Effects of heat treatment on microstructure and tensile deformation of Mg AZ80 alloy at room temperature

Yakubtsov, I.A.; Diak, B.J.; Sager, C.A.; Bhattacharya, Baby; MacDonald, W. D.; Niewczas, M.

doi:10.1016/j.msea.2008.05.019

Cited by 130 publications

(51 citation statements)

References 20 publications

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“…The high atom content in solution was thought beneficial to reducing dislocation recovery events at room temperature and enhancing work hardening [33]. In the present study, the Al 2 Ca particle precipitated in the Mg-5Al-2Ca alloy, which possesses the high melting point of *1352 K [15].…”

Section: Work Hardening Behaviormentioning

confidence: 58%

Effect of Extrusion Temperature on the Microstructure and Mechanical Properties of Mg–5Al–2Ca Alloy

Deng

et al. 2015

Acta Metall. Sin. (Engl. Lett.)

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In this work, the Mg-5Al-2Ca alloy was extruded at 573, 623 and 673 K, with a ratio of 16:1 and a constant speed of 3 mm/s. Results demonstrate that the Al 2 Ca particle is formed in Mg-5Al-2Ca alloy. The size, amount and distribution of Al 2 Ca particles are influenced evidently by extrusion temperature. Unlike previous reports, the intensity of basal texture increases with increasing extrusion temperature, and the reasons are analyzed and given. Even though the average grain size increases as the extrusion temperature increased from 573 to 623 K, the YS, UTS and elongation of asextruded Mg-5Al-2Ca alloy are almost kept the same at 573 and 623 K. The reason is speculated as the balance of grain size, Al 2 Ca phase and texture at the two temperatures. The work hardening rate depends on extrusion temperature, and the largest h value of Mg-5Al-2Ca alloy is obtained when the extrusion was performed at 623 K.

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Section: Work Hardening Behaviormentioning

confidence: 58%

Effect of Extrusion Temperature on the Microstructure and Mechanical Properties of Mg–5Al–2Ca Alloy

Deng

et al. 2015

Acta Metall. Sin. (Engl. Lett.)

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“…Alloys with Al contents less than about 10wt.% exhibit eutectic morphologies that are referred to as partially or fully divorced [12][13] . A partially divorced eutectic morphology is characterized by 'islands' of eutectic α-Mg (dark spots) within the β-Mg 17 Al 12 phase, but the bulk of the α-Mg is still outside the Mg 17 Al 12 particle, as shown in Fig.1 (a) (position 1) [12] .…”

Section: As-cast Microstructurementioning

confidence: 99%

“…In addition, there is a fully divorced morphology where the two eutectic phases are completely separated. Each interdendritic region consists of a single β-Mg 17 Al 12 particle surrounded by 'eutectic' α-Mg, which has grown from the preferentially formed dendrites α-Mg [13] . As shown in Fig.1 (b) (position 2), however, the 'eutectic' α-Mg cannot be easily discerned.…”

Section: As-cast Microstructurementioning

confidence: 99%

Effect of solution treatment on microstructure and hardness of rheo-forming AZ91-Y alloy

2016

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M g-Al series alloys have been recognized as ideal materials for lightweight applications in the automotive industry with great development potential because of their low density, high specific strength and stiffness, and excellent cast-ability [1][2] . But their applications are still limited due to the intermetallic phase Mg 17 Al 12 of easy brittleness and unstable structure at elevated temperatures [3][4] . Some efforts have focused on adding some elements like Ca, Si, rare earth (RE) into the alloy matrix for generating new phases to limit the growth of β-Mg 17 Al 12 and modify its microstructure, and eventually improve the mechanical properties of Mg-Al series alloys [4][5][6][7] . Simultaneously, T6 treatment that can also achieve similar goals has attracted more attention due to its low cost and convenience. This is done by making Mg 17 Al 12 dissolved into α-Mg matrix and then precipitated once again.Semisolid metal (SSM) processing is recognized as Abstract:The microstructure and hardness of rheo-forming AZ91-Y alloy before and after solution treatment (ST) have been investigated by means of optical microscope (OM), scanning electron microscope (SEM) equipped with energy dispersive spectroscopy (EDS), X-ray diffraction (XRD) and Vickers. The experimental results showed that the β-Mg 17 Al 12 phase of alloy was nearly dissolved after ST for 5 min. With the increasing of ST duration to 28 h, both the primary and secondarily solidified α-Mg grains faded away. At the same time, the alloy exhibited a much smoother surface due to the diffusion of solute atoms (Al). During ST, the thermal stable phase of Al 2 Y produced by ultrasonic vibration retained its size and morphology. As the ST duration was increased, the alloy hardness decreased sharply at first, and then gradually reached a minimum level. an outstanding technique for Mg alloys. Its advantages are compared to the conventional die casting processes, including the potential of producing near-net shape and high-integrity components, low processing temperature that resolved the problem of oxidation, and effective burning in Mg alloys processing [8] . Several works have studied the microstructure evolution of AZ91D alloy fabricated by SSM processing during heat treatment [9][10] , but few studies related to the SSM processed Mg-Al series alloys containing RE have been reported. Also, it is well known that different casting processes will result in a variation of the microstructure, which could influence dissolution and precipitation kinetics of Mg 17 Al 12 during subsequent heat treatment. In this present study, solution treatment (ST) at 410 °C was used to process a rheo-forming AZ91-Y alloy. The aim was to detail the alloy's microstructure and hardness before and after ST, and to acquire the appropriate solution duration for subsequent aging treatment. The effect of RE (Y) on kinetics of Mg 17 Al 12 dissolution and the effect of the rheo-forming technique on alloy composition homogenization were also analyzed.

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“…The reason for this is that magnesium alloys have a HCP crystal structure with only two active and independent base slip systems and a relatively strong texture owing to their process rolling history, which allow only limited deformation [2]. Improvement of formability can be achieved by increasing the forming temperature and by applying appropriate heat treatments prior to forming [2,3,4]. Various studies on formability of magnesium alloys have been performed at room temperature and elevated temperatures.…”

Section: Introductionmentioning

confidence: 99%

Formability of Magnesium Alloys AZ80 and ZE10

Pasang

Satanin

Ramezani

et al. 2014

KEM

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Formability of two magnesium alloys, namely, AZ80 and ZE10, has been investigated. Both alloys were supplied with a thickness of 0.8 mm. The grain structure of the as-received AZ80 alloy showed dislocations, twins and second-phase particles and-/or precipitates distributed uniformly within grains. These were not obvious on the ZE10 alloy. The investigations were carried out at room temperature for both alloys in the as-received and heat treated conditions (410oC for 1 hour followed by water quench). The heat treatment significantly changed the grain structure of the AZ80 alloy, but did not affect the ZE10 alloy apart from grain enlargement. The formability was studied on the basis of plastic strain ratio (r) and strain hardening coefficient (n) by means of tensile testing. In the as-received condition, the ZE10 alloy had a slightly better formability () than AZ80 alloy. Following heat treatment, however, the formability of the AZ80 alloy was improved significantly (by about 26%), while the ZE10 alloy did not show any significant change.

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Effects of heat treatment on microstructure and tensile deformation of Mg AZ80 alloy at room temperature

Cited by 130 publications

References 20 publications

Effect of Extrusion Temperature on the Microstructure and Mechanical Properties of Mg–5Al–2Ca Alloy

Effect of Extrusion Temperature on the Microstructure and Mechanical Properties of Mg–5Al–2Ca Alloy

Effect of solution treatment on microstructure and hardness of rheo-forming AZ91-Y alloy

Formability of Magnesium Alloys AZ80 and ZE10

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