DEVELOPMENT OF HIGH STRENGTH ALUMINUM ALLOYS AND PROCESSING TECHNIQUES FOR THE MATERIALS

doi:10.11900/0412.1961.2014.00406

Acta Metall Sin

2015, Vol. 51

Issue (3): 257-271 DOI: 10.11900/0412.1961.2014.00406

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DEVELOPMENT OF HIGH STRENGTH ALUMINUM ALLOYS AND PROCESSING TECHNIQUES FOR THE MATERIALS

ZHANG Xinming(

), DENG Yunlai, ZHANG Yong

School of Materials Science and Engineering, Central South University, Changsha 410083

Cite this article:

ZHANG Xinming, DENG Yunlai, ZHANG Yong. DEVELOPMENT OF HIGH STRENGTH ALUMINUM ALLOYS AND PROCESSING TECHNIQUES FOR THE MATERIALS. Acta Metall Sin, 2015, 51(3): 257-271.

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Abstract

The fundamental theories for the development of high strength aluminum alloys and processing techniques for the materials are briefly reviewed in this paper. It specifically focuses on alloying design, casting, homogenization, solution treatment, quenching, pre-stretching and ageing that have been extensively studied recently. Based on these discussions, some perspectives and suggestions have been proposed, which will benefit the development and applications of high strength aluminum alloys.

Key words: high strength aluminum alloy aluminum structural material aluminum alloying design aluminum processing

Received: 30 June 2014

ZTFLH:

TG146.2

Fund: Supported by National Basic Research Program of China (No.2012CB619500)

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https://www.ams.org.cn/EN/10.11900/0412.1961.2014.00406 OR https://www.ams.org.cn/EN/Y2015/V51/I3/257

Table 1 Development of high strength aluminum alloys, typical properties, key techniques and microstructural characteristics

Fig.1 Crystal structures of GP zone (a), θ″ (b), θ′ (c) and θ phase (Al2Cu) (d) that may precipitate in aged binaryAl-Cu alloys (Light balls represent copper atoms and darker balls represent aluminum atoms)^[2]

Fig.2 A comparison of published C-curves corresponding to 90% maximum yield strength for different 7××× alloys^[36~38]

Fig.3 Processing-microstructure-property relationships for high strength aluminium alloys^[42]

Fig.4 Inhibiting of dislocation movement by fine dispersoids (a) in alloy AlZnMgCu-0.16Zr-0.2Cr-0.3Yb and resulting bowed sub-grain boundaries (b)^[50]

Fig.5 A comparison of exfoliation corrosion (EC) for alloy Al-7.81Zn-1.81Mg-1.62Cu under different thermomechanical processings^[60]

(a) 100 ℃, 12 h+warm rolling

(b) 200 ℃, 12 h+warm rolling

Fig.6 Mg content-hardness-quench sensitivity relationships for alloy Al-8Zn-xMg-1.6Cu^[70]

(a) hardness increases with increasing Mg content

(b) the alloy becomes more quench sensitive with increasing Mg content

Fig.7 Bright field (a) and dark field (b) TEM images showing the distribution of Al₃Zr dispersoids in the air cooled condition, and corresponding micro-beam-diffraction-pattern (MBDP) (c, d) in different grains with the incident electron-beam parallel to [011] Al₃Zr (The dark field image uses the diffraction spot from Al₃Zr dispersoids appearing at (100) positions, which are prohibited reflection positions for the face-centred cubic matrix)^[77]

图8 Al-3.48Cu-0.71Mg合金中的S与 ω 相^[82]

Fig.9 Distribution of the precipitates in alloy 2519Aafter different interrupt ageing processes^[100]
(a) T87 (b) T8I6 (c) T9I6

Fig.10 The volume fraction of recrystallization of alloy 7050 plate after solution treatment is affected by the cooling rates after homogenization^[107]

(a) water quenching

(b) cooling with furnace, arrows indicate particle stimulated nucleation

Fig.11 Schematic of retrogression and re-ageing (RRA) heat treatment

Fig.12 Effects of RRA heat treatment on hardness or yield strength^[126]

Fig.13 Effect of high temperature pre-precipitation on distribution of grain boundary precipitates in aluminum alloy 7A55^[127]

(a) 450 ℃, 30 min+480 ℃, 30 min

(b) 450 ℃, 30 min+480 ℃, 30 min + 400 ℃, 30 min

Fig.14 A airplane wing panel for Airbus A380^[137]

Fig.15 Precipitation of Al₂Cu in alloy Al-4Cu is affected by external stress direction during ageing^[139]

(a) ageing at 201 ℃, 4 h

(b) creep ageing at 201 ℃, 4 h, 40 MPa

Table 2 Development of high strength aluminum alloys in China

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