Goss Orientation Research Articles

On the influence of austenite content in orientation selectivity and shear texture evolution during hot rolling of Fe-3 wt% Si grain-oriented electrical steel

A systematic investigation of the development of shear textures during hot rolling of Fe – 3 wt% Si steel has been carried out in the present work with a special focus on the influence of austenite in preferential orientation selectivity. This orientation selectivity was anticipated owing to the fact that texture evolution during thermomechanical processing is entirely an effect of crystallographic rotations and such rotations may experience constraining effects because of surrounding austenite. The influence of austenite on shear texture evolution was studied over a range of finish rolling temperatures (FRTs). The evolution of microstructure and microtexture within the surface-subsurface zone was studied adopting EBSD. Sharp Goss orientation was observed at lower FRT, while texture intensities of Brass and Copper were observed to be high at higher FRT. Additionally, it was inferred that in the surface-subsurface zone, next to the austenite, the ease of rotation about ND contributed to the higher observed frequency of the Brass orientation despite of its overall lesser fraction as compared to Copper orientation. The less observed frequency of Copper orientation near the austenite has been attributed to the resistance offered by the austenite to its adjacent ferrite grains while rotating about TD. This constraining effect of austenite has been shown to be consistent over the entire range of studied FRTs. Moreover, it has been shown that at higher rolling temperatures, the lower constraining effect by austenite paves the way for Goss orientation formation, which acts as the precursor to the formation of Brass at the FRT.

Effect of intermediate annealing temperature and cold rolling deformation on the texture of yttrium bearing oriented silicon steel

The cold rolling and intermediate annealing process, along with the incorporation of rare earth elements, play an important role in the microstructure, texture, and inhibitors of oriented silicon steel. Currently, there is limited research on the impact of rare earth yttrium on texture evolution during the cold rolling and intermediate annealing processes. Therefore, the effects of different cold rolling deformations and intermediate annealing temperatures on the microstructure and texture of Y bearing oriented silicon steel have been studied. The experimental results demonstrate that the average grain size of the intermediate annealed plate progressively decreases with increasing the cold rolling deformation. This is because the high cold rolling deformation brings more additional dislocations and distortions, consequently enhancing the driving force for recrystallization. Observing the microstructure with various cold rolling deformation, the results show that the annealed plate with a 72 % reduction rate exhibited the highest Goss texture percentage of 4.83 %. This is because the cold-rolled sheet with a reduction rate of 72 % exhibits an abundance of Goss oriented substructures. These substructures quickly dominate the {111}<112> deformed matrix during the initial recrystallization, and promote grains nucleation and growth. As the annealing temperature increases, the driving force for the growth of recrystallized grains also increases, leading to a gradual increase in grain size. The plate annealed at 940 °C exhibits the highest percentage (4.83 %) of Goss texture. The addition of rare earth Y can lead to an increase in grain size in the intermediate annealed plate and facilitate the formation of {411}<148> texture. This is advantageous for the abnormal growth of Goss texture. The results demonstrate that a cold rolling deformation rate of 72 % and an intermediate annealing temperature of 940 °C are good for promoting abnormal growth of Goss orientation. The study results on precipitation kinetics suggests that the grain boundary nucleation of AlN and dislocation nucleation of MnS are the most effective way of nucleation. The precipitates in oriented silicon steel without Y are Al2O3 and MnS, while those in the samples with Y are AlN, YS, and YOxSy. The addition of rare earth Y leads to a reduction in both the density and size of precipitates. Moreover, With the increase of annealing temperature, the size of precipitates decreases and the amount of precipitates increases. Additionally, the addition of Y makes the steel more clean, meanwhile, the pinning effect of inclusions on grain boundaries is weakened. Therefore, the grain size of the steel with Y is larger.

Machine Learning-Aided Analysis of the Rolling and Recrystallization Textures of Pure Iron with Different Cold Reduction Ratios and Cold-Rolling Directions.

