The effect of cold deformation on the kinetics of the β″ precipitates in an Al-Mg-Si alloy

Yassar, Reza S.; Field, David P.; Weiland, Hasso

doi:10.1007/s11661-005-0326-6

Cited by 59 publications

(36 citation statements)

References 25 publications

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“…Nevertheless, a small Mg2Si peak is still observed after four passes. Panigrahi et al [23] reported that the formation of the Mg2Si phase after SPD could be explained by the accumulation of dislocations that may act as a shortcircuit path for solutes and atomic migration facilitating this precipitation. Furthermore, they added that the frictional heat induced on the sample caused a clustering of Mg and Si atoms with vacancies, leading to the formation of Mg2Si peak in the XRD pattern.…”

Section: X-ray Diffraction Analysismentioning

confidence: 99%

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Structure and microstructure evolution of Al–Mg–Si alloy processed by equal-channel angular pressing

Khelfa

Rekik

Khitouni

et al. 2017

Int J Adv Manuf Technol

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An ultrafine grained Al-Mg-Si alloy was prepared by severe plastic deformation using the Equal Channel Angular Pressing (ECAP) method. Samples were ECAPed through a die with an inner angle of Φ=90º and outer arc of curvature of ψ= 37° from 1 to 12 ECAP passes at room temperature following route Bc. To analyze the evolution of the microstructure at increasing ECAP passes x-ray diffraction and Electron Backscatter Diffraction analyses were carried out. The results revealed two distinct processing regimes, namely: i) from 1 to 5 passes, the microstructure evolved from elongated grains and sub-grains to a rather equiaxed array of ultrafine grains and ii) from 5 to 12 passes where no change in the morphology and average grain size was noticed. In the overall behavior, the boundary misorientation angle and the fraction of high-angle boundaries increase rapidly up to 5 passes and at a lower rate from 5 to 12 passes. The crystallite size decreased down to about 45 nm with the increase in deformation. The influence of deformation on precipitate evolution in the Al-Mg-Si alloy was also studied by differential scanning calorimetry. A significant decrease in the peak temperature associated to the 50% of recrystallization was observed at increasing ECAP passes.

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Section: X-ray Diffraction Analysismentioning

confidence: 99%

“…On the other hand, among the age hardenable aluminum alloys, the Al-Mg-Si system has been the object of extensive investigation considering its technological importance as the basis of the high strength aluminum alloys. The precipitation sequence usually proposed for this type of alloys is as follows [13,14]:…”

Section: Introductionmentioning

confidence: 99%

Structure and microstructure evolution of Al–Mg–Si alloy processed by equal-channel angular pressing

Khelfa

Rekik

Khitouni

et al. 2017

Int J Adv Manuf Technol

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“…For Al-Mg-Si alloys, previous work revealed by DSC analysis that pre-straining accelerates precipitation because of decreased activation energy for the growth of precipitates. 8,9) Matsuda et al 10) reported that 5% pre-strain following pre-aged at 423 K for 60 ks improves bake-hardening response in under-aged condition and results in higher peak hardness at 473 K for an Al-0.37 mass%Mg-0.62 mass%Si alloy. Furthermore, Birol et al 11,12) reported that pre-straining shortly after solution heat treatment suppresses clustering behavior at room temperature, but results in the enhanced formation of the 00 phase during aging at 453 K. These suggest that the combined effect of pre-straining and pre-aging is quite useful, but still have room for investigation under various combinations of the amount of pre-strain and pre-aging temperature.…”

Section: )mentioning

confidence: 99%

Combined Effect of Pre-Straining and Pre-Aging on Bake-Hardening Behavior of an Al-0.6 mass%Mg-1.0 mass%Si Alloy

et al. 2010

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The effect of pre-straining in combination with pre-aging on bake-hardening behavior of an Al-0.6 mass%Mg-1.0 mass%Si alloy was investigated by means of Vickers hardness test, electrical conductivity measurement, differential scanning calorimetry (DSC) and transmission electron microscopy (TEM). Hardness change and DSC analysis revealed that only 3% pre-strain suppresses the formation of clusters; i.e. cluster(1), during single aging below 343 K. On the other hand, by combining with pre-aging at 343 K, pre-straining was found to improve bakehardening response during final aging at 443 K. TEM observation confirmed that the improvement of bake-hardening response by pre-straining is mainly due to the enhanced precipitation of 00 phase in the matrix. These results are explained by the consideration that dislocations induced by pre-straining reduce the concentration of quenched-in excess vacancies, resulting in both the suppressed clustering of solute atoms during pre-aging and the accelerated precipitation of the 00 phase from more supersaturated solute atoms in final aging.

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“…It has been reported [27][28][29][30][31] that 10%-15% pre-deformation leads to formation of heterogeneous nucleation along dislocation lines. After artificial aging, different types of precipitates (except for β") form: a continuous decoration of the dislocation lines ("string-like" precipitates) together with discrete precipitation consisting mainly of B' [27][28][29][30], and together with (often disordered) Q' [11,12,31,32] if Cu is present in the Al-Mg-Si alloys. In the case of 0.5%-5% pre-deformation, β" is dominant at peak hardness condition, and this level of pre-deformation accelerates formation of β" due to decreased activation energy [33][34][35][36].…”

Section: Introductionmentioning

confidence: 99%

The effects of quench rate and pre-deformation on precipitation hardening in Al–Mg–Si alloys with different Cu amounts

Saito

Marioara

Røyset

et al. 2014

Materials Science and Engineering: A

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The effects of quench rate after solution heat treatment in combination with 1% pre-deformation on precipitation hardening in three Al-Mg-Si alloys have been investigated by transmission electron microscopy and hardness measurements during an isothermal heat treatment. The alloys contain different Cu amounts (up to 0.1 wt%) and the same amounts of other solute elements. While a Cu amount below 0.01wt% does not affect precipitation hardening, an addition of 0.1wt% Cu increases hardness due to formation of a fine microstructure having a high number density of short precipitates. A double peak hardness evolution was observed during isothermal heat treatment. This effect was most pronounced for alloys with low quench rate, and less pronounced for alloys with 1% pre-deformation and 0.1wt% Cu addition. The low quench rate also led to wider precipitation free zones. This effect was also less pronounced by 1% predeformation and addition of 0.1wt% Cu.

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The effect of cold deformation on the kinetics of the β″ precipitates in an Al-Mg-Si alloy

Cited by 59 publications

References 25 publications

Structure and microstructure evolution of Al–Mg–Si alloy processed by equal-channel angular pressing

Structure and microstructure evolution of Al–Mg–Si alloy processed by equal-channel angular pressing

Combined Effect of Pre-Straining and Pre-Aging on Bake-Hardening Behavior of an Al-0.6 mass%Mg-1.0 mass%Si Alloy

The effects of quench rate and pre-deformation on precipitation hardening in Al–Mg–Si alloys with different Cu amounts

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