Non-isothermal precipitation kinetics and its effect on hot working behaviors of an Al–Zn–Mg–Cu alloy

Jiang, Fulin; Zhang, Hui

doi:10.1007/s10853-017-1691-4

Cited by 16 publications

(4 citation statements)

References 27 publications

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“…For the NA7d-TMT samples, it can be speculated that the natural aging clusters or the precursors of Si-modified GPB zone must affect the movement and reaction of dislocations during the subsequent cold rolling. Owing to the pinning effect of uniform small precipitates or clusters [36] and their inhibitory effect on dynamic recovery during deformation [37][38][39], a higher density of dislocations should be uniformly stored in the as-rolled TMT alloy, which further provides larger amount of nucleation sites and reduces the size of dislocation-induced precipitates. Besides, it was believed that the unstable NA clusters will dissolve into the matrix, and the stable NA clusters promote the precipitation of the Si-modified GPB zone by acting as nucleation sites of the strengthening precipitates during the subsequent aging process [40,41].…”

Section: Discussionmentioning

confidence: 99%

Improved Properties in Relation to Fine Precipitate Microstructures Tailored by Combinatorial Processes in an Al–Cu–Mg–Si Alloy

Niu

Chen

et al. 2020

Acta Metall. Sin. (Engl. Lett.)

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The 2xxx series Al alloys have been widely used in aerospace industry owing to their high strength, good plasticity and superior formability. To ensure a good control of shape, the quenched alloy sheets require a small pre-deformation before artificial aging. However, this pre-deformation considerably deteriorates the mechanical strength of the Al-3.0Cu-1.8Mg-0.5Si (wt%) alloys due to the formation of unfavorable large-sized precipitates at dislocations. To tackle this issue, we designed a pre-aging process prior to the pre-deformation. The thermal-mechanical treatment, involving pre-aging, pre-deformation and subsequent aging, markedly enhanced the ultimate tensile strength up to 521 MPa compared to that (448 MPa) of the alloy without pre-aging. Microstructure characterization revealed that the fine precipitates (~ 2 nm) with a uniform dispersion were promoted within the Al matrix, which in turn partly suppressed the formation of the unfavorable large-sized precipitate (~ 100 nm). Our findings provide a new clue for designing stronger Al alloys with age-hardenability.

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Section: Discussionmentioning

confidence: 99%

Improved Properties in Relation to Fine Precipitate Microstructures Tailored by Combinatorial Processes in an Al–Cu–Mg–Si Alloy

Niu

Chen

et al. 2020

Acta Metall. Sin. (Engl. Lett.)

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“…This abnormal evolution is either due to the inherent high resistivity of the T 1 phase according to [15] or to the presence of strain fields around the precipitates that act as electron scattering centers [16][17][18][19]. The methodology proposed by [20] and based on the Matthiessen equation has been used to calculate the evolution of the relative volume fraction of the T 1 phase according to the evolution of electrical resistivity. First, the electrical resistivity is considered to be dominated by the contribution of solutes atoms and precipitates as expressed in Equation ( 1):…”

Section: Monitoring T 1 Precipitate Evolution Using Electrical Resist...mentioning

confidence: 99%

Modeling Hardness Evolution during the Post-Welding Heat Treatment of a Friction Stir Welded 2050-T34 Alloy

et al. 2022

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A unified constitutive model of yield strength evolution during heat treatment has been revised to simulate the hardness evolution during the post-welding heat treatment of AA2050-T34 Friction Stir Welded (FSW) plates. The model considers the strengthening by dislocations, solid solution, clusters, and the T1 phase. As a result, the successful prediction of yield strength evolution during the aging of AA2050 with different initial tempers has been achieved. The kinetics of precipitation of the T1 phase during heat treatment has been characterized by electrical resistivity on the unwelded and FSW samples. The obtained results have been used to check the ability of the model to simulate the evolution of the relative volume fraction of the T1 phase and hardness during the post-welding heat treatment in the different zones of FSW samples. Despite some observed discrepancies on the top and bottom of the weld joint, the revised numerical model captures well the overall hardness profile after the post-weld heat treatment.

