The evolution of grain boundary character during superplastic deformation of an Al-6 pct Cu-0.4 pct Zr alloy

Eddahbi, M.; Ruano, Oscar Antonio; McNelley, Terry R.

doi:10.1007/s11661-001-0120-z

Cited by 31 publications

(13 citation statements)

References 58 publications

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“…This peak can be ascribed to randomly orientated Cube grains, [19] which were also reported for AA 2004 [20] and AA 5083 aluminum alloys. [21,22,23] It should be noted that ⌺29 (⌺29a 43.6 deg/͗100͘ and ⌺29b 46.4 deg/ ͗221͘) boundaries ( Figure 8) also contribute to the peak. Smaller grain-boundary populations with misorientations between 40 and 50 deg in DC material can be explained by less ⌺29 boundaries.…”

Section: Mesotextures (Grain-boundary Misorientation Distributions)mentioning

confidence: 99%

Texture and grain-boundary evolutions of continuous cast and direct chill cast AA 5052 aluminum alloy during cold rolling

Liu

Morris

2003

Metall Mater Trans A

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Commercially produced hot bands of continuous cast (CC) and direct chill (DC) cast AA 5052 aluminum alloy were cold rolled to different reductions from 10 pct through 90 pct. Evolution of deformation textures in the CC and DC materials was investigated by using three-dimensional orientation distribution functions (ODFs) that were determined by X-ray diffraction. The electron backscatter diffraction (EBSD) technique was adopted to keep track of the evolution of grain boundaries of CC and DC materials during the early stages of cold rolling (Յ40 pct thickness reduction). Results showed that the Cube cluster is found in annealed DC hot band. A much stronger Cube orientation is found in DC hot band than in CC hot band. The cold rolling texture evolutions for CC and DC materials follow the same path. The a and b fibers become well developed after 60 pct cold rolling in both CC and DC materials. The highest intensity along the b fiber (skeleton line) is located near the S orientation {123}͗634͘ in both materials. There exists a path by which the copper orientation (112)[ ʳ 1 ʳ 11] develops at the expense of the Cube orientation (001)[0 ʳ 10] with an increase in cold rolling reductions. Low-angle boundaries with misorientation angles between 1.5 and 5 deg are rapidly increased during the early stage of cold rolling. There is no evidence of the development of twin and twin-related boundaries in either CC or DC materials when the cold rolling reductions are less than 40 pct.

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Section: Mesotextures (Grain-boundary Misorientation Distributions)mentioning

confidence: 99%

Texture and grain-boundary evolutions of continuous cast and direct chill cast AA 5052 aluminum alloy during cold rolling

Liu

Morris

2003

Metall Mater Trans A

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“…[18,40,41] This ratio is significantly higher than that obtained in conventional thermo mechanical processed (TMP) aluminum alloys with a typical ratio of 50 to 65 pct. [42,43] Because the grain microstructure can be controlled by changing the FSP parameters, tool design, vertical pressure, and active cooling/heating, it is likely that the mechanical properties of a metallic material can be tailor made via FSP. The grain size of aluminum and magnesium alloys was continuously reduced by adjusting the FSP conditions, thereby resulting in an increase in both yield strength (YS) and hardness.…”

Section: Friction-stir Fine-grained Structurementioning

confidence: 99%

Friction Stir Processing Technology: A Review

2008

Metall Mater Trans A

1,018

358

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Friction stir processing (FSP), developed based on the basic principles of friction stir welding (FSW), a solid-state joining process originally developed for aluminum alloys, is an emerging metalworking technique that can provide localized modification and control of microstructures in near-surface layers of processed metallic components. The FSP causes intense plastic deformation, material mixing, and thermal exposure, resulting in significant microstructural refinement, densification, and homogeneity of the processed zone. The FSP technique has been successfully used for producing the fine-grained structure and surface composite, modifying the microstructure of materials, and synthesizing the composite and intermetallic compound in situ. In this review article, the current state of the understanding and development of FSP is addressed.

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“…1,5,6) These aluminum alloys are subjected to extensive cold or warm rolling followed by heating to temperatures of superplastic deformation. 1,5,6,[10][11][12][13][14][15][16][17][18][19][20] Dispersion particles prevent static recrystallization of the warm/cold worked material, and plastic deformation induces high-angle boundaries (HAB) via a continuous reaction called as continuous dynamic recrystallization (CDRX). 1,[12][13][14][15][16][17][18][19][20] The dispersoids effectively pin the deformation-induced boundaries preventing much of the low-angle boundary (LAB) migration resulting in their mutual elimination 21) and also growth of recrystallized grains as well that provides capability for superplasticity.…”

Section: Introductionmentioning

confidence: 99%

“…Despite considerable research works, the exact nature of such the recrystallization process and origin of superplasticity of aluminum alloys in this microstructure condition are not yet clear. 1,20) It has been proposed 12,[17][18][19][20] that LABs are evolved in cellular dislocation structure under static annealing preceded superplastic deformation. Following deformation results in the eventual conversion of these LABs into HABs, which become able to support GBS.…”

Section: Introductionmentioning

confidence: 99%

The Role of Grain Boundary Sliding in Microstructural Evolution during Superplastic Deformation of a 7055 Aluminum Alloy

et al. 2002

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The microstructure evolution in a 7055 aluminum alloy subjected to thermomechanical processing (TMP) was studied at 450 • C anḋ ε = 1.7 × 10 −3 s −1 at which the material exhibits superplastic behavior with a total elongation of 720% and the coefficient m = 0.58. Partially recrystallized initial structure of the as-processed 7055 Al consisted of bands of recrystallized grains with a mean size of 11 µm alternating with bands of recovered subgrains with a mean size of 2 µm. The true stress-true strain curve exhibits a well-defined peak stress, followed by gradual strain softening. The coefficient of strain rate sensitivity, m, remains unchanged at ε ≤ 1 and tends to decrease with strain at ε > 1. The initial microstructure persists near the peak strain. Following strain leads to evolution of initial partially recrystallized structure into uniform fully recrystallized structure due to occurrence of continuous dynamic reactions, i.e. continuous dynamic recrystallization (CDRX). The data of microstructural observation and misorientation analysis show that low-angle boundaries (LAB) gradually convert to high-angle boundaries (HAB) resulting in an extensive flow softening. It was shown that grain boundary sliding (GBS) provides superplastic flow at all strains. Concurrently, GBS plays an important role in the dynamic evolution of new grains facilitating conversion of LABs to HABs.

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The evolution of grain boundary character during superplastic deformation of an Al-6 pct Cu-0.4 pct Zr alloy

Cited by 31 publications

References 58 publications

Texture and grain-boundary evolutions of continuous cast and direct chill cast AA 5052 aluminum alloy during cold rolling

Texture and grain-boundary evolutions of continuous cast and direct chill cast AA 5052 aluminum alloy during cold rolling

Friction Stir Processing Technology: A Review

The Role of Grain Boundary Sliding in Microstructural Evolution during Superplastic Deformation of a 7055 Aluminum Alloy

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