{111}/{111} Near Singular Boundaries in an Al-Zn-Mg-Cu Alloy Recrystallized After Rolling at Different Temperatures

doi:10.11900/0412.1961.2022.00027

Acta Metall Sin

2023, Vol. 59

Issue (7): 947-960 DOI: 10.11900/0412.1961.2022.00027

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{111}/{111} Near Singular Boundaries in an Al-Zn-Mg-Cu Alloy Recrystallized After Rolling at Different Temperatures

WANG Zongpu¹, WANG Weiguo¹^,²(

), Rohrer Gregory S³, CHEN Song¹^,², HONG Lihua¹^,², LIN Yan¹^,², FENG Xiaozheng¹, REN Shuai¹, ZHOU Bangxin⁴

¹Institute of Grain Boundary Engineering, Fujian University of Technology, Fuzhou 350118, China
²School of Materials Science and Technology, Fujian University of Technology, Fuzhou 350118, China
³Department of Materials Science and Engineering, Carnegie Mellon University, Pittsburgh, PA15213 -3890, USA
⁴Institute of Materials, Shanghai University, Shanghai 200072, China

Cite this article:

WANG Zongpu, WANG Weiguo, Rohrer Gregory S, CHEN Song, HONG Lihua, LIN Yan, FENG Xiaozheng, REN Shuai, ZHOU Bangxin. {111}/{111} Near Singular Boundaries in an Al-Zn-Mg-Cu Alloy Recrystallized After Rolling at Different Temperatures. Acta Metall Sin, 2023, 59(7): 947-960.

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Abstract

Recent development in grain boundary design and control indicates that manipulating the {111}/{111} near singular boundaries will be a promising pertinent to improve the performance against intergranular corrosion attacks for the high stacking fault energy face-centered cubic metals such as aluminum and its alloys. In the current study, five samples of a home-made Al-Zn-Mg-Cu super-high-strength aluminum alloy were rolled at temperatures of 250, 300, 350, 400, and 450^oC, followed by 30 min annealing at 520^oC. A method of grain boundary interconnection characterization based on electron backscatter diffraction and five parameter analysis was utilized to assess the {111}/{111} near singular boundaries in the samples as processed. The preceding rolling temperature was discovered to have a significant impact on the formation of {111}/{111} near singular boundaries during the subsequent annealing at 520^oC, that is, the fraction of {111}/{111} near singular boundaries out of the entire grain boundaries increases at first and then decreases as the preceding rolling temperature increases from 250^oC to 450^oC. In the five samples as processed, the one rolled at 300^oC followed by annealing at 520^oC has a peak content of {111}/{111} near singular boundaries and the fraction reaches 5.0%, which is 10 times higher compared to that of the singular boundaries or namely the coherent twin boundaries. Further investigations reveal that the sample rolled at 300^oC possesses a specific deformation substructure as well as suitable stored energy, resulting in continuous recrystallization during the successive annealing. This type of behavior aids in the formation of {111}/{111} near singular boundaries. The samples rolled at or above 350^oC, on the other hand, exhibit discontinuous dynamic recrystallization, which is detrimental to the development of {111}/{111} near singular boundaries during subsequent annealing. Compared to the sample rolled at 300^oC, the sample rolled at 250^oC has higher stored energy and it improves discontinuous recrystallization during the subsequent annealing. This also harms the formation of {111}/{111} near singular boundaries. Off-line in-situ surface etching test and high-resolution transmission electron microscope (HR-TEM) observation demonstrate that the {111}/{111} near singular boundaries have much higher resistance to intergranular corrosion in comparison to the random boundaries, they possess disclination structures of which the atomic ordering is much higher than that of the random boundaries. The results show that the {111}/{111} near singular boundary is regulable, and to further improving the fraction of such boundaries by manipulating the microstructure evolution will be effective in the practice of how reducing the intergranular corrosion in the aluminum and its alloys.