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“…Sun et al observed that the large second-phase particles in 7075 alloy would hinder the slip of subgrain boundaries, while the small second-phase particles would promote continuous dynamic recrystallization through rotation of subgrain [ 20 ]. Jiang et al observed that the degree of initial supersaturation controlled the nucleation rates and strongly influenced the dynamic and static precipitation, and the flow stress curves [ 21 ]. In general, it has been proved in recent years that the hot deformation parameters affect the dynamic precipitation mechanism, and at the same time, the precipitation has an effect on the deformation structure, texture and recrystallization of the alloy [ 8 , 19 , 20 , 21 , 22 , 23 , 24 , 25 ].…”

Section: Introductionmentioning

confidence: 99%

“…Jiang et al observed that the degree of initial supersaturation controlled the nucleation rates and strongly influenced the dynamic and static precipitation, and the flow stress curves [ 21 ]. In general, it has been proved in recent years that the hot deformation parameters affect the dynamic precipitation mechanism, and at the same time, the precipitation has an effect on the deformation structure, texture and recrystallization of the alloy [ 8 , 19 , 20 , 21 , 22 , 23 , 24 , 25 ]. However, the existence forms of different second phases under different hot deformation parameters and their effects on the hot deformation behavior of alloys has scarcely been studied.…”

Section: Introductionmentioning

confidence: 99%

Evolution of Grain Structure and Dynamic Precipitation during Hot Deformation in a Medium-Strength Al-Zn-Mg-Er-Zr Aluminum Alloy

Chen

Wei

et al. 2023

Materials

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The hot deformation behavior of Al-Zn-Mg-Er-Zr alloy was investigated through an isothermal compression experiment at a strain rate ranging from 0.01 to 10 s−1 and temperature ranging from 350 to 500 °C. The constitutive equation of thermal deformation characteristics based on strain was established, and the microstructure (including grain, substructure and dynamic precipitation) under different deformation conditions was analyzed. It is shown that the steady-state flow stress can be described using the hyperbolic sinusoidal constitutive equation with a deformation activation energy of 160.03 kJ/mol. Two kinds of second phases exist in the deformed alloy; one is the η phase, whose size and quantity changes according to the deformation parameters, and the other is spherical Al3(Er, Zr) particles with good thermal stability. Both kinds of particles pin the dislocation. However, with a decrease in strain rate or increase in temperature, η phases coarsen and their density decreases, and their dislocation locking ability is weakened. However, the size of Al3(Er, Zr) particles does not change with the variation in deformation conditions. So, at higher deformation temperatures, Al3(Er, Zr) particles still pin dislocations and thus refine the subgrain and enhance the strength. Compared with the η phase, Al3(Er, Zr) particles are superior for dislocation locking during hot deformation. A strain rate ranging from 0.1 to 1 s−1 and a deformation temperature ranging from 450 to 500 °C form the safest hot working domain in the processing map.

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Non-isothermal precipitation kinetics and its effect on hot working behaviors of an Al–Zn–Mg–Cu alloy

Cited by 16 publications

References 27 publications

Improved Properties in Relation to Fine Precipitate Microstructures Tailored by Combinatorial Processes in an Al–Cu–Mg–Si Alloy

Improved Properties in Relation to Fine Precipitate Microstructures Tailored by Combinatorial Processes in an Al–Cu–Mg–Si Alloy

Modeling Hardness Evolution during the Post-Welding Heat Treatment of a Friction Stir Welded 2050-T34 Alloy

Evolution of Grain Structure and Dynamic Precipitation during Hot Deformation in a Medium-Strength Al-Zn-Mg-Er-Zr Aluminum Alloy

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