Journal of Alloys and Compounds

2017

DOI: 10.1016/j.jallcom.2017.09.060

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Development of intermetallic particles during solidification and homogenization of two AA 5xxx series Al-Mg alloys with different Mg contents

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Jochen Hasenclever

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Introduction4

Superplastic Tensile Tests1

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Cited by 87 publications

(53 citation statements)

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“…Superplastic tensile tests focused on investigating the states of cavity in superplastic deformation of the studied 5A70 alloy. Superplastic tensile tests of FG 5A70 alloy were performed at an initial strain rate of 1 × 10 −3 s −1 and the temperatures ranged from to 550 • C, according to relevant literature and thermal analysis experimental results [21]. The true stress-true strain results of the superplastic tensile tests are shown in Figure 1a.…”

Section: Superplastic Tensile Testsmentioning

confidence: 99%

Cavity Behavior of Fine-Grained 5A70 Aluminum Alloy during Superplastic Formation

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2018

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The study of the exact physical mechanism of cavity nucleation and growth is significant in terms of predicting the extent of internal damage following superplastic deformation. The 5A70 alloy was processed by cold rolling for 14 passes with a total reduction deformation of 90% (20–2 mm) and the heat treatment was inserted at a thickness of 10 and 5 mm at 340 °C for 30 min. The superplastic tensile tests were performed at 400, 450, 500, 550 °C and the initial strain rate was 1 10−3 s−1. Cavities were observed at the head of the particle and the interface of the grain boundaries. It is suggested that the cavity was nucleated during the sliding/climbing of the dislocations, due to the precipitate pinning effect and the impeding grain boundary during grain boundary sliding (GBS). In this study, the results demonstrated a clear transition from diffusion growth to superplastic diffusion growth and plastic-controlled growth at a cavity radius larger than 1.52 and 13.90 μm. The cavity nucleation, growth, interlinkage and coalescence under the applied stress during the superplastic deformation, as well as the crack formation and expansion during the deformation, ultimately led to the superplastic fracture.

“…Superplastic tensile tests focused on investigating the states of cavity in superplastic deformation of the studied 5A70 alloy. Superplastic tensile tests of FG 5A70 alloy were performed at an initial strain rate of 1 × 10 −3 s −1 and the temperatures ranged from to 550 • C, according to relevant literature and thermal analysis experimental results [21]. The true stress-true strain results of the superplastic tensile tests are shown in Figure 1a.…”

Section: Superplastic Tensile Testsmentioning

confidence: 99%

Cavity Behavior of Fine-Grained 5A70 Aluminum Alloy during Superplastic Formation

¹

,

²

,

³

2018

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The study of the exact physical mechanism of cavity nucleation and growth is significant in terms of predicting the extent of internal damage following superplastic deformation. The 5A70 alloy was processed by cold rolling for 14 passes with a total reduction deformation of 90% (20–2 mm) and the heat treatment was inserted at a thickness of 10 and 5 mm at 340 °C for 30 min. The superplastic tensile tests were performed at 400, 450, 500, 550 °C and the initial strain rate was 1 10−3 s−1. Cavities were observed at the head of the particle and the interface of the grain boundaries. It is suggested that the cavity was nucleated during the sliding/climbing of the dislocations, due to the precipitate pinning effect and the impeding grain boundary during grain boundary sliding (GBS). In this study, the results demonstrated a clear transition from diffusion growth to superplastic diffusion growth and plastic-controlled growth at a cavity radius larger than 1.52 and 13.90 μm. The cavity nucleation, growth, interlinkage and coalescence under the applied stress during the superplastic deformation, as well as the crack formation and expansion during the deformation, ultimately led to the superplastic fracture.