Key words: Al-Zn-Mg-Cu alloy super-high strength aluminum alloy near singular boundary grain boundary inter-connection intergranular corrosion

Received: 21 January 2022

ZTFLH:

TG113

Fund: National Natural Science Foundation of China(51971063);Special Program for Guiding Local Science and Technology Development by the Central Government(2019L3010)

Corresponding Authors: WANG Weiguo, professor, Tel: (0591)22863515, E-mail: wang_weiguo@vip.163.com

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	Articles by authors
	WANG Zongpu
	WANG Weiguo
	Rohrer Gregory S
	CHEN Song
	HONG Lihua
	LIN Yan
	FENG Xiaozheng
	REN Shuai
	ZHOU Bangxin

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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00027 OR https://www.ams.org.cn/EN/Y2023/V59/I7/947

Table 1 Samples and treatments of Al-Zn-Mg-Cu alloy

Fig.1 Orientation imaging microscopy (OIM) images (a, d, g, j, m), grain boundary networks (GBN) maps (b, e, h, k, n), and misorientation distributions (MD) (c, f, i, l, o) for the samples A (a-c), B (d-f), C (g-i), D (j-l), and E (m-o) (Black arr-ows in Figs.1b and h show the fine grains developed from the nucleus of discontinuous recrystallization (DRX); black and red dotted lines in Figs.1d and e show the banded grain clusters came from continuous recrystallization (CRX); red arrows in Figs.1k and n show the grains of abnormal growth; red-dotted-line circle areas show the relative fine grains produced by DRX)

Table 2 After-filtration statistics of the grain boundaries with the rotation axes of <111>, <112>, and <122> in the samples A-E

Fig.2 Misorientation distributions of grain boundaries with specific rotation axes for the samples A-E
(a) rotation around <111> (b) rotation around <112> (c) rotation around <122>

Fig.3 Five parameter grain boundary plane distributions of {111}/{111} near singular boundary (NSB) with varied misorientations in the sample A (MRD—multiple of random distribution)
(a) [111]/20° (b) [111]/45° (c) [111]/50° (d) [112]/30° (e) [122]/35°

Fig.4 Five parameter grain boundary plane distributions of {111}/{111}-NSB with varied misorientations in the sample B
(a) [111]/15° (b) [111]/35° (c) [111]/40°
(d) [111]/45° (e) [111]/50° (f) [111]/55°
(g) [112]/15° (h) [112]/30° (i) [112]/40°
(j) [122]/25° (k) [122]/30° (l) [122]/35°

Fig.5 Five parameter grain boundary plane distributions of {111}/{111}-NSB with varied misorientations in the sample C
(a) [111]/20° (b) [111]/25° (c) [111]/30° (d) [111]/50° (e) [122]/20° (f) [122]/25° (g) [122]/35°

Table 3 Statistics of the {111}/{111}-NSB in the samples A-E

Fig.6 Length fractions of {111}/{111}-NSB and singular boundary (SB) in the samples A-E

Fig.7 Five parameter grain boundary plane distributions of Σ3 (<111>/60°) boundaries in the samples A (a), B (b), and C (c)

Fig.8 OIM images of the areas containing {111}/{111}-NSB (a, d), grain boundary trace analyses for {111}/{111}-NSB based on {111} overlapped pole figures (b, e), and morphologies of {111}/{111}-NSB after off-line in-situ surface etching (c, f) (LAGB—low angle grain boundary, RB—random boundary, A—grain A, B—grain B, C—grain C, D—grain D) (a-c) {111}/{111}-NSB (GB_AB) with a misorientation of [1 $1 ¯$ 1]/45.4° (d-f) {111}/{111}-NSB (GB_CD) with a misorientation of [ $1 ¯$ 11]/33.7°

Fig.9 High resolution transmission electron microscopy (HRTEM) images and selected area electron diffraction (SAED) patterns (insets) of {111}/{111}-NSB in the Al-Zn-Mg-Cu alloy (d_{111}—{111} interplanar spacing)
(a) {111}/{111}-NSB with a misorientation of [111]/40.7°
(b) {111}/{111}-NSB with a misorientation of [1

1 ¯ 1 ¯

]/29.7°

Fig.10 OIM images of samples A₁ (a), B₁ (b), and C₁ (c)

Fig.11 Misorientation distributions of samples A₁ (a), B₁ (b), and C₁ (c)

