deformation texture (<100> + <111>)—though is very weak—was simultaneously appeared. According to a detailed discussion on the deformation kinetics and microstructure evolution, it was believed that the slip/twinning-accommodated grain boundary sliding was responsible for superplastic deformation and the dislocation climb inside of γ grains was the rate-controlling step.     

初始织构对差厚板非均匀塑性变形的影响

CR340轧制差厚板（TRB）在轧制过程中,其不同的厚度区形成了不同的织构,分别是薄区的{111}<01>和{141}<22>织构,过渡区的{225}<10>和{211}<01>织构,厚区的{876}<5>和{411}<01>织构。根据EBSD测试结果,建立了各厚度区的多晶体塑性有限元模型,研究了单向拉伸时各厚度区的晶粒织构对滑移系开动情况和应力应变分布的影响规律。结果表明,薄区的{111}<01>织构和厚区的{876}<5>织构有利于滑移系的开动,开动的数量分别为9和8组,这使得等厚区在变形中的应力集中弱化,具有良好的塑性变形行为。而过渡区的{225}<10>、{211}<01>织构的晶粒滑移系开动较少,开动的数量分别为6和7组,导致应力集中,其塑性变形行为较差。差厚板各厚度区织构的差异导致其塑性变形呈现明显的不均匀性,其断裂位置发生在单轴拉伸时塑性变形较差的过渡区。     

Crystal plasticity finite element simulation of NiTi shape memory alloy based on representative volume element

Crystal plasticity finite element method based on a representative volume element model, which includes the effect of grain shape and size, is combined with electron backscattered diffraction experiment in order to investigate plastic deformation of NiTi shape memory alloy during uniaxial compression at 400 °C. Simulation results indicate that the constructed representation of the polycrystal microstructure is able to effectively simulate macroscopically global stress-strain response and microscopically inhomogeneous microstructure evolution in the case of various loading directions. According to slip activity and Schmid factor in {110}<100>, {010}<100> and {110}<111> slip modes, <100> slip modes are found to play a dominant role in plastic deformation, while <111> slip mode is found to be a secondary slip mode. In addition, the simulation results are supported well by the experimental ones. With the progression of plastic deformation, the (001) [\(0\bar 10\)] texture component gradually disappears, while the γ-fiber (<111>) texture is increasingly enhanced.     

Stability of initial texture components during deep drawing of FCC polycrystals

Stability of ideal orientations and texture formation during deep drawing were investigated for a hot roiled AA 1050. Lattice rotation fields around ideal orientations were numericlly predicted using a rate sensitive polycrystal model with full constraint boundary conditions. In order to evaluate the strain path during deep drawing of an AA1050, simulations using a finite element analysis were carried out. The stability of orientations and texture formation were examined at the sequential strain paths such as flange deformation and wall deformation. During flange deformation, Goss and P_f 0 1 1 <21 32 32 > (shifted form P {0 1 1} <8 11 11>) satisfied the stability condition of texture formation, while during wall deformation, only B_w {0 1 1} <17 13 13> (shifted from Brass) and D_w {5 5 12} <6 6 5> (shifted from Dillamore) satisfied the stability condition of orientation.     

Spatial characterisation of the orientation distributions in a stable plane strain-compressed Cu crystal: A statistical analysis

Single copper crystals of the stable Goss orientation {0 1 1}〈1 0 0〉 were deformed in plane strain compression and the deformation-induced dislocation structures were investigated by high-resolution electron backscattered diffraction. Although the orientation maps exhibited an anisotropic dislocation boundary structure it was shown that the mean disorientation angle between point pairs saturated and became isotropic if their spacing was large enough (typically >30 μm). This saturation behaviour was interpreted as being a consequence of the anti-correlations between nearby dislocation boundaries and is discussed in terms of recent stochastic models of boundary formation. It was found that the disorientation boundaries, which were considered as being formed at relatively low strains, underwent rigid body-like rotations during deformation.     

