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

Hayoune, A.; Hamana, D.

doi:10.1016/j.jallcom.2008.06.070

Cited by 32 publications

(19 citation statements)

References 31 publications

(76 reference statements)

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“…The first strengthening effect is that dislocations cut the small precipitates with coherent interfaces. This strengthening mechanism often occurs in Al-Cu [15] and Al-Zn [16] alloys. In comparison, for the large particles with non-coherent interface, the dislocations have to bypass them.…”

Section: Discussionmentioning

confidence: 99%

Effect of Ti2Cu precipitates on mechanical behavior of Ti–2.5Cu alloy subjected to different heat treatments

Yao

Sun

Lin

et al. 2009

Journal of Alloys and Compounds

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Section: Discussionmentioning

confidence: 99%

Effect of Ti2Cu precipitates on mechanical behavior of Ti–2.5Cu alloy subjected to different heat treatments

Yao

Sun

Lin

et al. 2009

Journal of Alloys and Compounds

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“…It is well accepted 25,26 that in aluminium base alloys, due to the size differences between solute and aluminium atoms (specially Cu and Mg for which ∆r Cu = −10.5% and ∆r Mg = +11.8% where ∆r i = (r i − r Al )/r Al ), the formation of solute rich precipitates causes increasing or decreasing of the matrix lattice parameter, through the modification of the dissolved amounts of alloying atoms in the matrix. 20,21 On the other hand, the nature of the precipitate/matrix interface (coherent or incoherent) can be indicated by the presence or absence of distortion zones in the matrix surrounding the precipitates.…”

Section: Identification Of the Precipitation Sequencementioning

confidence: 99%

“…[3][4][5][6][7]21,22 The precipitation of the equilibrium phases S, θ and β, follows the pattern typical of other aluminum alloys with the initial zone and/or coherent stage of precipitation (Cu, Mg-rich GPB zones, Cu-rich GP zones and Mg, Si-rich GP zones), then precipitation of a single semi-coherent modification of the equilibrium phase and, finally, the formation of the equilibrium phase. 1,[3][4][5]9,11,16,25 However, several sequences of precipitation are proposed for the Q phase; Cayron et al have suggested 5,23 that the Q phase has two metastable precursors QP and QC. Other authors propose 24 coherent Q ′ -phase as the only metastable Q-phase precursor.…”

Section: Introductionmentioning

confidence: 99%

A CALORIMETRIC STUDY OF THE PRECIPITATION HARDENING MECHANISMS IN AN Al–Cu–Mg–Si ALLOY

Hayoune

2013

Int. J. Mod. Phys. B

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The precipitation phenomena and the related hardening in an Al-Cu-Mg-Si alloy were studied by calorimetry, X-ray diffraction analysis and microhardness measurements. The main calorimetric peaks were identified to be due to β ′′ , θ ′ and Q ′ phases precipitation. The hardening during aging at room temperature and 160 • C, was respectively, explained by atomic clusters and GP zones formation and by GP zones and β ′′ /θ ′ phases coprecipitation. Although the mechanical properties variation during aging at 200 • C is simple, the corresponding microstructural evolution is complex: on the basis of the DSC results, the increasing of microhardness values, is mainly due to the coprecipitation of GP zones and β ′′ /θ ′ phases, however, the maximum hardening is explained by the coexistence of β ′′ /θ ′ and θ ′′ phases. Another important conclusion is that during aging at 160 • C and 200 • C, the θ ′ phase is essentially developed from GP zones.

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“…It is well-known that the radii of Fe, Cu, and Si atoms (r Cu =0.157 nm, r Fe =0.172 nm, and r Si =0.146 nm) are all smaller than that of Al atoms (r Al =0.182 nm) [29]; the increase of the solubility of Fe, Cu, and Si elements leads to the lattice distortion, conducing to the unit-cell shrinkage and the reduction of the lattice constant [30]. Fig.…”

Section: Analysis Of the Microstructural Evolution Or Phase Transformmentioning

confidence: 99%

Microstructure evolution and phase transformation of traditional cast and spray-formed hypereutectic aluminium-silicon alloys induced by heat treatment

Hou

Cai

Cui

et al. 2010

Int J Miner Metall Mater

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Microstructural evolution and phase transformation induced by different heat treatments of the hypereutectic aluminium-silicon alloy, Al-25Si-5Fe-3Cu (wt%, signed as 3C), fabricated by traditional cast (TC) and spray forming (SF) processes, were investigated by differential scanning calorimetry (DSC) and scanning electron microscopy (SEM) combined with energy dispersive X-ray spectroscopy and X-ray diffraction techniques. The results show that Al 7 Cu 2 Fe phase can be formed and transformed in TC-and SF-3C alloys between 802-813 K and 800-815 K, respectively. The transformation from β-Al 5 FeSi to δ-Al 4 FeSi 2 phase via peritectic reaction can occur at around 858-870 K and 876-890 K in TC-and SF-3C alloys, respectively. The starting precipitation temperature of δ-Al 4 FeSi 2 phase as the dominant Fe-bearing phase in the TC-3C alloy is 997 K and the exothermic peak about the peritectic transformation of δ-Al 4 FeSi 2 →β-Al 5 FeSi is not detected in the present DSC experiments. Also, the mechanisms of the microstructural evolution and phase transformation are discussed.

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

Cited by 32 publications

References 31 publications

Effect of Ti2Cu precipitates on mechanical behavior of Ti–2.5Cu alloy subjected to different heat treatments

Effect of Ti2Cu precipitates on mechanical behavior of Ti–2.5Cu alloy subjected to different heat treatments

A CALORIMETRIC STUDY OF THE PRECIPITATION HARDENING MECHANISMS IN AN Al–Cu–Mg–Si ALLOY

Microstructure evolution and phase transformation of traditional cast and spray-formed hypereutectic aluminium-silicon alloys induced by heat treatment

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