We performed a machine learning-aided analysis of the rolling and recrystallization textures in pure iron with different cold reduction ratios and cold-rolling directions. Five types of specimens with different cold reduction ratios and cold-rolling directions were prepared. The effect of two-way cold-rolling on the rolling texture was small at cold reduction ratios different from 60%. The cold reduction ratio in each stage hardly affected the texture evolution during cold-rolling and subsequent short-term annealing. In the case of long-term annealing, although abnormal grain growth occurred, the crystal orientation of the grains varied. Moreover, the direction of cold-rolling in each stage also hardly affected the texture evolution during cold-rolling and subsequent short-term annealing. During long-term annealing, sheets with the same cold-rolling direction in the as-received state and in the first stage showed the texture evolution of conventional one-way cold-rolled pure iron. Additionally, we conducted a machine learning-aided analysis of rolling and recrystallization textures. Using cold-rolling and annealing conditions as the input data and the degree of Goss orientation development as the output data, we constructed high-accuracy regression models using artificial neural networks and XGBoost. We also revealed that the annealing temperature is the dominant factor in the nucleation of Goss grains.

Experimental characterization and crystal plasticity finite element simulation of the microstructural evolution in CVD tungsten during multi-step rolling

Atmospheric pressure chemical vapor deposition (CVD) is a promising technique for the preparation of tungsten products with high purity, high density and almost unlimited thickness. The tungsten prepared by using the CVD method (CVD-W) usually has a columnar coarse grain microstructure with strong preferred orientations. Multi-step rolling at gradually decreased operating temperatures is an effective method to lower the ductile-to-brittle transition temperature in pure tungsten. So far, the microstructural evolutions of CVD-W during the multi-step rolling processing is still unclear. In this study, the microstructure evolution and texture development of CVD-W during multi-step rolling are investigated by the coupling of electron backscattering diffraction technique and full-field crystal plasticity finite element simulations. After multi-step rolling, the sample exhibits through-thickness texture gradient. A layered structure with elongated 〈100〉 // ND and 〈111〉 // ND grains is observed in the central region and Goss orientation mainly appears in the surface region. Crystal plasticity finite element simulations show that {001}〈110〉 is a stable orientation under the plane strain compression, which is realized by the rotation of {100} grains around ND. Meanwhile, the shear flow promotes the rotation of {100} grains around TD, leading to the formation of 〈111〉 // ND orientation. 〈110〉 // ND orientation is observed near the shear bands, which is generated through the rotation of {100} grains around <100> // RD axis. The rolled CVD-W exhibits crystallographic orientation dependent recrystallization behavior, which is related to the orientation dependent distortion energy generated in the rolling processing. Our studies provide fundamental insights into the microstructure evolution and texture development of CVD-W under the multi-step rolling processing.

Texture evolution and stress formation behaviour during tensile deformation using crystal plasticity finite element method

In this work, a three-dimensional crystal plasticity (CP) model was constructed to study the texture evolution behaviour and stress distribution of AA2024 alloy under uniaxial tensile conditions. After parameter calibration, the accuracy of simulated stress–strain curve reached 98.82%, and with good convergence. It was found that the {111} plane dots of Brass in (111) pole figure predominantly prolong at an angle of approximately 35.8° with respect to the RD, while those of Copper, S, Goss and Cube scatter towards almost all directions by the way in a circular augmentation. Moreover, it was revealed that Brass orientation is more conducive to alleviating stress during deformation process, while Copper is the least effective. The situations for Cube and Goss orientations are similar.

Cross slip based dynamic recovery during plane strain compression of aluminium and its role in preferential nucleation of the cube-oriented recrystallized grains

Understanding nucleation of the cube-oriented grains during static recrystallization of medium to high stacking fault energy (SFE) FCC metals is both scientifically and industrially important. Dynamic recovery due to weak Hirth junctions is considered as one of the plausible explanations for the nucleation advantage of the cube orientation. However, influence of cross slip based dynamic recovery on the nucleation propensity of the cube orientation has not been studied in detail. For this purpose, we explicitly incorporated stress dependent dynamic recovery of screw dislocations into a dislocation density based crystal plasticity model. The model is utilized for studying influence of cross slip based local dynamic recovery during deformation and recrystallization nucleation of aluminium. We show that dynamic recovery influences local dislocation density difference and disorientation with the neighbouring locations for the main rolling texture components. Next, we analysed nucleation propensity of these texture components using a stochastic nucleation model. Simulation results show that without explicit incorporation of the dynamic recovery of screw dislocations, the Goss orientation shows the highest nucleation propensity. On the other hand, incorporation of the cross slip based dynamic recovery enhances nucleation propensity of the cube component. Therefore, cross slip based dynamic recovery is one of the important mechanisms for nucleation of the cube-oriented recrystallized grains. These results provide new insights into deformation and recrystallization nucleation of medium to high SFE FCC metals.

