“…In this section, ferrite orientations, resulting from the K-S model with and without variant selection and applied to different simulated parent textures, are analyzed and compared with published experimental results [23][24][25] in order to infer the most reliable austenitic texture.…”
The phase transformation of low-carbon steels is evaluated by means of computer simulations performed with a viscoplastic self-consistent (VPSC) code. The simulations allow calculating micromechanical data at high-temperature deformation that are currently inaccessible through experiments. The micromechanical data are later on used in phase transformation computer codes to evaluate the pre-eminence of certain transformation variants following different criteria. The texture results are compared with experimental results available in the literature. The main fibers and components develop and behave differently depending on the selection of hardening laws, fragmentation criteria, active slip systems, etc. The results are compatible with high-temperature textures characteristic of a high stacking fault energy (HSFE)-like alloy and selection of variants based on the activity of the high-temperature slip systems.
“…In this section, ferrite orientations, resulting from the K-S model with and without variant selection and applied to different simulated parent textures, are analyzed and compared with published experimental results [23][24][25] in order to infer the most reliable austenitic texture.…”
The phase transformation of low-carbon steels is evaluated by means of computer simulations performed with a viscoplastic self-consistent (VPSC) code. The simulations allow calculating micromechanical data at high-temperature deformation that are currently inaccessible through experiments. The micromechanical data are later on used in phase transformation computer codes to evaluate the pre-eminence of certain transformation variants following different criteria. The texture results are compared with experimental results available in the literature. The main fibers and components develop and behave differently depending on the selection of hardening laws, fragmentation criteria, active slip systems, etc. The results are compatible with high-temperature textures characteristic of a high stacking fault energy (HSFE)-like alloy and selection of variants based on the activity of the high-temperature slip systems.
“…However, it has been reported that these techniques have certain difficulty in measuring pole figures of coarse grain materials, unpolished industrial samples, rather weak texture materials and multi-phase composite materials. [1][2][3][4][5][6][7][8] Moreover, in order to precisely predict the macroscopic properties of a steel sheet, a high-quality statistical average texture (also called as global texture or bulk texture) is more valuable than the local plane texture obtained by X-ray diffraction or EBSD. [8][9][10][11][12][13] Though different sample preparation methods have been proposed rightly to measure the bulk texture of a sheet material by X-ray diffraction, 14,15) only the reflection method is applicable.…”
{110}, {200} and {211} neutron diffraction profiles of an interstitial-free annealed steel sheet were measured on 5 Â 5 degrees stereographic angle grids, and several evaluation methods of diffraction intensity were employed to calculate the bulk texture, including the peak intensity at a constant 2theta angle, the simply summed intensity in a constant 2theta angle spread and the Gaussian integrated intensity obtained by single peak fitting of each profile. The comparison among differently evaluated bulk textures shows that a stronger f111ghuvwi fiber component and a weaker f001gh110i rotated cube component appear in the texture of investigated steel and the Gaussian integrated intensity method with proper coefficient constraints possesses a higher sensitivity to both weak texture components and strong ones. The crystallographic orientation maps obtained from electron backscattering diffraction and the bulk textures estimated from X-ray diffraction confirm the feasibility of the neutron bulk texture based on the Gaussian integrated intensity, suggesting that it can be suitably utilized to evaluate the global orientation distribution characteristics of heterogeneous materials.
“…[1][2][3][4][5][6][7] As compared with the conventional slab casting process, rapid cooling solidification processes show the merits of reducing capital and operational costs through omitting the intermediate rolling and heating installation and processing stages. Meanwhile the high cooling rate during strip-casting or thin slab casting, about 100 times higher than that of conventional slab casting, makes a quite diminished microsegregation of impurities in steels.…”
The compact strip production (CSP) technology composed of thin slab casting and direct hot rolling has attracted much attention due to its apparent cost advantage. In this paper, the microstructural and textural variations in the through-thickness direction and their effects on the plastic anisotropy gradient in a thin-slab-cast low-carbon steel are investigated by optical metallography (OM), orientation imaging microscopy (OIM), transmission electron microscopy (TEM) and quantitative X-ray texture analysis. The thin steel slab shows a relatively uniform strengthductility balance with the exception of the surface and center layers. The textures in all the through-thickness layers are composed of relatively strong {111}huvwi and weak {001}huvwi components which reach their maximum intensities in the middle layer near S ¼ 0:4 and in the center layer, respectively (S is the normalized distance from the slab center to the specific layer and S to the slab surface is 1.0). The -fiber oriented ferrite exhibits a roof-shape tendency of the average grain size variation in the through-thickness direction. The lower carbon content in the surface layer is responsible for the better normal anisotropy (r m value) even with the weakest {111}huvwi component. In spite of the relatively strong {111}huvwi component intensity in the center layer, the lowest r m value is related to the solidified shrinkage cavities and the large MnS inclusions.
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