Effect of Mn / N Ratio on the Microstructure and Mechanical Properties of Multi-Pass Welding HAZ of 22%Cr Low Nickel Type Duplex Stainless Steel

doi:10.11900/0412.1961.2024.00225

Acta Metall Sin

2026, Vol. 62

Issue (7): 1257-1272 DOI: 10.11900/0412.1961.2024.00225

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Effect of Mn / N Ratio on the Microstructure and Mechanical Properties of Multi-Pass Welding HAZ of 22%Cr Low Nickel Type Duplex Stainless Steel

GUO Mengyu, YANG Yinhui(

), GAO Zihao, CAO Jianchun, WU Shiyu, CHEN Xiaoyu

School of Materials Science and Engineering, Kunming University of Science and Technology, Kunming 650093, China

Cite this article:

GUO Mengyu, YANG Yinhui, GAO Zihao, CAO Jianchun, WU Shiyu, CHEN Xiaoyu. Effect of Mn / N Ratio on the Microstructure and Mechanical Properties of Multi-Pass Welding HAZ of 22%Cr Low Nickel Type Duplex Stainless Steel. Acta Metall Sin, 2026, 62(7): 1257-1272.

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Abstract

Variations in the Mn / N ratio greatly affect the formation of reformed austenite and precipitation and two-phase ratio in duplex stainless steel (DSS) during the welding thermal cycle. Therefore, investigating the influence of the Mn / N ratio on the multipass welding heat-affected zone (HAZ) microstructure is beneficial for enhancing the comprehensive mechanical properties of the HAZ of low-nickel-type DSS thick plates. This study comparatively investigated the effect of Mn / N ratio on the microstructure evolution and mechanical properties of DSS in the solution-treated and multi-pass welded HAZ, with 2205 DSS as a reference. The higher nitrogen content (Mn / N ratio = 3.77) resulted in substantial partial transformed austenite formation with a high volume fraction of 58.7%, yielding a tensile strength of 836 MPa and an elongation of 39.5%, indicating its high strength and plasticity. As the Mn / N ratio increases to 17.80, an increase in the Widmanstätten austenite (WA) amount caused cellular Cr₂N formation at the δ/γ phase interfaces and dislocation walls in ferrite for HAZ, considerably decreasing elongation compared to the solid solution state. For DSS with a high Mn / N ratio of 65.91, the grain boundary austenite (GBA) amount initially increased and then decreased, while the intragranular austenite (IGA) and WA amounts increased in HAZ, inhibiting Cr₂N precipitation and reducing ductility and strength. Compared with the 2205 DSS (Mn / N ratio = 3.06), the fracture surfaces of DSS with lower Mn / N ratios exhibited brittle fracture. The combined strengthening effect of the high-nitrogen solid solution and Cr₂N precipitation on the austenite phase increased the hardness difference between the two phases in the HAZ of the DSS with Mn / N ratio of 3.77. In addition, the formation of some large (Cr, Mn)O inclusions promoted crack initiation to some extent, lowering the impact energy to 24.2 J. High Mn / N ratio led to more GBA and WA segmented ferrite refinement, as well as the formation of small amounts of IGA, which hindered crack propagation. Moreover, the precipitation of a small amount of the σ phase increased the hardness of ferrite, reduced the hardness difference between the two phases, and increased the impact energy to 134.8 J.

