Modelling of the microstructure and strength evolution in Al–Mg–Si alloys during multistage thermal processing

Myhr, Ole Runar; Grong, Ø.; Fjær, Hallvard G.; Marioara, Calin Daniel

doi:10.1016/j.actamat.2004.07.002

Cited by 232 publications

(204 citation statements)

References 14 publications

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“…Coarsening arises naturally in the model when the average solute concentration in the matrix ( c ) becomes larger than the solute concentration at the precipitate/matrix interface ( i c ), thus resulting in the dissolution of the smaller precipitates [6,10].…”

Section: Growth/coarsening Of S Phasementioning

confidence: 99%

“…v N is the number of the nucleation sites per unit volume estimated as the number of solute atoms per unit volume [10,36] and * r is the critical size which is evaluated by the Gibbs-Thompson relationship [6]. The formulation of the Gibbs-Thompson often used is given by [10,33,35]:…”

Section: Nucleation Of S Phasementioning

confidence: 99%

“…There has been considerable interest in the modelling of precipitation kinetics and strengthening in age hardening aluminium alloys [1,2,3,4,5,6,7,8,9,10,11,12,13]. Most of the published work on modelling of the precipitation kinetics in aluminium alloys is based on two main approaches [1][2][3][4][5][6][7][8][9][10].…”

Section: Introductionmentioning

confidence: 99%

“…Most of the published work on modelling of the precipitation kinetics in aluminium alloys is based on two main approaches [1][2][3][4][5][6][7][8][9][10]. In one of the approaches, the modelling of the nucleation, growth and impingement of precipitates are based on the concepts of the Johnson-Mehl-AvramiKolmogorov (JMAK) model [14,15,16] and the modelling of the coarsening kinetics is based on the Lifshitz-Slyozov-Wagner (LSW) theory [17,18].…”

Section: Introductionmentioning

confidence: 99%

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A model for precipitation kinetics and strengthening in Al–Cu–Mg alloys

Khan

Starink

Yan

2008

Materials Science and Engineering: A

133

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A physically-based numerical model is developed to predict the microstructural evolution and strengthening in Al-Cu-Mg alloys during isothermal treatments. The modelling of the formation kinetics of the precipitates is based on the Kampmann and Wagner model. The strengthening by the shearable Cu:Mg co-clusters is modelled on the basis of modulus strengthening mechanism and the strengthening by the non-shearable S phase precipitates is based on the Orowan looping mechanism. The model predictions are verified by comparing with the strength and differential isothermal calorimetery data on 2024-T351 aluminium alloys. The microstructural development and strength predictions of the model are generally in good agreement with the experimental data.

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Section: Growth/coarsening Of S Phasementioning

confidence: 99%

Section: Nucleation Of S Phasementioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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A model for precipitation kinetics and strengthening in Al–Cu–Mg alloys

Khan

Starink

Yan

2008

Materials Science and Engineering: A

133

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“…The modelling strategy chosen here is different from works based on Kampmann-Wagner type models of precipitate evolution during the weld thermal cycle [41,42]. The reason for the present choice of modelling approach is that in the present alloy co-clusters are the main strengthening (pre-)precipitates and treatments of the precipitation of these co-clusters and the interaction with the formation of other precipitates within the Kampmann-Wagner framework are not available.…”

Section: Model Formulation Application and Evaluationmentioning

confidence: 99%

VPPA welds of Al-2024 alloys: Analysis and modelling of local microstructure and strength

Wang

Lefebvre

Yan

et al. 2006

Materials Science and Engineering: A

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The microstructural features of variable polarity plasma arc welded Al-Cu-Mg 2024-T351 with 2319 filler have been studied by TEM, SEM and DSC. Fusion zone, partial melting zone, resolutionising zone, overageing (for S phase), peak ageing (for S phase) and under ageing zones (for S phase) have been identified. The Ω phase has been observed between re-solutionising zone and peak ageing zone. The hardness profile contains two peaks. The microstructure development, and resulting hardness and yield strength profiles are modelled using a model which combines primary precipitation, resolution, partial/full melting and resolidification (Scheil type) and reprecipitation, in a two precipitate -two mechanism approach. Hardness profiles and microstructures are accurately predicted. The hardness peak in the re-solutionising zone is due to re-solutionising and subsequent Cu-Mg co-cluster formation; and the second hardness peak is caused by S phase strengthening.

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Welding Aluminum Alloys

Courbiere¹

2008

Metallurgy and Mechanics of Welding

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Modelling of the microstructure and strength evolution in Al–Mg–Si alloys during multistage thermal processing

Cited by 232 publications

References 14 publications

A model for precipitation kinetics and strengthening in Al–Cu–Mg alloys

A model for precipitation kinetics and strengthening in Al–Cu–Mg alloys

VPPA welds of Al-2024 alloys: Analysis and modelling of local microstructure and strength

Welding Aluminum Alloys

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