Strengthening study on 6082 Al alloy after combination of aging treatment and ECAP process

Dadbakhsh, Sasan; Taheri, Ali; Smith, C. R.

doi:10.1016/j.msea.2010.04.017

Cited by 95 publications

(50 citation statements)

References 32 publications

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“…25 Thus, high strain-rate sensitivity indices lead to higher postnecking elongation or superplasticity. 1 The obtained results show that the strain-rate sensitivity index depends on the dominant deformation mechanisms. 26 Our m values may suggest that the deformation mechanism is related to conventional dynamic recovery (DRV) and/or controlled dislocation creep.…”

Section: Strain-rate Sensitivitymentioning

confidence: 81%

“…However, the increase in temperature may also cause microstructural changes such as precipitation, strain aging, or grain growth that may affect this general behavior. 1 Third, with increasing the temperature, the maximum in elongation values shifted to higher strain rates, especially at 500°C. This trend has also been observed during the deformation of severe plastic deformed alloys such as AA7034, 19 ZK60 magnesium alloy, 20 and Ti-6Al-4V.…”

Section: Elongation To Failurementioning

confidence: 89%

“…1 One of the most often used processes in this regard is equal-channel angular pressing (ECAP), which provides an opportunity for producing bulk UFG materials, although its application has remained in the laboratory scales. 2 Also, because of the limits dictated by ECAP, the shapes and sizes of the workpieces are far from the semifinal products required for industrial applications.…”

Section: Introductionmentioning

confidence: 99%

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Modeling the Hot Ductility of AA6061 Aluminum Alloy After Severe Plastic Deformation

Khamei

Dehghani

Mahmudi

2015

JOM

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Solutionized AA6061 aluminum alloy was processed by equal-channel angular pressing followed by cold rolling. The hot ductility of the material was studied after severe plastic deformation. The hot tensile tests were carried out in the temperature range of 300-500°C and at the strain rates of 0.0005-0.01 s À1 . Depending on the temperature and strain rate, the applied strain level exhibited significant effects on the hot ductility, strain-rate sensitivity, and activation energy. It can be suggested that the possible mechanism dominated the hot deformation during tensile testing is dynamic recovery and dislocation creep. Constitutive equations were developed to model the hot ductility of the severe plastic deformed AA6061 alloy.

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Section: Strain-rate Sensitivitymentioning

confidence: 81%

Section: Elongation To Failurementioning

confidence: 89%

Section: Introductionmentioning

confidence: 99%

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Modeling the Hot Ductility of AA6061 Aluminum Alloy After Severe Plastic Deformation

Khamei

Dehghani

Mahmudi

2015

JOM

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“…Al-Mg-Si alloys are widely used for demanding structural applications due to their good physical and chemical properties [1][2][3]. The alloy with the designation AA6082 is optimized to be the strongest alloy in the family.…”

Section: Introductionmentioning

confidence: 99%

Controlling the high temperature mechanical behavior of Al alloys by precipitation and severe straining

Cepeda-Jiménez

Castillo-Rodríguez

Molina-Aldareguia

et al. 2017

Materials Science and Engineering: A

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The aim of this work was to investigate the influence of the precipitate distribution on the microstructure and on the room and high temperature mechanical properties of an age-hardenable aluminium AA6082 alloy following severe straining by high-pressure torsion (HPT). With this goal, specimens in the as-cast and T6 peak-aged conditions were processed by HPT using 0.5, 1 and 5 turns at room temperature. At high strain levels (J>100), similar saturation grain sizes (~250 nm), high-angle boundary fractions (~80%) and hardness values (Hv~160) were obtained for both initial conditions. Grain refinement led to significant strengthening and to good ductility values at room temperature. Analysis by TEM and EDS elemental mapping revealed that HPT processing of the as-cast condition led to fracture of the stable E-phase into many small precipitates located preferentially along grain boundaries and triple junctions. By contrast, HPT processing of the T6 peak-aged specimens revealed a partial dissolution of the needle-shaped nanoprecipitates. The different evolutions of the precipitate distributions following straining in the as-cast and peak-aged conditions gave rise to dramatic differences in the mechanical properties and the operative deformation mechanisms at warm temperatures. These results provide evidence that the high temperature mechanical behavior of age-hardenable Al alloys may be conveniently controlled by altering the precipitate distribution followed by severe straining.

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“…Despite this difficulty, as the age-hardenable Al alloys are of high performance in aerospace applications, there is a growing interest in process these alloys by ECAP and combining the nanocrystalline microstructure with a good control of the precipitation hardening 11,[13][14][15][16] . Recently, Chinh et al 10 developed a strategy for processing these alloys by ECAP at room temperature and found that the pressing may be conducted successfully, without the formation of catastrophic cracking or segmentation, if performed immediately after quenching from the solution treatment temperature or at least within a very short pre-aging time 12,17 .…”

Section: Introductionmentioning

confidence: 99%

Microstructure evolution of AA7050 Al alloy during Equal-Channel Angular Pressing

et al. 2012

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High strength AA7050 aluminum alloy was processed by ECAP through route A in the T7451 condition. Samples were processed at 423 K, with 1 and 3 passes. The resulting microstructure was evaluated by optical microscopy (OM), scanning electron microscopy (SEM) and transmission electron microscopy (TEM). The phases were identified by X-ray diffraction (XRD) using monochromatic Cu Kα radiation. Rockwell B hardness and tensile tests were performed for assessment of mechanical properties. The microstructure was refined by the formation of deformation bands, with dislocation cells and elongated subgrains, with an average width of 240 nm, inside these bands. The number of deformation bands increased with the number of passes. A reduction of precipitates size was observed with increase in the number of passes, when compared to initial condition, probably resulting from particle fragmentation during ECAP. After three passes the precipitates tend to a more equiaxed morphology and have sizes smaller than 10 nm. Phases η' and η coexist in the microstructure, but η is the dominant phase, mainly after three passes. The hardness of alloy after the first pass of ECAP is almost equal to the initial condition. After three passes the hardness showed a slight reduction which must be result from recovery process. There was a slight improvement in the yield strength and elongation after one pass, when compared to the initial T7451 condition. The improvement in the ultimate tensile strength was less significant.

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Strengthening study on 6082 Al alloy after combination of aging treatment and ECAP process

Cited by 95 publications

References 32 publications

Modeling the Hot Ductility of AA6061 Aluminum Alloy After Severe Plastic Deformation

Modeling the Hot Ductility of AA6061 Aluminum Alloy After Severe Plastic Deformation

Controlling the high temperature mechanical behavior of Al alloys by precipitation and severe straining

Microstructure evolution of AA7050 Al alloy during Equal-Channel Angular Pressing

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