Fig.12 Vickers hardnesses of samples A₁-E₁

1	Dursun T, Soutis C. Recent developments in advanced aircraft aluminium alloys [J]. Mater. Des., 2014, 56: 862 doi: 10.1016/j.matdes.2013.12.002
2	Georgantzia E, Gkantou M, Kamaris G S. Aluminium alloys as structural material: A review of research [J]. Eng. Struct., 2021, 227: 111372 doi: 10.1016/j.engstruct.2020.111372
3	Liu Y R, Pan Q L, Li H, et al. Revealing the evolution of microstructure, mechanical property and corrosion behavior of 7A46 aluminum alloy with different ageing treatment [J]. J. Alloys Compd., 2019, 792: 32 doi: 10.1016/j.jallcom.2019.03.324
4	Bai F, Gao W L, He Z L, et al. Effect of ageing processes on mechanical properties and intergranular corrosion of 7A85 aluminum alloy [J]. Chin. J. Nonferrous Met., 2016, 26: 957
	柏璠, 高文理, 何正林等. 时效工艺对7A85铝合金力学和晶间腐蚀性能的影响 [J]. 中国有色金属学报, 2016, 26: 957
5	Li J H, Li F G, Ma X K, et al. Effect of grain boundary characteristic on intergranular corrosion and mechanical properties of severely sheared Al-Zn-Mg-Cu alloy [J]. Mater. Sci. Eng., 2018, A732: 53
6	Zhang Z, Deng Y L, Ye L Y, et al. Influence of aging treatments on the strength and localized corrosion resistance of aged Al-Zn-Mg-Cu alloy [J]. J. Alloys Compd., 2020, 846: 156223 doi: 10.1016/j.jallcom.2020.156223
7	Rao A C U, Vasu V, Govindaraju M, et al. Stress corrosion cracking behaviour of 7xxx aluminum alloys: A literature review [J]. Trans. Nonferrous Met. Soc. China, 2016, 26: 1447 doi: 10.1016/S1003-6326(16)64220-6
8	Xie P, Chen S Y, Chen K H, et al. Enhancing the stress corrosion cracking resistance of a low-Cu containing Al-Zn-Mg-Cu aluminum alloy by step-quench and aging heat treatment [J]. Corros. Sci., 2019, 161: 108184 doi: 10.1016/j.corsci.2019.108184
9	Marlaud T, Deschamps A, Bley F, et al. Evolution of precipitate microstructures during the retrogression and re-ageing heat treatment of an Al-Zn-Mg-Cu alloy [J]. Acta Mater., 2010, 58: 4814 doi: 10.1016/j.actamat.2010.05.017
10	Wang W Y, Pan Q L, Wang X D, et al. Non-isothermal aging: A heat treatment method that simultaneously improves the mechanical properties and corrosion resistance of ultra-high strength Al-Zn-Mg-Cu alloy [J]. J. Alloys Compd., 2020, 845: 156286 doi: 10.1016/j.jallcom.2020.156286
11	Cai B, Adams B L, Nelson T W. Relation between precipitate-free zone width and grain boundary type in 7075-T7 Al alloy [J]. Acta Mater., 2007, 55: 1543 doi: 10.1016/j.actamat.2006.10.015
12	Martinez-Lombardia E, Lapeire L, Maurice V, et al. In situ scanning tunneling microscopy study of the intergranular corrosion of copper [J]. Electrochem. Commun., 2014, 41: 1 doi: 10.1016/j.elecom.2014.01.007
13	Aust K T. Grain boundary engineering [J]. Can. Metall. Quart., 1994, 33: 265 doi: 10.1179/cmq.1994.33.4.265
14	Du A H, Wang W G, Gu X F, et al. The dependence of precipitate morphology on the grain boundary types in an aged Al-Cu binary alloy [J]. J. Mater. Sci., 2021, 56: 781 doi: 10.1007/s10853-020-05239-5
15	Wang W G, Zhou B X, Rohrer G S, et al. Textures and grain boundary character distributions in a cold rolled and annealed Pb-Ca based alloy [J]. Mater. Sci. Eng., 2010, A527: 3695
16	Prithiv T S, Bhuyan P, Pradhan S K, et al. A critical evaluation on efficacy of recrystallization vs. strain induced boundary migration in achieving grain boundary engineered microstructure in a Ni-base superalloy [J]. Acta Mater., 2018, 146: 187 doi: 10.1016/j.actamat.2017.12.045