EFFECT OF COLD ROLLING PROCESS ON TEXTURE EVOLUTION IN AUSTENITIC STEEL SHEETS

The investigation presents the evolution of texture and microstructure of cold-rolled austenitic AISI 301 stainless steel sheets. The austenite steel was deformed by cold-rolling to 30%, 50% and 80% of rolling reduction. It was found, that during cold plastic deformation, phase transformation of austenite into martensite takes place. The transformation progress was confirmed by the microscopic investigation, as well as by X-ray diffraction methods. Texture analysis was performed on the basis of the orientation distribution functions (ODFs) calculated from the experimental pole figures. The texture of the deformed austenite is dominated by fiber orientations α =110║KN, mainly Goss orientation {110}001 and alloy type orientation {110}112. On the other hand, plastic deformation-induced martensitic transformation of the type (γ') significantly affects the development of martensite texture ' in the cold rolling process. After rolling with a 30% of deformation degree in the texture of  martensite, the strongest orientation is {001}110, while after maximum deformation (about 80%), the {111}112 and {112}110 type orientations dominate. It was found that in AISI 301 steel structure after deformation range from 30% to 80% proportion of α’ martensite phase changes from about 26.7% to about 67.8%.

Simulation and Microstructural Analysis of Twin-Induced Plasticity Steel Cylinder Deep Drawing.

This study investigated the stress-strain behavior and microstructural changes of Fe-Mn-Si-C twin-induced plasticity (TWIP) steel cylindrical components at different depths of deep drawing and after deep drawing deformation at various positions. The finite element simulation yielded a limiting drawing coefficient of 0.451. Microstructure and texture were observed using a scanning electron microscope (SEM) and electron backscatter diffraction (EBSD). The research revealed that the extent of grain deformation and structural defects gradually increased with increasing drawing depth. According to the orientation distribution function (ODF) plot, at the flange fillet, the predominant texture was Copper (Cu){112}<111> orientation; at the cylinder wall, the main textures were Copper Twin (CuT) and Goss (G) orientations; at the rounded bottom corner of the cylinder, the primary texture was τ-fiber (<110>//TD), with its strength increasing with deeper drawing.

A Study on the Formation of Fiber Texture in the Subsurface Layer of Hot-Rolled Plate of 3.2%Si Grain-Oriented Steel

During the hot rolling process, inhomogeneity microstructure and variations of texture along the thickness direction of hot-rolled plate were formed through shear deformation and recrystallization. The purpose of this study is to investigate the formation and evolution of fiber texture in hot-rolled plate of grain-oriented silicon steel. The results indicate that, in the surface layer s = 1 of hot-rolled plate, a large number of equiaxed grains are formed under high shear force. Under the surface layer, as shear force gradually decreases along the thickness direction, the grain aspect ratio of recrystallized grains gradually increases along the thickness direction of hot-rolled plate, and the shape of the recrystallized grains formed in the subsurface layer and center layer becomes more irregular along the thickness direction. Under the combination of compressive force and decreasing shear force along the thickness direction, fiber texture composed of dozens of specific orientations (such as {112}&lt;111&gt;, {110}&lt;112&gt;, {213}&lt;364&gt;, {441}&lt;104&gt; and Goss orientations) is formed in the subsurface layer s = 0.5~0.9 and gradually evolves along the thickness direction. Therefore, the formation of Goss texture is a small part of fiber texture and is the result of texture evolution in the subsurface layer s = 0.5~0.9.

Comprehensive study on the through-process Goss texture evolution in Fe-3.78 wt.%Si grain oriented electrical steel

Cold rolled grain oriented steel is used in transformer cores due to its superior magnetic properties. Large Goss oriented grains develop after the final secondary recrystallization provide low hysteresis loss. The present study represents the development of Goss orientation after each processing stage of Fe-3.78 wt% Si steel with the help of electron backscatter diffraction and x-ray diffraction techniques. The Goss oriented grains developed during hot rolling and hot band annealing did not remain stable in cold rolling. On the other hand, shear bands developed inside {111}<112> component of γ-fiber texture during cold rolling. Partial recrystallization of the cold rolled sheet revealed that Goss oriented grains started evolving inside the shear bands of {111}<112> oriented grains. Intermediate annealing between cold rolling passes was found to be not essential to achieve Goss orientation in primary recrystallization. The optimum primary recrystallization temperature was in between 923 and 948 K where a significant amount of Goss oriented grains were present. Further, secondary recrystallization was attempted at different temperatures between 1173 and 1473 K. Grain boundary curvature of Goss oriented grains and all other grains after both primary and secondary recrystallization was studied. Despite the percentage of convex boundaries surrounding Goss oriented grains was found slightly higher than that around other grains, it was insufficient to cause abnormal grain growth.

