Simulation of the evolution of GP zones in Al–Cu alloys: an extended Cahn–Hilliard approach

Löchte, L.; Gitt, A.; Gottstein, Günter; Hurtado, I.

doi:10.1016/s1359-6454(00)00073-2

Cited by 48 publications

(33 citation statements)

References 27 publications

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“…16) On the other hand, Löchte et al have reported that Cu solubility below 200 C is less than 0.1 at.%Cu (0.24 mass%Cu). 19) From these Cu solubility, Cu concentration used for the formation of Al 2 Cu phase at 300 C or below 200 C are 0.68 mass% or 0.24 mass% less than Cu composition shown in Fig. 6 Fig.…”

Section: Heat Treatmentmentioning

confidence: 84%

Density and Hardness Gradients of Functionally Graded Material Ring Fabricated from Al-3 mass%Cu Alloy by a Centrifugal <I>In-Situ</I> Method

Watanabe

Sato

Ogawa³

et al. 2007

Mater. Trans.

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In present study, the Al-Al 2 Cu functionally graded material (FGM) ring was fabricated from Al-3 mass%Cu initial master alloy by the centrifugal in-situ method. In the case of Al-3 mass%Cu alloy, the density of the primary -Al crystal is larger than that of the molten Al alloy. Therefore, the solid -Al phase migrates towards the outer periphery of the ring when the centrifugal force is applied in the early stage of solidification. Consequently, since the Cu concentration within the FGM ring monolithically increases towards the ring's inner position, the FGM ring, whose density increases toward inner region, can be successfully fabricated by the centrifugal in-situ method from dilute Al-Cu alloy. It is also found that the hardness increases towards the inner region of the ring within the Al-Al 2 Cu FGM ring. The hardness of the fabricated specimens at the inner region of the ring increases in a large scale by the heat treatments, since Guinier-Preston (GP) zones would be formed by aging.

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Section: Heat Treatmentmentioning

confidence: 84%

Density and Hardness Gradients of Functionally Graded Material Ring Fabricated from Al-3 mass%Cu Alloy by a Centrifugal <I>In-Situ</I> Method

Watanabe

Sato

Ogawa³

et al. 2007

Mater. Trans.

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“…From Fig.3, it can be seen that the cube of the average size of the particles is not a linear function of the aging time, which is required for the LSW The LSW theory predicts that during the coarsening process, the growth law of precipitates follows: R ∝t m , where R is the average radius, t is the aging time (number of time step), and m is the coarsening rate time index and is equal to 1/3 in the LSW theory. In an elastic-contained system, a finite lattice mismatch introduces significant internal stress in the system and has remarkable effect on the coarsening kinetics of the particles [16] .…”

Section: Growth and Coarsening Of Ordered Phasesmentioning

confidence: 99%

Microscopic phase-field simulation for coarsening behavior of L12 and DO22 phases of Ni75CrxAl25−x alloy

Chen

Zhang

2008

J. Cent. South Univ. Technol.

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Based on the microscopic phase-field dynamic model and the microelasticity theory, the coarsening behavior of L1 2 and DO 22 phases in Ni 75 Cr x Al 25−x alloy was simulated. The results show that the initial irregular shaped, randomly distributed L1 2 and DO 22 phases are gradually transformed into cuboidal shape with round corner, regularly aligned along directions [100] and [001], and highly preferential selected microstructure is formed during the later stage of precipitation. The elastic field produced by the lattice mismatch between the coherent precipitates and the matrix has a strong influence on the coarsening kinetics, and there is no linear relationship between the cube of the average size of precipitates and the aging time, which does not agree with the results predicted by the classical Lifshitz-Slyozov-Wagner. The coarsening processes of L1 2 and DO 22 phases are retarded in elastically constrained system. In the concurrent system of L1 2 and DO 22 phases, there are two types of coarsening modes: the migration of antiphase domain boundaries and the interphase Ostwald ripening.

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Section: Introductionmentioning

confidence: 95%

“…The maximum solubility of Cu in the fcc, Al-rich phase is 2.48 ± 0.05 at.% at the eutectic temperature (548.2 • C) [3]. The Cu solubility decreases with decreasing temperature, and it is lower than 0.1 at.% Cu for temperatures below 200 • C [3]. When an alloy with a composition Al-(0.5-2.48) at.% Cu is homogenised at about 540 • C and subsequently quenched to a lower temperature; the Cu is retained in a supersaturated solid solution.…”

Section: Introductionmentioning

confidence: 96%

“…Upon heat treatment this singlephase alloy will decompose into a sequence of metastable and stable phases. Many investigations have been devoted to examining the details of the precipitation sequence in this alloy system [2][3][4][5][6][7][8][9][10][11][12][13][14], using both theoretical models and several newly developed techniques [10]. The precise precipitation sequence is a function of the alloy composition and the ageing temperature, but usually follows the order: supersaturated solid solution (s.s.s.)…”

Section: Introductionmentioning

confidence: 99%

See 1 more Smart Citation

Structural evolution during non-isothermal ageing of a dilute Al–Cu alloy by dilatometric analysis

Hayoune

Hamana

2009

Journal of Alloys and Compounds

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Simulation of the evolution of GP zones in Al–Cu alloys: an extended Cahn–Hilliard approach

Cited by 48 publications

References 27 publications

Density and Hardness Gradients of Functionally Graded Material Ring Fabricated from Al-3 mass%Cu Alloy by a Centrifugal <I>In-Situ</I> Method

Density and Hardness Gradients of Functionally Graded Material Ring Fabricated from Al-3 mass%Cu Alloy by a Centrifugal <I>In-Situ</I> Method

Microscopic phase-field simulation for coarsening behavior of L12 and DO22 phases of Ni75CrxAl25−x alloy

Structural evolution during non-isothermal ageing of a dilute Al–Cu alloy by dilatometric analysis

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