Microstructure structure and mechanical properties of coherent precipitation strengthened ultrahigh strength maraging stainless steel

YANG Yuxian; WANG Zhenhua; WANG Qing; TANG Caiyu; WAN Peng; CAO Dahua; DONG Chuang

doi:10.7498/aps.74.20241483

Abstract

Ultra-high strength maraging stainless steels possess many important applications such as in aircraft landing gears owing to their excellent strength and good process ability. However, traditional ultra-high strength maraging stainless steels are facing the challenge of balancing strength and ductility while pursuing ultra-high strength. This is mainly due to the semi-coherent or non-coherent relationship between the precipitated nanoparticles and the body-centered cubic (BCC) martensitic matrix. In this work, a novel ultra-high strength maraging stainless steel (Fe-7.95Cr-13.47Ni-3.10Al-1.83Mo-0.03C-0.23Nb, weight percent, %) is designed using a cluster formula approach. Alloy ingots are prepared by vacuum induction melting under an argon atmosphere, followed by hot rolling at 950 ℃ and multiple passes of cold rolling. Finally, the alloy is aged at 500 ℃ for 288 h. Microstructural characterizations of the alloy in different aging states are performed using electron backscatter diffraction (EBSD) and transmission electron microscope (TEM). As a result, the martensitic structure of the alloy is fragmented and elongated, with high-density dislocations (~1.8×10^–3 nm^–2) and a large number of coherent B2-NiAl nanoparticles (<5 nm) observed in the BCC martensitic matrix after cold rolling and aging. In terms of mechanical properties, the alloy exhibits significant age-hardening, with a peak-aged hardness of 651 HV after ageing treatment. It also demonstrates an extraordinarily high yield strength (σ_YS = 2.3 GPa) and a decent elongation (El = 3.6%), indicating a well-balanced strength-ductility property. Finally, the origins of the ultra-high strength in the novel alloy are discussed in depth, showing that the ultra-high strength of this stainless steel comes from the strengthening effect of different microstructures. This study provides valuable guidance for designing high-performance ultra-high strength maraging stainless steels.

Keywords:

Authors and contacts

1.
Engineering Research Center of High Entropy Alloy Materials (Lianoning Province), School of Materials Science and Engineering, Dalian University of Technology, Dalian 116024, China
2.
Foshan Shunde Midea Electrical Heating Appliances Manufacturing Co., Ltd., Foshan 528300, China
3.
School of Materials Science and Engineering, South China University of Technology, Guangzhou 510641, China

Corresponding author: WANG Zhenhua, ahua@mail.dlut.edu.cn ; WAN Peng, pengwan@midea.com ;

Funds: Project supported by the National Natural Science Foundation of China (Grant No. 52171152).

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References

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Cited By

图 1 由Pandat软件计算得到的Fe-7.95Cr-13.47Ni-3.10Al-1.83Mo-0.23Nb-0.03C合金的平衡相图

Figure 1. Equilibrium phase diagram of the designed Fe-7.95Cr-13.47Ni-3.10Al-1.83Mo-0.23Nb-0.03C alloy calculated by Pandat software.

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图 2 合金冷轧态(CR)的EBSD反极图(IPF)和相分布图(a), (b); 冷轧态合金TEM明场像及其对应的SAED花样(c); HRTEM图像及其对应的FTT图像(d)

Figure 2. EBSD IPF image and phase image of the designed alloy after cold-rolling (CR) treatment (a), (b); TEM bright-field (BF) image and corresponding SAED patterns (c) and High-resolution TEM image and its FTT pattern (d) of CR.

DownLoad: Full-Size Img PowerPoint

图 3 12 h时效后CRA合金的微观结构　合金冷轧+时效态(CRA)的EBSD反极图(IPF)和相分布图(a), (b); CRA合金TEM明场、暗场像及其对应的SAED花样(c), (d); CRA合金HRTEM图像及其对应的FTT图像(e), (e1), (e2), 以及衍射环图像(f)

Figure 3. Microstructures of 12 h-aged CRA alloys: EBSD IPF image and phase image of the CRA alloy (a), (b); TEM bright-field (BF) image and corresponding SAED patterns (c), TEM DF image (d); HRTEM image and its FTT patterns (e), (e1), (e2), and diffraction ring (f) of the CRA alloy.

