Mechanisms of Dynamic Recrystallization in Aluminum Alloys

Kaibyshev, Rustam; Malopheyev, Sergey

doi:10.4028/www.scientific.net/msf.794-796.784

Cited by 46 publications

(25 citation statements)

References 22 publications

(112 reference statements)

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“…This volume fraction of grains was deemed to be the ''recrystallized'' fraction [12]. Transmission electron microscope (TEM) was applied to examine crystallographic aspects of the deformation structure [3,8,9] and shear bands. In addition, TEM was used for microstructural characterization on the microscale level of the structural elements with inter-boundary spacing of less than *1 lm.…”

Section: Methodsmentioning

confidence: 99%

“…2, 3, 4, 5. Over the mesoscale at e * 1, coarse deformation bands evolve aligned with the SP [1,8,9,19,20] (see Fig. 2a).…”

Section: Microstructural Evolution In the Quenched Alloymentioning

confidence: 96%

“…3D arrays of LABs evolve through the intersection of GNBs appearing in non-coplanar slip planes [8,9] or rearrangement of lattice dislocations by climb [2, 4,12]. Next, in Stage II, these boundaries are gradually transformed into HABs at a relatively high rate due to the continued occurrence of dislocation slip within the individual domains [2, [8][9][10][11]. The dispersion of a secondary phase and solutes may affect both the generation of GNBs in the early stages of ECAP, the formation of 3D network of LABs and their transformation to HABs.…”

Section: Introductionmentioning

confidence: 99%

“…In aluminum alloys, the formation of geometrically necessary boundaries (GNB), which are initially low-angle in nature, occurs during Stage I [2, 4,[8][9][10][11]. 3D arrays of LABs evolve through the intersection of GNBs appearing in non-coplanar slip planes [8,9] or rearrangement of lattice dislocations by climb [2, 4,12]. Next, in Stage II, these boundaries are gradually transformed into HABs at a relatively high rate due to the continued occurrence of dislocation slip within the individual domains [2, [8][9][10][11].…”

Section: Introductionmentioning

confidence: 99%

“…The formation of stable three-dimensional (3D) arrays of deformation-induced lowangle boundaries (LABs) is followed by their gradual transformation into high-angle grain boundaries (HABs) [2]. In aluminum alloys, the formation of geometrically necessary boundaries (GNB), which are initially low-angle in nature, occurs during Stage I [2, 4,[8][9][10][11]. 3D arrays of LABs evolve through the intersection of GNBs appearing in non-coplanar slip planes [8,9] or rearrangement of lattice dislocations by climb [2, 4,12].…”

Section: Introductionmentioning

confidence: 99%

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The effect of second-phase particles on grain refinement during equal-channel angular pressing in an Al–Cu–Mg–Ag alloy

2014

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In this work, the effect of second-phase particle distributions on grain refinement during equal-channel angular pressing (ECAP) was studied at 250°C by comparing the microstructural evolution in an Al-Cu-Mg-Ag alloy processed in three different states. The first state (QA) was obtained by water quenching, and the second state was obtained by overaging at 250°C. Both these states contain fine dispersions of X-phase shearable plates with coherent and/or semi-coherent interfaces. The QA plate thickness prior to ECAP was higher by a factor of four than in the OA. The third alloy (HA) contained relatively coarse non-deformable particles of thermodynamically equilibrium phases with incoherent interfaces. It was shown that distribution of the secondary phase particles strongly affects the continuous dynamic recrystallization through the initial formation of geometrically necessary boundaries (GNBs), pinning dislocations and deformationinduced boundaries. The formation of a fully recrystallized structure occurs at the highest rate in the HA material with rounded grains because of 3D networks of low-angle boundaries (LABs) evolve at e * 1 due to the concurrent formation of GNBs belonging to two families. In the QA and OA materials, the shearing of the X-phase plates with the coherent interfaces leads to the strong localization of dislocation slip and the dominant formation of one family of GNBs. Nonshearable nanoscale dispersoids hinder the formation of 3D arrays for GNBs. As a result, only a partially recrystallized structure evolves, even at strains of up to e * 12.

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