The Influence of Crystallographic Texture on DynamicRecrystallization

Кайбышев, Р. О.; Соколов, Б. К.; Galiyev, Arthur

doi:10.1155/tsm.32.47

Cited by 21 publications

(11 citation statements)

References 10 publications

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“…They may also be related to deformation becoming localized in the dynamically recrystallized fraction of the material, brought about by the large difference between the initial and dynamically recrystallized grain sizes. This process has been observed during the hot deformation of magnesium by other researchers [2,3,19,50] and also in superplasticity studies (low strain rates). [51] In a review on DDRX, Sellars [14] notes that if the deformation conditions change within the dynamically recrystallized fraction, then further nucleation may cease in the unrecrystallized fraction.…”

Section: B Ebsd and Nucleation Mechanismssupporting

confidence: 66%

Microstructural Development during Hot Working of Mg-3Al-1Zn

Beer

Barnett

2007

Metall Mater Trans A

235

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The microstructural evolution is examined during the hot compression of magnesium alloy AZ31 for both wrought and as-cast initial microstructures. The influences of strain, temperature, and strain rate on the dynamically recrystallized microstructures are assessed. Both the percentage dynamic recrysallization (DRX) and the dynamically recrystallized grain size were found to be sensitive to the initial microstructure and the applied deformation conditions. Lower Z conditions (lower strain rates and higher temperatures) yield larger dynamically recrystallized grain sizes and increased percentages of DRX, as expected. The rate with which the percentage DRX increases for the as-cast material is considerably lower than for the wrought material. Also, in the as-cast samples, the percentage DRX does not continue to increase toward complete DRX with decreasing Z. These observations may be attributed to the deformation becoming localized in the DRX fraction of the material. Also, the dynamically recrystallized grain size is generally larger in as-cast material than in wrought material, which may be attributed to DRX related to twins and the inhomogeneity of deformation. Orientation maps of the as-cast material (from electron backscattering diffraction (EBSD) data) reveal evidence of discontinuous DRX (DDRX) and DRX related to twins as predominant mechanisms, with some manifestation of continuous DRX (CDRX) and particle-stimulated nucleation (PSN).

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Section: B Ebsd and Nucleation Mechanismssupporting

confidence: 66%

Microstructural Development during Hot Working of Mg-3Al-1Zn

Beer

Barnett

2007

Metall Mater Trans A

235

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“…13) contradict with the commonly accepted interpretation in terms of the Friedel-Escaig mechanism. On the other hand, direct topographic observations do not show any essential qualitative changes in cross-slip mechanisms at temperatures of 523 to 723 K. 29) The only effect of increasing deformation temperature is that the slip at higher temperatures appears to be considerably more homogeneous. With the magnitudes of the activation energy Q ¼ 135 kJ/mol and stress exponent n ¼ 5 this gives good grounds to suggest the transition from the cross-slip to dislocation climb controlling mechanism in the high temperature range.…”

Section: The Effect Of Solid Solution Alloying On the Changes In The mentioning

confidence: 93%

“…Differences between the structural changes occurring upon deformation of Mg and an Mg-5.8%Zn-0.65%Zr (in weight %) alloy [3][4][5] suggest that the latter may be a suitable object for such a study. Based on these data, we can a priori assume that alloying Mg with such elements as Zn decreases SFE and, hence, affects the mechanisms for plastic flow.…”

Section: Introductionmentioning

confidence: 99%

Deformation Behavior and Controlling Mechanisms for Plastic Flow of Magnesium and Magnesium Alloy

2003

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Deformation behavior of pure Mg and Mg alloy were studied in the temperature range of 423 to 773 K and at strain rates of 10 À4 -10 À2 s À1 . Three temperature regions can be categorized both in Mg and Mg alloy. The deformation behavior in Mg can be described by an exponantional law at temperatures below 523 K. At the higher temperatures a power law of deformation is valid with the stress exponent close to n ¼ 7 in the intermediate (523-623 K) and 2.2 in the high (673-773 K) temperature ranges. The alloying of Mg with elements such as Zn changes the phenomenology of plastic deformation. An exponantional law is operative at temperatures below 473 K. At above 473 K deformation obeys a power law. The stress exponent is close to n ¼ 7 at intermediate temperatures (473-523 K) and 5 in the high temperature range. An analysis of experimental results shows that alloying changes the controlling mechanisms of plastic deformation and so leads to different deformation behavior in pure Mg and Mg alloy that can be associated with decreasing stacking fault energy (SFE) in Mg alloy. The effect of SFE on the mechanisms of plastic deformation when alloying Mg is discussed.

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“…Several recrystallization mechanisms were observed to be operative in Mg alloys, namely continuous dynamic recrystallization (CDRX), discontinuous dynamic recrystallization (DDRX), twinning induced dynamic recrystallization (TDRX) and particle stimulated nucleation (PSN) [15]. DRX has been found to be strongly related to the operative slip and twinning systems [16][17][18][19][20][21][22]. Most studies agree that recrystallization occurs readily when multiple slip M A T E R I A L S C H A R A C T E R I Z A T I O N 7 5 ( 2 0 1 3 ) 1 0 1 -1 0 7 operates [16][17][18][19][20][21][22], i.e., when both basal and non-basal systems contribute to deformation.…”

Section: Introductionmentioning

confidence: 99%