Effects of material combination for ultrasonic spot welding on microstructure and strength of Al/Al, Al/Cu, and Al/Ni dissimilar joints

The dissimilar joining of Al/Cu and Al/Ni is required to reduce the weight of electronic and electrical devices. Ultrasonic spot welding (USW) is expected to be applied to dissimilar materials because of the low heat input during the joining process. However, to obtain high strength via USW, the relationship among the welding parameters, joining strength, and microstructure for different material combinations must be investigated. In this study, Al/Al, Al/Cu, and Al/Ni are joined via USW by systematically varying the welding parameters; subsequently, their tensile shear load and microstructure are investigated. Results show that the vibration amplitude and welding time impose greater effects on the joint strength than the welding pressure for all material combinations. High-strength joints that fractured at the Al upper plate are obtained by optimizing the welding parameters for each material combination. Al/Ni bonding had a narrower margin of welding time to obtain a higher tensile shear load compared with other material combinations. This is due to the high heating rate and maximum temperature of Al/Ni joints, which cause the excessive deformation of the Al upper plate during prolonged welding. Texture analysis showed that recrystallized grains with GOSS orientation was remained in the high-strength dissimilar joints.

Effect of Mg/Si Ratio on the Bendability and Anisotropic Bend Behavior of Extruded 6000-Series Al Alloy.

Extruded Al-Mg-Si profiles applied in the automotive industry are required to achieve an appropriate combination of strength and bendability. In order to investigate the effect of Mg/Si ratio on the bendability and anisotropic bending behavior, AA6005 and AA6061C were extruded to 2 mm thick plates. More Goss texture and anisotropic particle clusters exist in AA6005 alloys with a low Mg/Si ratio, which leads to a high tendency of surface roughing and cracking and to strong anisotropy in their bendability. However, more low-angle grain boundaries, cubic texture and comparatively random distribution of particles exists in AA6061C alloys with a high Mg/Si ratio, which blunts the surface roughing and crack process. The surface undulation is the outcome of the strain-intense localization of several layers of grains in the vicinity of the outer elongated surface. The strain localization and surface undulation lead to shear band initiation near the valleys. Several cooperating micro-mechanisms in AA6005, including grain clusters with Goss and Cubic orientation, heterogeneously nucleated particles and grain boundary spatial arrangements, lead to the grain boundary decohesion along a shear direction. AA6005 shows for predominately intergranular fractures in nature, with some areas exhibiting grain boundary decohesion during bending in the TD. However, AA6061C shows a predominately transgranular in nature, with some areas exhibiting intergranular fracture, which is affected by shear band development.

Formation of recrystallization texture and its effect on deep drawability for high-purified ferritic stainless steel by two step cold rolling

For working out the approach of acquiring low planar anisotropy while achieving high ridging resistance and r-value, during two step cold rolling processes with different total reductions the texture evolution and corresponding mechanism were investigated for ferritic stainless steel. During cold rolling, the crystallites having orientations near {111} 〈112〉 and Goss were induced by shear bands and with further deformation Goss orientation tended to rotate towards more stable {111} 〈112〉. During subsequent annealing, these crystallites induced the recrystallized nuclei and {111} 〈112〉 nuclei consumed preferentially the adjacent matrixes, generating the γ-fiber recrystallization texture having the main component of {111} 〈112〉. With increasing total cold rolling reduction, the γ-fiber recrystallization textures were gradually intensified and band-like grain colonies having approximate r-value and those having variant with ε23 of same sign became more obvious and their distribution more uneven, the average r-value and ridging resistance exhibited a monotonous upward and downward trend, respectively, and the planar anisotropy of r-value first deteriorated and then improved and reached lowest value at 90 %. Considering acceptable ridging resistance in practical application, the excellent deep drawability can be acquired at the total reduction of 90 %.