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图 4 冷轧态合金在时效48 h后的TEM明场(a)、暗场像(b)

Figure 4. TEM bright-field image (a), the corresponding dark-field image (b) of 48 h-aged CRA alloy.

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图 5 合金经热轧(HR)处理(a)和热轧+500 ℃/12 h时效(HRA)处理(c)后的EBSD反极图(IPF), HR(b)和HRA(d)处理后的EBSD相图

Figure 5. EBSD inverse pole figures (IPFs) of the designed alloy after hot-rolling (HR) treatment (a) and hot-rolling + aging at 500 ℃/12 h (HRA) treatment (c), EBSD phase images of HR (b) and HRA (d).

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图 6 12 h时效HRA合金(a)和12 h时效冷轧+时效态(CRA)合金(c)的晶界分布图, HRA(b)和CRA(d)的核平均取向差(KAM)　　　

Figure 6. Grain boundary distribution maps of 12 h-aged HRA alloys (a) and 12 h-aged CRA alloys (c), kernel average misorientation (KAM) of HRA (b) and CRA (d).

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图 7 CRA合金在500 ℃时效时显微硬度随时效时间的变化(a), 不同热处理状态下合金在室温拉伸下的工程应力-应变曲线(b)和室温三点弯曲下的载荷-位移曲线(c)

Figure 7. Variation tendency of microhardness of the CRA alloy with aging time at 500℃ (a), room-temperature engineering stress-strain tensile curves of the current alloy at different heat-treated (b), and 3-points bending test of the current alloy at different heat-treated (c).

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图 8 根据不同强化机制计算得到的CR合金以及时效12 h CRA合金的屈服强度, 黑色星型符号表示通过实验测得的屈服强度

Figure 8. Calculated strength increments from different strengthening mechanisms in CR and 12 h-aged CRA alloys, in which the measured yield strength values are also presented with black star symbols for comparison.

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表 1 不同热处理状态下设计合金以及18 Ni(300)^[45]的H, σ_YS, σ_UTS, El, 极限弯曲载荷(F_B), 及极限弯曲角度(θ_B)

Table 1. Mechanical properties of the current stainless steel at different heat-treated states and the 18 Ni(300) steel^[45], including microhardness (H), yield strength (σ_YS), ultimate tensile strength (σ_UTS), elongation to fracture (El), ultimate bending force (F_B), and ultimate bending angle (θ_B).

States	H/HV	σ_YS/MPa	σ_UTS/MPa	El/%	F_B/kN	θ_B/(°)
HR	326±10	787	1100	9.3	8.5	35.5
CR	404±5	1408	1432	4.4	9.7	14.9
HRA: 5 h-aged	573±6	1704	1940	3.9	10.1	9.7
CRA: 5 h-aged	645±6	2326	2344	3.6	22.2	15.4
CRA: 12 h-aged	641±8	2254	2324	3.0	18.2	17.9
18 Ni(300)	—	2000	2050	7.0	—	—