Key words: multi-pass welding welding HAZ Mn / N ratio impact toughness tensile strength

Received: 04 July 2024

ZTFLH:

TG142

Fund: National Natural Science Foundation of China(51861019)

Corresponding Authors: YANG Yinhui, professor, Tel: 13518726308, E-mail: yyhyanr@sina.com

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	GUO Mengyu
	YANG Yinhui
	GAO Zihao
	CAO Jianchun
	WU Shiyu
	CHEN Xiaoyu

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https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00225 OR https://www.ams.org.cn/EN/Y2026/V62/I7/1257

Table 1 Chemical compositions and Mn / N ratios of duplex stainless steel (DSS) samples

Fig.1 Multi-pass welding thermal cycle curve of DSS1-DSS4 samples

Fig.2 Dimension of tensile samples (unit: mm)

Fig.3 OM images of solid solution treated samples (a, c, e, g) and multi-pass welding HAZ samples (b, d, f, h) (GBA—grain boundary austenite, WA—Widmanstätten austenite, PTA—partial transformed austenite, IGA—intragranular austenite, HAZ—heat affected zone)
(a, b) DSS1 (c, d) DSS2 (e, f) DSS3 (g, h) DSS4

Fig.4 Variations of austenite volume fraction of solid solution treated samples and multi-pass welding HAZ samples (a) and proportions of GBA, WA, IGA, and PTA in HAZ (b)

Fig.5 STEM image and SAED patterns of HAZ for DSS1 and DSS2 samples after multi-pass welding
(a-c) morphology (a), SAED pattern of γ (b), and dislocation distribution (c) of DSS1 sample
(d-i) morphology (d) and corresponding SAED patterns of γ and δ phases (e, f), dislocation distribution near γ/δ interface (g), and distribution of Cr₂N precipitates (h) and corresponding SAED pattern (i) of DSS2 sample (Inset in Fig.5h is locally enlarged view)

Fig.6 STEM images and SAED patterns of HAZ for DSS3 sample after multi-pass welding
(a) distribution of GBA, IGA, and δ
(b) dislocation distribution at γ/δ interface
(c) enlarged morphology of Cr₂N precipitates
(d, f) SAED patterns of ferrite (d) and austenite and Cr₂N precipitates (f) in Fig.6e
(e) morphology of Cr₂N precipitate at γ/δ interfaces

Fig.7 STEM images, SAED patterns, and EDS result of HAZ for DSS4 sample after multi-pass welding
(a-c) two-phase morphology distributions (a) and SAED patterns of austenite (b) and ferrite (c)
(d) dislocation tangles near γ/δ interfaces
(e) reformed austenite morphology in two phases
(f-h) distribution of σ-phase precipitates and the amplified morphology (inset) (f), SAED pattern (g), and corresponding compositions (h)

Fig.8 Engineering stress-strain curves of DSS1-DSS4 samples for solid solution treated samples (a) and multi-pass welding HAZ samples (b)

Fig.9 Tensile mechanical properties of solid solution treated samples (a) and multi-pass welding HAZ samples (b)

Fig.10 SEM images of tensile fractures of multi-pass welding HAZ for DSS1 (a-c), DSS2 (d-f), DSS3 (g-i), and DSS4 (j-l) samples
(a, d, g, j) marcrophologies (b, e, h, k) radial regions (c, f, i, l) shear lips

Fig.11 Impact energies of solid solution treated samples and multi-pass welding HAZ samples (a), and hardness distributions of the multi-pass welding HAZ samples (b)

Fig.12 SEM images of impact fractures of multi-pass welding HAZ for DSS1 (a-c), DSS2 (d-f), DSS3 (g-i), and DSS4 (j-l) samples
(a, d, g, j) marcrophologies (b, e, h, k) radial regions (c, f, i, l) shear lips

Fig.13 Morphologies (a, d, g, j), particle size distributions (b, e, h, k), and EDS results (c, f, i, l) of inclusions in multi-pass welding HAZ impact fractures of DSS1 (a-c), DSS2 (d-f), DSS3 (g-i), and DSS4 (j-l) samples (σ—standard deviation)

Fig.14 Schematic of reformed austenite evolution in HAZ of DSS1-DSS4 samples after multi-pass welding

Fig.15 Schematics of impact fracture evolution of multi-pass welded HAZ of DSS1 (a-c), DSS2 (d-f), DSS3 (g-i), and DSS4 (j-l) samples

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