In-situ observation of microstructure and orientation evolution of the Cu–Cr–Zr-Hf alloys

The roles of Hf element in the mechanical properties, deformation mode and orientation evolution of the Cu-0.4Cr-0.2Zr-0.2Hf (wt.%) alloys were investigated using both ex-situ and in-situ electron backscatter diffraction (EBSD). The results indicate that the trace Hf element (0.2 wt%) addition into the Cu–Cr–Zr alloys motivates the multiple slip activities. The activation of multiple slip systems indirectly or directly influences the tensile strength, strain distribution and lattice rotation. Firstly, it promotes the generation of dislocations, and thus enhances the work hardening rate, contributing to the improvement of the ultimate tensile strength. Secondly, it inhibits the movement of dislocations to the grain boundaries, and thus hinders the strain localization at the grain boundaries, promoting the homogeneous deformation. Thirdly, the interaction between dislocations on different slip systems restricts the intragranular lattice rotation, leading to the high stability of the grains with Goss orientation in the Cu–Cr–Zr-Hf alloys. The mutual transform between the R-CubeRD orientation and Goss orientation is also observed. This study deepens the understanding of deformation mechanisms and texture evolution of the Cu–Cr–Zr-Hf alloys.

Biaxial deformation behaviour of duplex stainless steels: Experiments and crystal plasticity based stress predictions

Biaxial tensile tests are performed on two phase duplex stainless steel using a newly developed multiaxial testing rig integrated with a digital image correlation mapping facility. A cruciform-shaped specimen geometry is subjected to equibiaxial tensile (EBT) loading, and the load–strain response is captured. Unlike uniaxial tensile testing, a well-defined gauge area is absent in biaxial specimens; hence, stress cannot be estimated directly. Finite element analysis is used to calculate the stress state. The phenomenological finite element model failed to capture the inherent anisotropy of the material; hence, a crystal plasticity finite element based method is used to estimate the stresses. It is observed that the 0.2% proof stress increased, but the strain to failure remained constant in comparison with uniaxial tensile properties. The work hardening behaviour is isotropic similar to that observed during uniaxial testing. The goss and rotated goss orientations in austenite accommodated most of the strain along RD and TD, respectively. During EBT, the change in austenite and ferrite textures is minimal and similar to their single phase counterparts reported in the literature. The EBT test results indicate that the influence of micromechanical interactions between the phases on the work hardening behaviour and texture evolution is weak.

Experimental analysis of deformation texture evolutions in pure Cu, Cu-37Zn, Al-6Mg, and −8Mg alloys at cold-rolling processes

Generally, two types of deformation textures of copper-type and brass-type textures are evolved in face-centered cubic (FCC) metals. During deformation, dislocation motion determines which texture will be dominant. The copper-type texture is formed in metals of high stacking fault energy by cross-slip of dislocations and subsequent dislocation cell formation. On the other hand, deformation twinning involves the brass-type texture evolution, whereas some exceptions, such as Al-Mg alloys, also have been reported. This study examined deformation texture evolutions in four cold-rolled FCC alloys of pure Cu, Brass (Cu-37Zn), Al-6Mg, and Al-8Mg alloys. Electron backscattered diffraction and X-ray line profile analysis methods investigated the deformation texture evolution. Three different strains of 0.25, 0.45, and 0.63 were applied to observe the strain effect on texture evolution. In pure Cu, the copper-type texture is developed, as commonly known. The brass-type texture is developed in Brass and Al-Mg alloys. More reduction ratios in those alloys lead to the copper-type texture strengthening in pure Cu, whereas stronger brass-type texture is shown in Brass and Al-Mg alloys by applying more reduction. While the brass-type texture evolution in Brass can be illustrated by deformation twinning, deformation twins are absent in deformed Al-Mg alloys despite their evident brass-type texture formation. Instead, the short-range ordering (SRO) mechanism can explain the brass-texture evolution in Al-Mg alloys. Planar slips by the high Mg content of Al alloys strengthen the rotated Goss orientation with brass-type texture evolution after cold-rolling processes of those alloys.

