Superplasticity in a 2219 aluminum alloy

Кайбышев, Р. О.; Kazakulov, I. Ya.; Gromov, D. A.; Musin, Fanil; Lesuer, D.R.; Nieh, T.G.

doi:10.1016/s1359-6462(01)00930-7

Cited by 50 publications

(34 citation statements)

References 7 publications

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“…4 and 5, the cavities are observed to be present predominantly on the grain boundaries, triple points and/or near secondary-phase particles, only few occurring in the grain interior. The cavities have small spherical and large irregular or jagged in shape, implying the operations of diffusion-controlled cavity growth and plasticity-controlled cavity growth mechanisms together [20,21]. During the deformation, the coarse secondaryphase particles exceeding the critical nucleation diameter (typically larger than 1 m) can act as nucleation sites for cavitation [22].…”

Section: Resultsmentioning

confidence: 99%

High temperature deformations of Mg–Y–Nd alloys fabricated by different routes

Liu

Chen

Han

2008

Materials Science and Engineering: A

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Section: Resultsmentioning

confidence: 99%

High temperature deformations of Mg–Y–Nd alloys fabricated by different routes

Liu

Chen

Han

2008

Materials Science and Engineering: A

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“…There are two different TMP routes to achieve grain refinement in wrought aluminum alloys. One of these routes termed as overaging/recrystallization TMP, 1,[3][4][5][6] involves overaging treatment to produce coarse precipitate particles, which become sites for particle-stimulated nucleation of static recrystallization after cold rolling. The other route, which can be termed as recrystallization/recrystallization TMP, [7][8][9] involves two sequential procedures of warm/cold rolling followed by recrystallization annealing.…”

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

“…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%

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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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“…[29] On a macroscopic scale, grain boundaries after sliding and accommodation form discontinuous stringers that are oriented at approximately 45 deg to the tensile axis (i.e., along the planes of maximum shear). [31] The traces of grain boundary orientations with respect to the tensile axis in superplastically deformed specimens were determined from several two-dimensional (2-D) sections of the microstructures in the gage portions and are plotted as a histogram in Figure 14. This histogram shows a peak with a large population of boundaries oriented at about 40 to 50 deg with respect to the tensile axis, which confirms that GBS predominantly occurs during the deformation in the ␤ phase.…”

Section: B Deformation Behavior In the ␤ Phase Field At Low Strain Rmentioning

confidence: 99%

Thermomechanical response of a powder metallurgy Ti-6Al-4V alloy modified with 2.9 pct boron

Bhat

Tamirisakandala

Miracle

et al. 2005

Metall Mater Trans A

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The thermomechanical response of Ti-6Al-4V modified with 2.9 pct B produced by a blended powder metallurgy route was studied with isothermal constant strain-rate hot compression tests in the temperature range 850 °C to 1200 °C and strain rate range 10 Ϫ3 to 10 s Ϫ1 . Detailed analyses of the flow stress data were conducted to identify various microstructural deformation and damage mechanisms during hot working by applying available materials modeling techniques. In the ␣ ϩ ␤ phase field, cavitation at the matrix/TiB interfaces and TiB particle fracture occurs at low strain rates (Ͻ10 Ϫ1 s Ϫ1 ), while adiabatic shear banding also occurs at high strain rates. At low strain rates, the ␤ phase deforms superplastically due to the stabilization of a fine grain size by the TiB particles. Grain boundary and matrix/TiB interface sliding with simultaneous diffusional accommodation are observed to contribute to the ␤ superplasticity. The deformation behavior at high strain rates in the ␤-phase field is similar to that of the ␣ ϩ ␤ phase field, with microstructural manifestations of extensive cavitation at the matrix/TiB interfaces and TiB particle fracture.

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Superplasticity in a 2219 aluminum alloy

Cited by 50 publications

References 7 publications

High temperature deformations of Mg–Y–Nd alloys fabricated by different routes

High temperature deformations of Mg–Y–Nd alloys fabricated by different routes

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

Thermomechanical response of a powder metallurgy Ti-6Al-4V alloy modified with 2.9 pct boron

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