DownLoad: CSV

[1]	杨柯, 牛梦超, 田家龙, 王威 2018 金属学报 54 1567 Google Scholar Yang K, Niu M C, Tian J L, Wang W 2018 Acta. Metall. Sin. 54 1567 Google Scholar
[2]	罗海文, 沈国慧 2020 金属学报 56 494 Google Scholar Luo H W, Shen G H 2020 Acta. Metall. Sin. 56 494 Google Scholar
[3]	Sun W W, Marceau R K W, Styles M J, Barbier D, Hutchinson C R 2017 Acta Mater. 130 28 Google Scholar
[4]	Morris Jr J W 2017 Nat. Mater. 16 787 Google Scholar
[5]	Yang J R, Yu T H, Wang C H 2006 Mater. Sci. Eng. A 438 276
[6]	Shi X H, Zeng W D, Zhao Q Y, Peng W W, Kang C 2016 J. Alloys. Compd. 679 184 Google Scholar
[7]	Wert D E, DiSabella R P 2006 Adv. Mater. Process. 164 34
[8]	Ifergane S, Pinkas M, Barkayc Z, Brosh E, Ezersky V, Beeri O, Eliaz N 2017 Mater. Charact. 127 129 Google Scholar
[9]	Floreen S 1968 Metall. Rev. 13 115 Google Scholar
[10]	Tewari R, Mazumder S, Batra I S, Dey G K, Banerjee S 2000 Acta Mater. 48 1187 Google Scholar
[11]	Xu W, Rivera-Díaz-del-Castillo P E J, Yan W, Yang K, San Martín D, Kestens L A I, van der Zwaag S 2010 Acta Mater. 58 4067 Google Scholar
[12]	Qi L, Jin Y C, Zhao Y H, Yang X M, Zhao H, Han P D 2015 J. Alloys. Compd. 621 383 Google Scholar
[13]	Moshka O, Pinkas M., Brosh E, Ezersky V, Meshi L 2015 Mater. Sci. Eng. A 638 232 Google Scholar
[14]	周倩青, 翟玉春 2009 金属学报 45 1249 Google Scholar Zhou Q Q, Zhai Y C 2009 Acta Metall. Sin. 45 1249 Google Scholar
[15]	Hättestrand M, Nilsson J O, Stiller K, Liu P, Andersson M 2004 Acta Mater. 52 1023 Google Scholar
[16]	Ghosh A, Das S, Chatterjee S 2008 Mater. Sci. Eng. A 486 152 Google Scholar
[17]	Mahmoudi A, Zamanzad Ghavidel M R, Hossein Nedjad S, Heidarzadeh A, Nili Ahmadabadi M 2011 Mater. Charact. 62 976 Google Scholar
[18]	Leitner H, Schnitzer R, Schober M, Zinner S 2011 Acta Mater. 59 5012 Google Scholar
[19]	Vaithyanathan V, Chen L Q 2002 Acta Mater. 50 4061 Google Scholar
[20]	Li H, Liu Y, Liu B 2022 Mater. Sci. Eng. A 842 143099 Google Scholar
[21]	Niu M C, Zhou G, Wang W, Shahzad M B, Shan Y Y, Yang K 2019 Acta Mater. 179 296 Google Scholar
[22]	Wan J Q, Ruan H H, Ding Z Y, Kong L B 2023 Scr. Mater. 226 115224 Google Scholar
[23]	Li K, Yu B, Misra R D K, Han G, Liu S, Shang C J 2018 Mater. Sci. Eng. A 715 485
[24]	Ooi S W, Hill P, Rawson M, Bhadeshia H K D H 2013 Mater. Sci. Eng. A 564 485 Google Scholar
[25]	Liu T Q, Cao Z X, Wang H, Wu G L, Jin J J, Cao W Q 2020 Scr. Mater. 178 285 Google Scholar
[26]	Li Y C, Yan W, J. D. Cotton, G. J. Ryan, Shen Y F, Wang W, Shan Y Y, Yang K 2015 Mater. Des. 82 56 Google Scholar
[27]	Hedströma P, Baghsheikhi S, Liu P, Odqvist J 2012 Mater. Sci. Eng. A 534 552 Google Scholar
[28]	Li J L, Zhang J Q, Li Z, Wang Q, Dong C, Xu F, Sun L X, Liaw P K 2024 J. Mater. Sci. Technol. 186 174 Google Scholar
[29]	Zhang J X, Wang J C, Harada H, Koizumi Y 2005 Acta Mater. 53 4623 Google Scholar
