Precipitation of silicon in aluminum-silicon: A calorimetric analysis of liquid-quenched and solid- quenched alloys

Rooyen, M. Van; Mittemeijer, E. J.

doi:10.1007/bf02647402

Cited by 63 publications

(17 citation statements)

References 21 publications

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“…This comparison is generally favourable. For instance, the interfacial energy during the coarsening regime (~ 0.5 J/m 2 ) is lower than the interfacial energies reported for incoherent precipitates, which are generally in the order of 1 J/m 2 [55]; but they are somewhat higher than interfacial energies reported for fully coherent particles, which are generally in the order of 0.2 J/m 2 (see e.g. work on Al 3 Zr precipitates in Al [11] and on η precipitates in Al [35]).…”

Section: Resultsmentioning

confidence: 70%

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

Khan

Starink

Yan

2008

Materials Science and Engineering: A

128

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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: Resultsmentioning

confidence: 70%

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

Khan

Starink

Yan

2008

Materials Science and Engineering: A

128

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“…Due to the limited DSC data at very low cooling rates for Al-0.26Si, |ΔHRT sat | for this alloy was estimated from value |ΔHRT sat | = 11.3 J/g for Al-0.72Si using the Si content proportion of both alloys. The enthalpy change of precipitation per mole Si from the Al-rich matrix was experimentally studied in [15,38] and was derived to be about 54 kJ mol -1 . Taking this value into 370 account, theoretically |ΔHRT sat | ≈ 13.2 J/g for Al-0.72Si and |ΔHRT sat | ≈ 4.8 J/g for Al-0.26Si result, respectively.…”

Section: Model For Calculation Of Solute Content and Precipitated Volmentioning

confidence: 99%

Quench-induced precipitates in Al–Si alloys: Calorimetric determination of solute content and characterisation of microstructure

et al. 2015

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The present study introduces an experimental approach to investigate mechanical properties of well-defined nonequilibrium states of Al-Si alloys during cooling from solution annealing. The precipitation behaviour of binary Al-Si alloys during the cooling process has been investigated in a wide cooling rate range (2 K/s-0.0001 K/s) with differential scanning calorimetry (DSC). To access the low cooling rate range close to equilibrium an indirect DSC measurement method is introduced. Based on the enthalpy change measured by DSC a physically-based model for the calculation of remaining solute Si amount as function of temperature and cooling rate is presented.Microstructural analyses via light optical microscopy, scanning electron microscopy, atom probe tomography 50 and X-ray diffraction have been performed to evaluate the introduced model and for information on cooling rate dependent precipitate formation. It was found that quench-induced particles of different morphology are formed during cooling. Thermomechanical analyses on clearly distinct undercooled Al-Si states show that flow stress during cooling is dependent on temperature as well as cooling rate. The mechanical behaviour is therefore influenced by solute Si content and quench-induced precipitates.

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“…The precipitate/matrix interfacial energy, σ s , is constant, whilst the equilibrium solubility is taken according to a regular solution model (see e.g. [48]):…”

Section: Interfacial Energy: the Gibbs-thomson Effectmentioning

confidence: 99%

“…For the various parameters we will take values for precipitation of Si from Al, the interfacial energy in this system has been estimated at 1.5 J/m 2 [48]. Results, presented in Fig.…”

Section: Interfacial Energy: the Gibbs-thomson Effectmentioning

confidence: 99%

Untitled

Starink

2001

Journal of Materials Science

162

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If certain preconditions are met, the Johnson-Mehl-Avrami-Kolmogorov (JMAK) kinetic equation is exactly accurate for nucleation and growth reactions with linear growth and is, at least, a good approximation for nucleation and growth reactions with parabolic growth. These preconditions include randomly distributed product phases, isotropic growth and constant equilibrium state. Mechanisms causing deviations from these preconditions include: capillarity effect, vacancy annihilation, blocking due to anisotropic growth. It is shown that deviations lead to a modification of the overall transformation, which can be approximated well by a single equation:

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Precipitation of silicon in aluminum-silicon: A calorimetric analysis of liquid-quenched and solid- quenched alloys

Cited by 63 publications

References 21 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

Quench-induced precipitates in Al–Si alloys: Calorimetric determination of solute content and characterisation of microstructure

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