Aging Behaviour of Al-Mg-Si Alloys Subjected to Severe Plastic Deformation by ECAP and Cold Asymmetric Rolling

Farè, S.; Lecis, N.; Vedani, Maurizio

doi:10.1155/2011/959643

Cited by 30 publications

(6 citation statements)

References 23 publications

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“…At lower aging temperatures, the hardness remained almost constant owing to enhanced precipitation hardening over recovery and grain coarsening. Faré et al [32] also studied the aging behavior of the 6082 alloy processed by ECAP and asymmetric rolling. It was indicated that aging at 180 • C led to a fast aging process, resulting in a continuous drop in hardness with increasing time due to the overwhelming effects of structure restoration.…”

Section: Hardnessmentioning

confidence: 99%

Aging Behavior of Aluminum Alloy 6082 Subjected to Friction Stir Processing

Al‐Fadhalah

Asi

2018

Crystals

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The present work examined the effect of artificial aging on the microstructure, texture, and hardness homogeneity in aluminum alloy AA6082 subjected to friction stir processing (FSP). Aging was applied to FSP samples at three different temperatures (150 °C, 175 °C, and 200 °C) for a period of 1 h, 6 h, and 12 h. Microstructure analysis using optical Microscopy (OM) and Electron Back-Scattered Diffraction (EBSD) indicated that FSP produced fine equiaxed grains, with an average grain size of 6.5 μm, in the stir zone (SZ) due to dynamic recrystallization. Aging was shown to result in additional grain refinement in the SZ due to the occurrence of recovery and recrystallization with either increasing aging temperature and/or aging time. An optimum average grain size of 3–4 μm was obtained in the SZ by applying aging at 175 °C. This was accompanied by an increase in the fraction of high-angle grain boundaries. FSP provided a simple shear texture with a major component of B fiber. Increasing aging temperature and/or time resulted in the formation of recrystallization texture of a Cube orientation. In addition, Vickers microhardness was evaluated for the FSP sample, indicating a softening in the SZ due to the dissolution of the hardening precipitates. Compared to other aging temperatures, aging at 175 °C resulted in maximum hardness recovery (90 Hv) to the initial value of base metal (92.5 Hv). The hardness recovery is most likely attributed to the uniform distribution of fine hardening precipitates in the SZ when increasing the aging time to 12 h.

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Section: Hardnessmentioning

confidence: 99%

Aging Behavior of Aluminum Alloy 6082 Subjected to Friction Stir Processing

Al‐Fadhalah

Asi

2018

Crystals

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“…Consequently, this behavior can lead to the anticipation of the metastable β″/ β′ peak temperature, the creation of obvious peak of the GP zones and finally the reduction of Mg2Si and Si amount ratio in the eventually formed phases. Farè et al [15] and Vedani et al [16] have reported that the precipitation 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60 61 62 63 64 65 4 kinetics in Al-Mg-Si alloys depend on the strain accumulated during the ECAP process. They noticed that the diffraction peak positions and activation energies were a function of the ECAP passes, and explained how the precipitation kinetics in ultra fine grained (UFG) alloys was largely affected regarding the coarse-grained materials.…”

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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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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“…For both the mesh analysis and the subsequent ageing simulations, the overall microstructure has been set equal to 20 × 20 µm 2 . In order to insert a sufficient number of matrix phase grains, they are set to have a quite low average diameter, between 7.7 and 10 µm, which lies in the lower price range [26][27][28], while the ageing temperature does not permit recrystallisation to take place. It is worth noting that the applied values of the Al matrix grain diameter are not the same as the grain size estimated in the recrystallisation simulation.…”

Section: Isothermal Artificial Ageing Simulationmentioning

confidence: 99%

Phase Field Simulation of AA6XXX Aluminium Alloys Heat Treatment

Baganis

Bouzouni

Papaefthymiou

2021

Metals

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Heat treatment has a significant impact on the microstructure and the mechanical properties of Al-Mg-Si alloys. The present study presents a first Phase-Field modelling approach on the recrystallisation and grain growth mechanism during annealing. It focuses on the precipitate fraction, radius, and Mg-Si concentration in the matrix phase, which are used as input data for the calculation of the yield strength and hardness at the end of different ageing treatments. Annealing and artificial ageing simulations have been conducted on the MultiPhase-Field based MICRESS@ software, while the ThermoCalc@ software has been used to construct the pseudo-binary Al-Mg phase-diagrams and the atomic-mobility databases of MgxSiy precipitates. Recrystallisation simulation estimates the recrystallisation kinetics, the grain growth, and the interface mobility with the presence/absence of secondary particles, selecting as annealing temperature 400 °C and a microstructure previously subjected to cold rolling. The pinning force of secondary particles decelerates the overall recrystallisation time, causing a slight decrease in the final grain radius due to the reduction of interface mobility. The ageing simulation examines different ageing temperatures (180 and 200 °C) for two distinct ternary systems (Al-0.9Mg-0.6Si/Al-1.0Mg-1.1Si wt.%) considering the interface energy and the chemical free energy as the driving force for precipitation. The combination of Phase-Field and the Deschamps–Brechet model predicted the under-ageing condition for the 180 °C ageing treatment and the peak-ageing condition for the 200 °C ageing treatment.

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Aging Behaviour of Al-Mg-Si Alloys Subjected to Severe Plastic Deformation by ECAP and Cold Asymmetric Rolling

Cited by 30 publications

References 23 publications

Aging Behavior of Aluminum Alloy 6082 Subjected to Friction Stir Processing

Aging Behavior of Aluminum Alloy 6082 Subjected to Friction Stir Processing

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

Phase Field Simulation of AA6XXX Aluminium Alloys Heat Treatment

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