“…Various researches have been performed to investigate the microstructure and phase identification during the solidification in 5xxx aluminum alloys. The main intermetallic phases formed during solidification of this series were reported to be Al6(Mn,Fe), α-Al(Fe,Mn)Si, Al3Fe and Alm(Mn, Fe) [3][4][5][6][7][8][9][10][11]. Alloys with 3% Mg content or higher display the formation of β-Al5Mg3 or τ-Al6CuMg4 [3].…”

Section: Introductionmentioning

confidence: 99%

“…The solidified microstructure of AA5083 alloy is found to be composed of two main iron-rich phases, which are Al6(Mn,Fe), α-Al(Fe,Mn)Si with minor ε-Al18(Cr,Mn)2Mg3 and eutectic β-Al5Mg3 or τ-Al6CuMg4 [6]. Studies showed that the dominant Fe-rich phases of the as-cast AA5754 alloy are changed to Al3(Fe,Mn) and α-Al(Fe,Mn)Si, and only Al3(Fe,Mn) phase with Fe:Mn ratio of about 5 in AA5182 alloy [7,10]. However, most of literatures focused on the alloys with a high Mg range (4-5%), such as 5083, 5182 and 5457 alloys, and there are also controversies on the formation of different intermetallic phases.…”

Section: Introductionmentioning

confidence: 99%

Formation of intermetallic phases during solidification in Al-Mg-Mn 5xxx alloys with various Mg levels

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2020

MATEC Web Conf.

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In the present study, four Al-Mg-Mn 5xxx alloys with different Mg levels (2-5 wt.%) were investigated for better understanding the evolution of intermetallic phases formed during solidification. Optical and scanning electron microscopes, electron backscattered diffraction and differential scanning calorimetry analyses in combination with thermodynamic calculation were used to identify various intermetallic phases. Results showed that the most dominant intermetallic phases are Al6(Mn,Fe), α-Al(Fe,Mn)Si, Al3Fe, Alm(Mn,Fe) and Mg2Si in experimental Al-Mg-Mn alloys, which is greatly dependant on the Mg levels. It is found that Chinese script α-Al(Fe,Mn)Si is the dominant iron-rich intermetallic phase for the alloys containing 2-3 wt.% Mg, while blocky Al6(Mn,Fe) and needle-like Al3(Mn,Fe) become the major phases for the alloy containing 4 wt.% Mg. Further increasing Mg content to 5 wt. %, the dominant phase transfers to blocky Al6(Mn,Fe) intermetallic. Meanwhile, the morphology of primary Mg2Si is changed from well-branched to plate-like with increasing Mg contents. In addition, β-Al3Mg2 and τ-Al6CuMg4 eutectic phases have been observed in the alloys with 3-5 wt. % Mg. A comparison on various intermetallic phases from the Scheil simulation and the actual as-cast microstructure is provided.

“…However, the low hardness of these alloys limits their use for some applications [7]. As a consequence of this, alloys of Al-Mg + M (M = Fe, Si, Cu, Cr, Mn, Zn, Zr, and Ti) have been developed to increase the hardness [3,6,8,9].…”

Section: Introductionmentioning

confidence: 99%

Microstructure and microhardness of the Al-10Mg alloy processed by the mechanical alloying technique

Sánchez-Cuevas

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Zárate‐Medina

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Mercado-Zúñiga³

et al. 2020

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In this work, the Al-10Mg nanostructured alloy was synthesized by high-energy mechanical milling. Subsequently, the powders consolidated under a uniaxial pressing in the air. The as milled powders were analyzed using scanning electron microscopy (SEM), transmission electron microscopy (TEM), X-ray diffraction (XRD) and differential scanning calorimetry (DSC). SEM and XRD also characterized the sintered samples. Vickers microhardness of sintered Al-10Mg alloy was measured. SEM, XRD, and TEM characterizations show that the Al-10Mg alloy was synthesized after 10 h milling. The X-ray powder analysis of the structural parameters showed the increment with the time of the lattice parameter, strain as well as the solubility of Mg in Al. Besides, XRD and TEM studies showed that the crystallite size was reaching an average value of 19 nm after 10 h milling. XRD patterns of the all sintered specimens show the formation of the MgAl2O4 spinel phase. After powders compaction, the specimen sintered at 420?C for 2 h shows microhardness of 125 HV.

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