Effect of precipitation on the evolution of cube recrystallisation texture

Benum, Steinar; Nes, E.

doi:10.1016/s1359-6454(97)00157-2

Cited by 60 publications

(26 citation statements)

References 10 publications

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“…4 stronger than the cube orientation. It is known that the P-component develops when rolled aluminum alloy sheets including hard particles are annealed [2,5,9,19,20]. Fig.…”

Section: Resultsmentioning

confidence: 99%

“…Over forty years much effort has been directed toward defining the critical parameters which control the recrystallized structure of binary aluminum alloys containing dispersions of intermetallic compounds [1][2][3][4][5][6][7][8][9][10][11][12][13][14][15]. In the annealing of a material containing second phase particles, the interaction between precipitation and recrystallization controls the annealing mechanism.…”

Section: Introductionmentioning

confidence: 99%

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The effect of precipitation on the evolution of recrystallization textures in an AA 8011 aluminum alloy sheet

Ryu

Lee

2001

Met. Mater. Int.

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The texture of an AA 8011 aluminum alloy sheet cold rolled by 95% showed a typical β-fiber, which runs from the copper orientation [C={112}<111>] over S [{123}<634>] to brass [B={011}<112>]. The development of annealing textures depended on annealing temperatures due to the interaction between precipitation and recrystallization. Upon annealing at a low temperature of 275 o C, precipitation took place before recrystallization. This led to a weak recrystallization texture consisting of {011}<122>, {001}<100>, and {hk0}<001>, among which the {011}<122> orientation developed near large FeAl 3 particles as the main orientation and the cube [{001}<100>] orientation originating from the matrix was relatively weak. After annealing at 350 and 500 o C, a strong cube texture developed along with a weak {011}<122> orientation. When the cube orientation developed, the copper orientation disappeared most rapidly. These results were discussed based on the interaction between precipitation and recrystallization.

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“…4 stronger than the cube orientation. It is known that the P-component develops when rolled aluminum alloy sheets including hard particles are annealed [2,5,9,19,20]. Fig.…”

Section: Resultsmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

The effect of precipitation on the evolution of recrystallization textures in an AA 8011 aluminum alloy sheet

Ryu

Lee

2001

Met. Mater. Int.

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“…In estimating P D and P Z , respectively, according to Equation (2), we use γ GB = 0.3 Jm´2 [32] and γ SB " Gbθ 4πp1´vq lnˆe θ c θ˙= 0.15 Jm´2 (assuming an average misorientation angle of θ~4a nd θ c~1 5˝), G = 26.5 GPa, b = 2.86 Å together with relevant data from Tables 4 and 6 with…”

Section: Discussionmentioning

confidence: 99%

“…Moreover the equivalent circle diameter (CED) is used for the sub-grain size. Following [32], the contribution from cell interior dislocations can be ignored as it represents only a small contribution to the stored energy at the onset of recrystallization (typically 1%-2% [32]). The results are presented in Table 7, where values marked with an asterisk refer to artificially changed input parameter values to highlight how the stored energy and the Zener drag may influence the result.…”

Section: Discussionmentioning

confidence: 99%

The Influence of Processing Conditions on Microchemistry and the Softening Behavior of Cold Rolled Al-Mn-Fe-Si Alloys

Wang

Huang

et al. 2016

Metals

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Using different homogenization treatments, different initial microchemistry conditions in terms of solid solution levels of Mn, and number densities and sizes of constituents and dispersoids were achieved in an Al-Mn-Fe-Si model alloy. For each homogenized condition, the microchemistry and microstructure, which further change both during deformation and subsequent annealing, were quantitatively characterized. The influence of the different microchemistries, with special focus on different particle structures (constituents and dispersoids), on the softening behavior during annealing after cold rolling and the final grain structure has been systematically studied. Time-Temperature-Transformation diagrams with respect to precipitation and recrystallization as a basis for analysis of the degree of concurrent precipitation during back-annealing have been established. Densely distributed fine pre-existing dispersoids and/or conditions of significant concurrent precipitation strongly slows down recrystallization kinetics and lead to a grain structure of coarse and strongly elongated grains. At the lowest annealing temperatures, recrystallization may even be completely suppressed. In conditions of low number density and coarse pre-existing dispersoids, and limited additional concurrent precipitation, recrystallization generally results in an even, fine and equi-axed grain structure. Rough calculations of recrystallized grain size, assuming particle stimulated nucleation as the main nucleation mechanism, compare well with experimentally measured grain sizes.

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“…It has been reported that the interaction between precipitates and grain boundaries, i.e., Zener pinning, retards recrystallization by hindering nucleation and obstructing the growth of recrystallized grains. [13,[15][16][17] It has been found that fine precipitates of the transition elements (Cr, Mn) inhibit recrystallization in aluminum alloys. [18,19] Therefore, the significant concurrent precipitation that occurred during recrystallization of the CC AA5052 hot band is a major factor that caused the more difficult recrystallization of the CC AA5052 hot band.…”

Section: A Recrystallizationmentioning

confidence: 99%

Comparison of the texture evolution of direct chill and continuous cast AA5052 hot bands during isothermal annealing

Zhang

Morris

2005

Metall Mater Trans A

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As-received commercial direct chill cast (DC) and continuous cast (CC) AA5052 hot bands were isothermally annealed at different temperatures. The variations of electrical resistivity, hardness, microstructure, and texture of these hot bands during annealing were examined. Texture was investigated by X-ray diffraction. The variation in texture volume fractions with annealing time was quantitatively analyzed by the Johnson-Mehl-Avrami-Kolmogorov (JMAK) equation. The orientation maps of the partially and fully recrystallized samples were characterized by electron backscattered diffraction (EBSD). It was found that electrical resistivity of the CC AA5052 hot band was higher than that of the DC AA5052 hot band. The electrical resistivity of CC AA5052 decreased more significantly than that of DC AA5052 during isothermal annealing. The DC AA5052 hot band was more easily recrystallized than CC AA5052 hot band during annealing. After complete recrystallization, DC AA5052 hot band possessed a stronger cube texture than the CC AA5052 hot band. The texture evolutions of DC and CC AA5052 can be expressed quantitatively by the JMAK equation after the volume fractions of the texture components are calculated by an improved integration method. Annealing temperature had an influence on the n values in the JMAK-type equations. The n values are small at low annealing temperatures.

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Effect of precipitation on the evolution of cube recrystallisation texture

Cited by 60 publications

References 10 publications

The effect of precipitation on the evolution of recrystallization textures in an AA 8011 aluminum alloy sheet

The effect of precipitation on the evolution of recrystallization textures in an AA 8011 aluminum alloy sheet

The Influence of Processing Conditions on Microchemistry and the Softening Behavior of Cold Rolled Al-Mn-Fe-Si Alloys

Comparison of the texture evolution of direct chill and continuous cast AA5052 hot bands during isothermal annealing

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