Ti-2Al-2.5Zr单道次皮尔格轧制过程中显微组织和织构的演化

研究了单道次皮尔格轧制过程中Ti-2Al-2.5Zr材料的变形行为和织构的演变规律。结果表明,在轧制过程中,｛102｝孪晶和柱面滑移是最容易被激活的2种变形模式,｛102｝孪晶的产生使得晶粒在轴向上的位向从<100>转向<110>。并且,在不同瞬时Q值和等效应变量下,滑移和孪生导致｛0001｝极图中最大极密度点在切向上发生变化。     

Microstructural evolution and grain boundary sliding in a superplastic magnesium AZ31 alloy

Tensile experiments on a fine-grained single-phase Mg–Zn–Al alloy (AZ31) at 673 K revealed superplastic behavior with an elongation to failure of 475% at 1 × 10^?4 s^?1 and non-superplastic behavior with an elongation to failure of 160% at 1 × 10^?2 s^?1; the corresponding strain rate sensitivities under these conditions were ～0.5 and ～0.2, respectively. Measurements indicated that the grain boundary sliding (GBS) contribution to strain ξ was ～30% under non-superplastic conditions; there was also a significant sharpening in texture during such deformation. Under superplastic conditions, ξ was ～50% at both low and high elongations of ～20% and 120%; the initial texture became more random under such conditions. In non-superplastic conditions, deformation occurred under steady-state conditions without grain growth before significant flow localization whereas, under superplastic conditions, there was grain growth during the early stages of deformation, leading to strain hardening. The grains retained equiaxed shapes under all experimental conditions. Superplastic deformation is attributed to GBS, while non-superplastic deformation is attributed to intragranular dislocation creep with some contribution from GBS. The retention of equiaxed grain shapes during dislocation creep is consistent with a model based on local recovery related to the disturbance of triple junctions.     

Separate contributions of texture and grain size on the creep mechanisms in a fine-grained magnesium alloy

The influence of texture and grain size on the creep behavior of a fine-grained magnesium alloy, over the temperature range 423–723 K was investigated. Equal channel angular pressing and rolling were used to produce samples with different textures. Two deformation regimes could be distinguished by their stress exponents. A stress exponent close to 2 and activation energy of 91 kJ mol⁻¹, close to that for grain boundary diffusion, were found at the lower strain rates. In this range, there is no detectable effect of texture. In the high stress exponent regime, within the range 3 < n < 12, a noticeable effect of texture and grain size has been found. The texture effect is related to the orientation of the basal planes. The influence of grain size distribution on flow stress is satisfactorily explained by modeling the deformation as a combination of grain boundary sliding and slip creep.     

Effect of deformation texture on the anisotropy of elasticity and damage of two-phase steel sheets

The effect of small tensile deformation (3, 6, and 10%) on the texture of preliminary annealed sheets of two-phase DP600 steel (0.10 C, 0.15 Si, 1.4 Mn, 0.007 P, 0.008 S, 0,009 N, 0.02–0,06 Al, 1 Cr–Mo–Ni (wt %)) is studied. Against the background of the annealing texture in the sheets, the {001} <110>, {111} <110>, {111} <112>, {111} <312> components of the slip texture and {115} <110>, {115} <552>, {221} <110>, {221} <114> orientations are developed, which can be associated with the twinning processes. The anisotropy pattern of the Young’s modulus (E) in the sheet plane remains the same after tensile deformation of the annealed sheets. After tension, the values of E decrease in all directions as a result of the onset and development of microdamages. The anisotropy of damage (D) in the plane of the steel sheets after tension is characterized by a maximum in the transverse direction (TD) and a minimum in the rolling direction (RD).     

Micromechanical mechanism of texture formation in γ-TiAl

Texture evolution in TiAl depends on the type of deformation such as uniaxial compression, tension or rolling as well as on the initial microstructure. Cast TiAl shows a lamellar microstructure with an alignment of the lamellae and exhibits a strong texture. Deformation parallel to the aligned lamellae results in a plane-strain deformation which leads to a brass type texture. From room temperature up to 700 °C, compression tests of TiAl specimens with equiaxed microstructures result in <110>-fiber textures where the <101> component is shifted to <302>. At higher temperatures the orientation <302> is caused by dynamic recrystallization. In rolled sheets of TiAl with equiaxed microstructure the main texture component is a modified cube texture {100}<010> where the tetragonal c-axis is aligned in transverse direction of the sheet. This texture component is caused by dynamic recrystallization and appears to be stable against further rolling.     

Recrystallisation of channel die deformed single crystals of typical rolling orientations

The effect of deformation microstructure heterogeneity on recrystallisation behaviour has been studied using channel die deformed single crystals of typical f.c.c. rolling texture components. These orientations exhibit a wide range of both spatial and orientational heterogeneity. The likelihood of recrystallisation nuclei developing from within the deformed microstructure is found to be directly related to the extent of this heterogeneity. The recrystallisation textures comprise both a retained deformation texture component, as well as a component close, but beyond, to one extreme of the deformation texture spread. The growth of recrystallised grains, regardless of orientation, is affected by the degree of heterogeneity of the deformation microstructure. For randomly oriented nucleation, and under equivalent annealing conditions, recrystallisation proceeds two orders of magnitude faster in the lower stored energy homogeneous {110}<112> orientation than in the {123}<634> orientation, with a much more heterogeneous microstructure and higher stored energy, even after recovery.     

