Effect of Strain Rate on the Strain Partitioning Behavior of Ferrite/Bainite in X80 Pipeline Steel

doi:10.11900/0412.1961.2021.00412

Acta Metall Sin

2023, Vol. 59

Issue (10): 1299-1310 DOI: 10.11900/0412.1961.2021.00412

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Effect of Strain Rate on the Strain Partitioning Behavior of Ferrite/Bainite in X80 Pipeline Steel

WANG Nan¹, CHEN Yongnan¹(

), ZHAO Qinyang¹, WU Gang², ZHANG Zhen¹, LUO Jinheng²

^1.School of Materials Science and Engineering, Chang'an University, Xi'an 710064, China
^2.CNPC Tubular Goods Research Institute, Xi'an 710077, China

Cite this article:

WANG Nan, CHEN Yongnan, ZHAO Qinyang, WU Gang, ZHANG Zhen, LUO Jinheng. Effect of Strain Rate on the Strain Partitioning Behavior of Ferrite/Bainite in X80 Pipeline Steel. Acta Metall Sin, 2023, 59(10): 1299-1310.

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Abstract

X80 pipeline steel, which is mainly composed of ferrite/bainite, is an important structural steel for pipeline transportation. The plastic deformation of X80 pipeline steel at different strain rates caused by geological and human factors deteriorates its strength. Microstructural transformation and strain localization during deformation are the fundamental factors that deteriorate the mechanical properties of steel. Therefore, in this study, the strain partitioning behavior and microstructure evolution mechanism of ferrite and bainite in X80 pipeline steel at different strain rates (10^-4 s^-1 to 10^-1 s^-1) under 5% deformation were revealed using representative volume element models and electron backscatter diffraction technology. The results show that when the strain rate is low (10^-4 s^-1 to 10^-3 s^-1), ferrite has sufficient time to complete the evolution of geometrically necessary dislocations (GNDs) to low-angle grain boundaries (LAGBs) and the transformation of LAGBs to high-angle grain boundaries (HAGBs). Ferrite can release strain distortion energy, which can weaken the strain localization behavior of X80 steel. As the strain rate increases, the strain response time decreases, hindering the transition from LAGBs to HAGBs. This results in the accumulation of high-density GNDs and LAGBs in ferrite, thereby intensifying strain localization. Additionally, when the strain rate is high (10^-2 s^-1 to 10^-1 s^-1), the strain partitioning coefficient between ferrite and bainite could be reduced, thereby producing the strain gradient in the vicinity of the interface and resulting in GNDs accumulation and back stress formation. Furthermore, ferrite and bainite could show compressive and tensile stresses, respectively, thus limiting the strain coordination between the two phases significantly, increasing the stress concentration near the interface, and reducing the strain hardening ability. The strain partitioning behavior between ferrite and bainite was further revealed to better understand the plastic deformation of X80 pipeline steel.

Key words: X80 steel strain rate RVE model strain localization strain hardening

Received: 27 September 2021

ZTFLH:

TG142.1

Fund: Natural Science Foundation of Shaanxi Province(2019JZ-27)

Corresponding Authors: CHEN Yongnan, professor, Tel: 13384948620, E-mail: frank_cyn@163.com

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	WANG Nan
	CHEN Yongnan
	ZHAO Qinyang
	WU Gang
	ZHANG Zhen
	LUO Jinheng

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https://www.ams.org.cn/EN/10.11900/0412.1961.2021.00412 OR https://www.ams.org.cn/EN/Y2023/V59/I10/1299

Fig.1 Schematics of making representative volume element (RVE) model (a-e) and true stress-strain curves of ferrite and bainite (f)
(a) OM image (b) locally magnified OM image (c) binarization model
(d) boundary line model (e) boundary condition of displacement (U_x and U represent the displacement of x-axis and boundary displacement direction, respectively)

Table 1 Mechanical property parameters of ferrite and bainite^[21]

Fig.2 Equivalent plastic strain (PEEQ) distributions under deformation of 5% at strain rates of 10^-4 s^-1 (a1-a3), 10^-3 s^-1 (b1-b3), 10^-2 s^-1 (c1-c3), and 10^-1 s^-1 (d1-d3) for ferrite (a1-d1), bainite (a2-d2), and X80 steel (a3-d3)

Fig.3 Probability density functions at strain rates of 10^-4 s^-1 (a) and 10^-1 s^-1 (b), strain localization factor (c), cumulative density functions (CDF) at strain rates of 10^-4 s^-1 (d) and 10^-1 s^-1 (e), and plastic deformation difference between two phases (f) of ferrite and bainite under deformation of 5%

Fig.4 Strain partitioning behaviors between ferrite and bainite
(a) true stress-strain curve at strain rate of 10^-4 s^-1 (b) strain partitioning coefficient

Fig.5 Engineering stress-strain curves (a) and strain rate sensitivity indexes (m) (b) under different strain rates

Table 2 Mechanical properties of X80 steel under different strain rates

Fig.6 Kernel average misorientation (KAM) maps of X80 steel after deformation of 5% at strain rates of 10^-4 s^-1 (a), 10^-3 s^-1 (b), 10^-2 s^-1 (c), and 10^-1 s^-1 (d) (Inset shows the strain gradient between ferrite and bainite)

Fig.7 Schematic of back stress caused by geometrically necessary dislocations (GNDs) accumulation (a) and GND densities after different strain rates (b)

Fig.8 Grain boundary distribution maps at strains rates of 10^-4 s^-1 (a) and 10^-1 s^-1 (b) (Black lines represent high-angle grain boundaries (HAGBs) and red lines represent low-angle grain boundaries (LAGBs)), and misorientation statistical diagrams at strain rates of 10^-4 s^-1 (c), 10^-3 s^-1 (d), 10^-2 s^-1 (e), and 10^-1 s^-1 (f) in X80 steel

Fig.9 Relative volume fractions of LAGBs and HAGBs under different strain rates

Fig.10 Schematic of the microstructure evolution for ferrite under low strain rate and high strain rate from yield to 5% deformation in X80 steel

Fig.11 Strain hardening behaviors of X80 steel under different strain rates
(a) true stress-strain curves
(b) modified C-J model (ε_I-II is the strain at the transition point from stage I to stage II, and ε_II-III is the strain at the transition point from stage II to stage III)

Table 3 Strain hardening capacities and transition point strains in each stage for the modified C-J model

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