[30]	Wang Z H, Wang Q, Niu B, Dong C, Zhang H W, Zhang H F, Liaw P K 2021 Mater. Res. Lett. 9 458 Google Scholar
[31]	Jiang S H, Wang H, Wu Y, Liu X J, Chen H H, Yao M J, Gault B, Ponge D, Raabe D, Hirata A, Chen M W, Wang Y D, Lu Z P 2017 Nature 544 460 Google Scholar
[32]	Zhou B C, Liu S F, Wu H H, Luan J H, Guo J M, Yang T, Jiao Z B 2023 Mater. Des. 234 112341 Google Scholar
[33]	Liang Y J, Wang L J, Wen Y R, Cheng B Y, Wu Q L, Cao T Q, Xiao Q, Xue Y F, Sha G, Wang Y D, Ren Y, Li X Y, Wang L, Wang F C, Cai H N 2018 Nat. Commun. 9 4063 Google Scholar
[34]	Hong H L, Wang Q, Dong C, Liaw P K 2014 Sci. Rep. 4 7065 Google Scholar
[35]	Pang C, Jiang B B, Shi Y, Wang Q, Dong C 2015 J. Alloys. Compd. 652 63 Google Scholar
[36]	Wang Z H, Niu B, Wang Q, Dong C, Jie J C, Wang T M, Nieh T G 2021 J. Mater. Sci. Technol. 93 60 Google Scholar
[37]	Calderon H A, Fine M E, Weertman J R 1987 Metall. Trans. A 19 1135
[38]	Vo N Q, Liebscher C H, Rawlings M J S, Asta M, Dunand D C 2014 Acta Mater. 71 89 Google Scholar
[39]	Czyryca E J 1993 Key Eng. Mater. 84 491
[40]	Wen D H, Wang Q, Jiang B B, Zhang C, Li X N, Chen G Q, Tang R, Zhang R Q, Dong C, P. K. Liaw 2018 Mater. Sci. Eng. A 719 27 Google Scholar
[41]	Bailey N 1993 Welding Steels without Hydrogen Cracking (Cambridge: Woodhead Publishing) p69
[42]	Briant C L, Banerji S K 1978 Int. Metal. Rev. 23 164
[43]	Hosford W F 2005 Mechanical Behavior of Materials (New York: Cambridge University Press) p16
[44]	Leitner H, Schober M, Schnitzer R 2010 Acta Mater. 58 1261 Google Scholar
[45]	毕正绪 2014 特钢技术 20 11 Google Scholar Bi Z X 2014 Special Steel Technol. 20 11 Google Scholar
[46]	Galindo-Nava E I, Rivera-Díaz-del-Castillo P E J 2015 Acta Mater. 98 81 Google Scholar
[47]	Galindo-Nava E I, Rainforth W M, Rivera-Díaz-del-Castillo P E J 2016 Acta Mater. 117 270 Google Scholar
[48]	Rivera-Díaz-del-Castillo P E J, Hayashi K, Galindo-Nava E I 2013 Mater. Sci. Technol. 29 1206 Google Scholar
[49]	Fleischer R L 1961 Acta Matall. 9 966 Google Scholar
[50]	Lide D R 2008 CRC Handbook of Chemistry and Physics (Boca Raton: CRC Press) pp12–10
[51]	Morito S, Yoshida H, Maki T, Huang X 2006 Mater. Sci. Eng. A 438 237
[52]	Su J, Raabe D, Li Z M 2019 Acta Mater. 163 40 Google Scholar
[53]	Kocks U F, Mecking H 2003 Prog. Mater Sci. 48 171 Google Scholar
[54]	Nembach E 1997 Mater. Sci. Technol. 3 329
[55]	Gladman T 1999 Mater. Sci. J. 15 30
[56]	Argon A 2007 Strengthening Mechanisms in Crystal Plasticity (Oxford: Oxford University Press) p74
[57]	P. M. Kelley 1973 Int. Metall. Rev. 18 31 Google Scholar
[58]	A. Kelly, R. B. Nicholson 1971 Strengthening Methods in Crystals (London: Elsevier) p37
[59]	T. Hong, A. J. Freeman 1991 Phys. Rev. B Condens. Matter. 43 6446 Google Scholar

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Vol. 74, Issue 5 - 2025-03-05

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