Interpretation of hot rolling and cold rolling texture in high purity aluminium

In high purity aluminium two different types of hot band textures were produced by changing the final hot rolling temperatures. The texture of the hot bands was found to be inhnmogeneous through thickness. The strong preferred orientation of {001}<110> developed in the surface layer of the hot band which had been rolled at the higher finishing temperature. For the lower finishing temperature sample, the cold rolling type of texture was formed in the hot band. The cold rolling texture was dependent on the initial hot rolling texture. The hot band which had strong {001}<110> at the surface layer led to the maximum orientation density at {44 11}<11 11 8> after the subsequent cold rolling. Preferred orientations near {123}<634> in the hot band caused the maximum at {123}<634> in the cold rolling texture. The experimental results were discussed based on the simulation test of deformation texture in which the rotation of orientations was calculated from the Taylor model. In this calculation, the strain state of the deformation zone in the rolling gap is assumed to vary with shears induced from the geometry and the friction.     

Effect of Zn and Y Additions on Grain Boundary Movement of Mg Binary Alloys During Static Recrystallization

Texture evolution in rolled Mg–1 wt% Zn and Mg–1 wt% Y binary alloys was analyzed by quasi-in situ electron backscatter diffraction (EBSD) during static recrystallization. Mg–1 wt% Zn and Mg–1 wt% Y alloys exhibited strong basal texture at the initial recrystallization state. After grain growth annealing, the basal texture component {0001} < $11\overline{2}0$ > was increased in Mg–1 wt% Zn alloy and that of Mg–1 wt% Y alloy was decreased to be a random texture. Zn and Y atoms segregated strongly to the recrystallized grain boundaries in Mg–1 wt% Zn alloy and Mg–1 wt% Y alloy, respectively. Thus, Zn and Y elements facilitated the grain boundary movements along contrary directions during grain growth. In Mg–1 wt% Zn alloy, due to the Zn element segregation on grain boundaries, the grains consisted of a strong texture grew more easily because the grain boundary migration tended to move from the orientation close to normal direction to the orientation near to transverse direction or rolling direction. Therefore, after grain growth, the volume fraction of texture component {0001} < $11\overline{2}0$ > was increased by consuming the neighboring grains, leading to a stronger basal texture. On the contrary, in the Mg–1 wt% Y alloy, the Y element segregation caused the opposite direction of grain boundary migration, resulting in a random texture.     

Studies of deformation mechanisms in ultra-fine-grained and nanostructured Zn

The temperature, strain rate, grain size and grain size distribution effects on plastic deformation in ultra-fine-grained (UFG) and nanocrystalline Zn are systematically studied. The decrease of ductility with the decrease of average grain size could be an inherent effect in nanocrystalline materials, that is, not determined by processing artifacts. The superior ductility observed in UFG Zn may originate from both dislocation creep within large grains and grain boundary sliding of small nanograins. The stress exponent for dislocation creep is about 6.6. The activation energy for plastic deformation in UFG Zn is close to the activation energy for grain boundary self diffusion in pure Zn.     

Grain Boundary Responses to Heterogeneous Deformation in Tantalum Polycrystals

The evolution of heterogeneous deformation in a tantalum polycrystal was examined during a three-point bending experiment using electron backscatter pattern mapping. Slip bands formed at strains as low as 1%, and they became more intense with strain. Heterogeneous deformation was evident as intragranular orientation gradients as large as 30° were observed after a strain of about 8%. Nonmonotonic changes in the local average misorientation distribution were observed, implying that dislocation substructure developed in a complex manner. Slip bands were analyzed using plane traces computed from local orientation information. With the assumption of uniaxial stress, Schmid factors for favorable slip systems were identified for each grain and compared with observations, showing evidence for macroscopic activity on both {110} and {112} slip systems. Reconstructed boundary data were used to estimate the geometric potential for slip transfer at grain boundaries. The correlations indicated that when active slip systems were favorably oriented for slip transfer across the boundary, it was often observed in the form of continuous slip bands aligned across the boundary. In boundaries where geometrical alignment and Schmid factors were not favorable for slip transfer, there was a higher likelihood to form ledges (topographic discontinuities) along the grain boundaries. Dislocation pileups at grain boundaries were also correlated with a low potential for slip transfer.     

