Role of {110}<111>, {112}<111>, and {123}<111> slip systems for BCC alloy texture evolution
The development of crystallographic texture during rolling of BCC alloys and metals is fundamentally governed by the activation of specific slip systems, predominantly of the {110}〈111〉, {112}〈111〉, and {123}〈111〉 families. Unlike FCC metals where slip occurs preferentially on close-packed {111} planes, BCC metals exhibit a temperature- and strain-rate-dependent slip behavior due to the non-close-packed nature of their lattice. At low to moderate temperatures, the critical resolved shear stress (CRSS) on these three slip families is of comparable magnitude, leading to co-activation and a characteristic rolling texture evolution that is distinct from the copper-type texture observed in FCC systems.
Simulation of rolling textures of b.c.c. metals considering grain interactions and crystallographic slip on {110}, {112} and {123} planes
The rolling textures of b.c.c. transition metals are simulated using a Taylor-type model which takes into account grain interactions and allows for the activation of dislocation slip on {110}, {112} and {123} glide planes. Whereas in the relaxed constraints Taylor models some strain constraints are dropped, in the grain interaction approach the degree of shear strain relaxation depends on the resulting gain in deformation energy. The simulations are carried out within the range ¢=0% to ¢=90%. The predicted textures are in good accord with experiment.
Mater Sc Engin A 1997 Taylor modeling st[...]
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The rolling textures of b.c.c. transition metals are simulated using a Taylor-type model which takes into account grain interactions and allows for the activation of dislocation slip on {110}, {112} and {123} glide planes. Whereas in the relaxed constraints Taylor models some strain constraints are dropped, in the grain interaction approach the degree of shear strain relaxation depends on the resulting gain in deformation energy. The simulations are carried out within the range ¢=0% to ¢=90%. The predicted textures are in good accord with experiment.
Mater Sc Engin A 1997 Taylor modeling st[...]
PDF-Dokument [679.1 KB]
The {110}〈111〉 slip systems, being the most densely packed planes in the BCC structure, are typically the first to activate at low strains and ambient temperatures.
Their activation promotes lattice rotations that stabilize orientations with the 〈110〉 direction parallel to the rolling direction (RD) and the {111} plane parallel to the rolling plane (ND). This
contributes to the formation of the α-fiber (RD∥〈110〉) and the γ-fiber (ND∥〈111〉), which are the two dominant texture components in rolled BCC metals. However, the geometric slip length and the
relatively high Schmid factors for certain grain orientations restrict {110}〈111〉 slip alone from fully explaining the observed texture sharpness.
The {112}〈111〉 slip systems become increasingly significant with higher strain or lower deformation temperatures. Their activation is critical for stabilizing the
{112}〈110〉 component along the α-fiber and for enhancing the γ-fiber component, specifically the {111}〈112〉 orientation. From a mechanistic perspective, {112}〈111〉 slip offers a lower Taylor factor
for certain grain orientations compared to {110}〈111〉 slip, thereby reducing the required external work for a given strain. This leads to a more homogeneous deformation and promotes a sharper, more
stable rolling texture. The so-called "pencil glide" mechanism—whereby the effective slip plane is not fixed but rotates to maintain the slip direction within the plane of maximum resolved shear
stress—is often approximated by the simultaneous or alternating activation of {110} and {112} planes sharing the same 〈111〉 direction.
The {123}〈111〉 slip systems, while having the lowest planar density and highest CRSS among the three, play a crucial role in texture broadening and the formation of
the weaker, yet experimentally observed, texture components. Their activation is often invoked at higher strains or elevated temperatures, where thermal activation facilitates slip on less
close-packed planes. The {123}〈111〉 systems allow additional degrees of freedom for lattice rotation, preventing the over-sharpening of the α- and γ-fibers and enabling a more diffuse transition
between them. In polycrystal plasticity models, such as the Taylor-type or viscoplastic self-consistent (VPSC) models, the inclusion of {123}〈111〉 slip is essential to correctly predict the measured
texture intensities and the slight orientation spread around the ideal fibers. Specifically, {123}〈111〉 slip facilitates the continuous rotation from the {001}〈110〉 towards the {111}〈110〉 component
along the α-fiber, a transition that cannot be accurately captured using only {110} and {112} slip.
In summary, the understanding of rolling texture evolution in BCC metals requires a multislip framework where {110}〈111〉, {112}〈111〉, and {123}〈111〉 systems
contribute synergistically. {110}〈111〉 provides the initial texture framework, {112}〈111〉 sharpens and stabilizes the primary texture fibers, and {123}〈111〉 introduces the necessary orientational
flexibility to reproduce the full experimental texture topology. The relative activity of each system is not fixed but evolves with strain, temperature, and alloy composition, dictating the final
anisotropy of mechanical properties. Consequently, any quantitative texture prediction for rolled BCC alloys must incorporate the hierarchical yet cooperative role of these three slip
families.
Rolling and recrystallization textures of bcc steels
Raabe_overview_steel_textures_01.pdf
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Raabe_overview_steel_textures_01.pdf
PDF-Dokument [767.4 KB]
Overview on Basic Types of Hot Rolling Textures of Steels
Review on basic types of crystallographic textures deve loping during hot rolling ot polycrvstatline steels.
overview_textures.pdf
PDF-Dokument [2.7 MB]
Review on basic types of crystallographic textures deve loping during hot rolling ot polycrvstatline steels.
overview_textures.pdf
PDF-Dokument [2.7 MB]
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