Precipitation structure and strengthening mechanisms in an Al-Cu-Mg-Ag alloy

Газизов, М. Б.; Kaibyshev, Rustam

doi:10.1016/j.msea.2017.06.110

Cited by 119 publications

(30 citation statements)

References 54 publications

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“…, where n 1 and n 2 are the numbers of intercepts on the sets of orthogonal lines of total lengths L 1 and L 2 in TEM images. The foil thickness was determined by the convergent beam electron diffraction (CBED) method based on Kossel-Mӧllenstedt fringe oscillations [15,16,43,44] and averaged using at least three measurements for each TEM image. A JEOL ARM-200F microscope equipped with a probe-aberration corrector and JEOL ADF-detector was used to examine the crystal structure of the precipitates formed in the aged samples.…”

Section: Methodsmentioning

confidence: 99%

Precipitation behavior in an Al–Cu–Mg–Si alloy during ageing

Газизов

Marioara

Friis

et al. 2019

Materials Science and Engineering: A

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wt. %) alloy was examined in detail after aging at 170°C with different dwell times up to 96 h. Deformation by 3%stretching prior to aging was used to investigate the effect of dislocations on phase and hardness evolution and compared with the undeformed material. The small pre-deformation led to a slight decrease of peak strength due to reduced homogenous nucleation. Strong interaction between different phases caused the formation of hybrid structures both in the undeformed bulk areas and on dislocations. These phases consist of different fragments of the GP zones, θ"and θ'-phases from the Al-Cu system, GPB zones and S1-phase from the Al-Cu-Mg system, and β"-, β'-Cu, C-and Q'-phases from the Al-Mg-Si-Cu system. A new phase named C1, isostructural to the C-phase but having a different orientation with the Al matrix -(010) C //(010) Al , [001] C //[101] Al , has been found predominantly on dislocation lines, and to a lesser extent in hybrid precipitates in the bulk. Calculations of structural stability by density functional theory (DFT) were performed on experimentally found structures, consisting of a C-phase core in two different orientations, and having Cu segregations in GP-like structures at their interfaces with the matrix.

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Section: Methodsmentioning

confidence: 99%

Precipitation behavior in an Al–Cu–Mg–Si alloy during ageing

Газизов

Marioara

Friis

et al. 2019

Materials Science and Engineering: A

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“…It can thus be deduced that Mg has a greater facility to dissolve during the solution treatment than Cu, the latter needing more time. The omega-Al 7 Cu 2 Fe phase was found to precipitate during the heat treatment as a result of the dissolution and atom diffusion of Cu [23], which is a transition phase during aging [24]. Figure 9 shows the hardness profile obtained during the natural ageing, up to 1700 h, of the quenched specimens following the solution treatment at 495 °C.…”

Section: Methodsmentioning

confidence: 99%

Heat Treatment Optimization in Al-Cu-Mg-Si Alloys, with or without Prior Deformation

Álvarez-Antolín

Segurado-Frutos

Neira-Castaño

et al. 2018

Metals

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The properties of Al-Cu-Mg alloys simultaneously depend on dissolving the maximum amount of Cu and Mg in the solution treatment and on achieving optimal ageing. The aim of this study is to analyze the effect on an Al-Cu4.5-Mg1.5-Si0.75 alloy, manufactured by continuous casting and hot rolling until achieving a reduction in its cross-section greater than 90%, of the dwell time at the solution temperature, 495 • C (4, 8, and 24 h), of the different ageing temperatures (160, 180, and 200 • C), and of cold rolling prior to ageing. The microstructural variations underwent the material during its manufacturing process, form its continuous casting to subsequent hot rolling, were analyzed by means of optical microscopy (OM) and scanning electronic microscopy (SEM), with characteristic energy dispersive X-ray (EDX) microanalysis. The crystalline phases present after the different solution and natural ageing treatments were identified and quantified by means of X-ray diffraction (XRD), concluding that Mg is easier to dissolve than Cu. The transient states associated with the Mg 2 Si phase are the most abundant. However, the longer the dwell time at the solution temperature, the greater the weight percentage of the transient states associated with the Al 2 Cu phase during ageing. The higher the ageing temperature, the faster the peak hardness is reached, but the lower its value. The ageing temperature that allows the highest hardness to be obtained was 160 • C. The maximum hardness value reached was 162 HV, obtained after a solution treatment at 495 • C for 4 h and ageing at 160 • C for 50 h. By means of prior cold rolling, the peak hardness values are reached more quickly and their values slightly exceed those obtained without this deformation. With ageing at 180 • C, 168 HV are reached after 6 h at this temperature.

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“…According to the Friedel mechanism, the mechanical properties can be also attributed to the ability of the strengthening precipitates to withstand shearing by gliding dislocations [52].…”

Section: Precipitation Microstructurementioning

confidence: 99%

Effect of T6 Heat Treatment on the Microstructure and Hardness of Secondary AlSi9Cu3(Fe) Alloys Produced by Semi-Solid SEED Process

Fabrizi

Capuzzi

Mori

et al. 2018

Metals

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The effect of the T6 heat treatment on the microstructure and hardness of a secondary semi-solid AlSi9Cu3(Fe) alloy have been investigated by using optical, scanning and transmission electron microscopy and hardness testing. The semi-solid alloy was produced using the swirled enthalpy equilibration device (SEED). The solution heat treatments were performed at 450, 470 and 490 °C for 1 to 6 h followed by water quenching and artificial ageing at 160, 180 and 220 °C for holding times ranging from 1 to 30 h. The microstructural investigations have revealed the spheroidization of the eutectic Si and the dissolution of the majority of Cu-rich compounds after all the solution heat treatments; moreover, the greater the solution temperature and time, the higher the hardness of the alloy. Unacceptable surface blistering has been observed for severe solution condition, 490 °C for 3 and 6 h. The artificial ageing at 160 °C for 24 h has led to the highest alloy strengthening thanks to the precipitation of β” and Q’ (or L) phases within the α-Al matrix. The hardening peaks at higher temperatures have been early achieved due to faster hardening kinetic; however, the lower number density of β” and Q’ (or L) phases and the presence of coarser θ’ precipitates result in a reduction of hardness values for peak aged condition at 180 and 220 °C, respectively.

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Precipitation structure and strengthening mechanisms in an Al-Cu-Mg-Ag alloy

Cited by 119 publications

References 54 publications

Precipitation behavior in an Al–Cu–Mg–Si alloy during ageing

Precipitation behavior in an Al–Cu–Mg–Si alloy during ageing

Heat Treatment Optimization in Al-Cu-Mg-Si Alloys, with or without Prior Deformation

Effect of T6 Heat Treatment on the Microstructure and Hardness of Secondary AlSi9Cu3(Fe) Alloys Produced by Semi-Solid SEED Process

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