一种5083铝合金中晶界面热轧织构的研究

通过电子背散射衍射技术,测定了一种5083铝合金中的热轧织构。结果表明：在结构中的不同位置,织构组分呈现非均匀发展的特点,特别地,晶界面亦呈现取向织构。在样品的中心位置,晶界面趋向于{111}取向,且其数量高出随机晶界50%;同时,在样品的边缘位置,晶界面趋向于{110}与{112} 取向,且其数量高出随机晶界28%。更具体地,小角和大角晶界中均呈现这种晶界面的各向异性分布。     

Cold-rolling and recrystallization textures of a nano-lamellar AlCoCrFeNi2.1 eutectic high entropy alloy

The development of texture during cold-rolling and recrystallization was investigated in a AlCoCrFeNi_2.1 eutectic high entropy alloy (EHEA). For this purpose, the as-cast alloy was cold-rolled to 90% reduction in thickness and annealed at temperatures ranging from 800 °C to 1200 °C. The microstructure of the as-cast EHEA showed a nano-lamellar mixture of L1₂ and B2 phases. The B2 phase was significantly harder than the L1₂ phase. Development of an ultrafine microstructure was observed after 90% cold-rolling. During cold-rolling, progressive disordering of the L1₂ phase was observed while the B2 phase maintained the ordered structure. The progressive disordering and development of a predominantly brass type texture in the L1₂ phase correlated well with profuse shear band formation during cold-rolling. The B2 phase showed the presence of the {111}<110> component which was typical for cold-rolled B2 alloys. An ultrafine duplex structure of equiaxed L1₂ and B2 phases developed after complete recrystallization that showed significant resistance to grain growth up to very high annealing temperatures (∼1300 °C). The remarkable resistance to grain growth compared to conventional or even other single or dual phase HEAs was due to the formation of a homogeneous duplex structure where growth of one phase was effectively retarded by the other phase. The strong presence of the α-fiber components, but weak BR ({236}<385>) and D ({113}<332>) components in the recrystallization texture of the L1₂/FCC phase was due to the absence of strong preferential nucleation or growth. Presence of ND-fiber (ND//<111>) with strong {111}<011> component in the recrystallization texture of the B2 phase indicated ease of nucleation from similarly oriented regions in the deformed microstructure.     

Grain structure and microtexture evolution during superplastic forming of a high strength AlZnMgCu alloy

Grain structure and microstructure evolution during superplastic forming were studied on an unrecrystallized sheet of a modified 7050 superplastic alloy. A SEM-based local orientation technique was used to cover a large number of (sub)grain boundaries in combination with other metallographic techniques. The gradual boundary misorientation and microtexture evolution during superplastic forming (SPF) confirmed that a continuous evolutionary process was occurring. There was no evidence of dynamic recrystallization at the stress maximum. The fraction of high angle boundaries increased rapidly once the mean misorientation reached a critical value. These and other results suggest that both grain boundary sliding (GBS) and dislocation slip were operative initially until the stress maximum was approached, beyond which GBS was predominant. The results of quantitative orientation distribution function (ODF) analyses suggest that grain rotation, which resulted in texture randomization, became important from slightly beyond the stress maximum through most of the stress-strain curve.     

高磁感取向硅钢轧制及热处理过程中的晶界和织构演化

采用电子背散射衍射(EBSD)对不同轧制和热处理态的高磁感取向硅钢的重合位置点阵(CSL)晶界和织构进行了研究。结果表明,热轧态取向硅钢截面织构呈层状分布,表层主要为{110}<001>Goss织构,1/4厚度主要为{001}<110>立方织构、{112}<111>铜型织构和{110}<001>Goss织构,而心部则形成较强的{112}<111>铜型织构、{111}<110>形变织构和{110}<001>Goss织构;常化处理后截面织构梯度变化不明显,但中心位置{112}<111>织构向{110}<001>Goss织构转变。冷轧退火态主要织构为{110}<001>Goss织构、{112}<111>织构和{111}<110>形变织构。二次再结晶后,则生成强烈的{110}<001>Goss织构。随着织构的变化,CSL晶界也发生了明显的转变。热轧态CSL重位晶界中∑3~∑29均有出现,但比例较低;常化处理后CSL重位晶界比例增加,冷轧退火后CSL晶界比例大幅提高,特别是∑3、∑7、∑9和∑15等晶界;二次再结晶后,由于CSL晶界发生了转化,CSL晶界类型减少,∑3、∑13等晶界比例增加,∑9晶界消失。