17	Liu Z Q, Wang W G. Study on Σ3 boundaries in an cold rolled and recrystallized Al-Cu alloy [J]. J. Chin. Electron Microsc. Soc., 2018, 37: 232
	刘智强, 王卫国. 冷轧变形Al-Cu合金再结晶Σ3晶界研究 [J]. 电子显微学报, 2018, 37: 232
18	Fang H C, Chao H, Chen K H. Effect of Zr, Er and Cr additions on microstructures and properties of Al-Zn-Mg-Cu alloys [J]. Mater. Sci. Eng., 2014, A610: 10
19	Wang W G, Cai C H, Rohrer G S, et al. Grain boundary inter-connections in polycrystalline aluminum with random orientation [J]. Mater. Charact., 2018, 144: 411 doi: 10.1016/j.matchar.2018.07.040
20	Janssens K G F, Olmsted D, Holm E A, et al. Computing the mobility of grain boundaries [J]. Nat. Mater., 2006, 5: 124 pmid: 16400330
21	Ashrafizadeh S M, Eivani A R, Jafarian H R, et al. Improvement of mechanical properties of AA6063 aluminum alloy after equal channel angular pressing by applying a two-stage solution treatment [J]. Mater. Sci. Eng., 2017, A687: 54
22	Rohrer G S, Saylor D M, Dasher B E, et al. The Distribution of Internal Interfaces in Polycrystals [J]. Z. Metallkd., 2004, 95: 197 doi: 10.3139/146.017934
23	Wang W G, Du A H, Yang X M, et al. Quantitative determination of grain boundary inter-connections [P]. Chin Pat, 202011173146.8, 2021
	王卫国, 杜阿华, 杨先明等. 晶界界面匹配定量表征方法 [P]. 中国专利, 202011173146.8, 2021))
24	Yang X M, Wang W G, Gu X F. The near singular boundaries in BCC iron [J]. Philos. Mag., 2022, 102: 440 doi: 10.1080/14786435.2021.2004327
25	Wright S I, Larsen R J. Extracting twins from orientation imaging microscopy scan data [J]. J. Microsc., 2002, 205: 245 doi: 10.1046/j.1365-2818.2002.00992.x
26	Mackenzie J K. Second paper on statistics associated with the random disorientation of cubes [J]. Biometrika, 1958, 45: 229 doi: 10.1093/biomet/45.1-2.229
27	Xie B C, Zhang B Y, Ning Y Q, et al. Mechanisms of DRX nucleation with grain boundary bulging and subgrain rotation during the hot working of nickel-based superalloys with columnar grains [J]. J. Alloys Compd., 2019, 786: 636 doi: 10.1016/j.jallcom.2019.01.334
28	Yang Y, Zhou K, Li G J. Surface gradient microstructural characteristics and evolution mechanism of 2195 aluminum lithium alloy induced by laser shock peening [J]. Opt. Laser Technol., 2019, 109: 1 doi: 10.1016/j.optlastec.2018.07.041
29	Li J C M. Disclination model of high angle grain boundaries [J]. Surf. Sci., 1972, 31: 12 doi: 10.1016/0039-6028(72)90251-8
30	Klimanek P, Klemm V, Romanov A E, et al. Disclinations in plastically deformed metallic materials [J]. Adv. Eng. Mater., 2001, 3: 877 doi: 10.1002/1527-2648(200111)3:11<877::AID-ADEM877>3.0.CO;2-L
31	Zhao J H, Deng Y L, Tang J G. Grain refining with DDRX by isothermal MDF of Al-Zn-Mg-Cu alloy [J]. J. Mater. Res. Technol., 2020, 9: 8001 doi: 10.1016/j.jmrt.2020.05.033
32	Gao W L, Bai G R, Luan G F, et al. A criterion for dynamic recrystallization in metals' hot working [J]. J. Northeast Univ. Technol., 1993, 14: 49
	高维林, 白光润, 栾瑰馥等. 金属热变形中动态再结晶的临界判据 [J]. 东北工学院学报, 1993, 14: 49
33	Gao W L, Bai G R, Zhou Z M. An evolution model of dislocation patterns in plastic deformation and its applications [J]. Sci. China, 1995, 38A: 875
	高维林, 白光润, 周志敏. 金属塑性变形中位错组态演化模型及其应用 [J]. 中国科学, 1994, 24A: 1225

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