Microstructure and texture evolution of ultra-thin high grade non-oriented silicon steel used in new energy vehicle

The evolutions of microstructure and texture of ultra-thin high-grade non-oriented silicon steel for new energy vehicles were investigated in this paper, and the formation mechanism of typical recrystallized α*-fiber texture was described. The results show that: The microstructure of the hot rolled plate was inhomogeneous along the thickness direction because of the shear force and temperature gradient, resulting in the texture in each layer of the hot rolled plate appearing rotational distribution around the Goss orientation. After normalizing, the fully recrystallized microstructure was obtained, and α*-fiber texture was formed. Banded structure was obtained in the cold rolled sheet, with α-fiber texture {114}〈110〉 dominated. The typical α*-fiber texture was formed after annealing recrystallization, which mainly consist of {114}<481 > and {113}<361>. The {114}<481 > oriented grains were mainly nucleated within the deformed {114}<110 > grains and at the grain boundaries of α-fiber deformed grains, and without size, quantity and strength advantages. {111}<112 > is dominated in the early stage of recrystallization, but {114}<481 > became the main texture with size, strength and quantitative advantages in the late stage of recrystallization.

The effect of temper rolling and final annealing on microstructure, texture and magnetic properties of non-oriented electrical steels

In this paper, the effect of temper rolling and final annealing on microstructure, texture and magnetic properties of a 0.6 wt% Si non-oriented electrical steel, with 5.7% temper rolling reduction, were investigated via EBSD and XRD three-dimensional orientation distribution function (ODF) analysis. The results indicate that final annealing plays an essential role in improving the magnetic properties of non-oriented electrical steels. The core loss decreases with the increasing annealing time, reaches the lowest value at 10 min, and then tends to be stable. The magnetic induction quickly increased with prolonged annealing time, reached the highest value, then decreased slightly to a lower value after 15 min. The peak permeability increased rapidly with the increasing annealing time, reached the highest value after 3 min, and became stable after 10 min. The grains abnormally develop from the sample surface to the inner layer derived from gradient strain. Before and after temper rolling, the texture of the material is mainly dominated by {111}<112>. As annealing time increases, the intensity of {111}<112> decreases, emerging the weak Goss ({110}<001>) and other orientations. Finally, there are without preferred orientations when time exceeds 10 min.

Effect of Recovery Annealing Prior to Recrystallization Annealing on the Texture Evolution of a 3.3% Silicon Steel

Non‐oriented silicon steels containing 0.006 wt% C and 3.3 wt% Si are cold‐rolled, recovery, and recrystallization annealed. The microstructure and texture evolution are analyzed using optical microscopy, X‐ray diffraction, and electron backscatter diffraction. In the samples with recovery annealing, strong {021}&lt;100&gt;, {332}&lt;uvw&gt;, and some Goss orientations and λ‐fiber (&lt;001&gt;//normal direction [ND]) are observed, which differs from the texture of non‐oriented silicon steel processed by the cold‐rolling and the subsequent recrystallization annealing. It is shown that the recovery annealing has an obvious effect on the texture evolution during the subsequent recrystallization annealing. The nucleation and growth of the grains with {021}&lt;100&gt;, {332}&lt;uvw&gt;, and λ orientations are promoted, while the typical γ‐fiber (&lt;111&gt;//ND) is dramatically weakened. The results of this study may offer some new ideas for the treatment process for non‐oriented silicon steel.

Statistical analysis of misorientation to goss orientation of highly grain-oriented silicon steel

Grain-oriented (GO) steel is primarily used as a core material for transformers. For better magnetic performance, the high selectivity to the exact {110} 〈001〉 orientation has been a target for GO steel. Commercially available high-grade of GO steel consists of grains with a misorientation <3° from the {110} 〈001〉 orientation. However, the magnetic properties of the commercial GO steel implies that the GO steel should contain grains with larger deviation angles. As GO steel has much larger grains (diameters of several centimeters) than low-carbon steel, the conventional microscopy method used to measure the orientations of the grains is not suitable for GO steel. In this study, Laue diffraction was used to analyze the orientation of large grains of HI-B GO (HGO) steel to obtain statistically reliable topological data and characterize the grain boundaries between abnormally grown grains. The measured area was 6300 cm2, which contained 1230 grains. The analyzed HGO steel sheet had 1/3 of the grains with orientations close to an exact Goss orientation, which was defined as a range of orientations with a misorientation angle <5°, and 2/3 of the grains with higher misorientation to the Goss orientations. The topological and grain-boundary characteristics of the grains based on the misorientation to the exact Goss orientation are discussed in detail.