Microstructure and Mechanical Properties of an Austenite/Ferrite Laminate Structured High-Manganese Steel

doi:10.11900/0412.1961.2018.00100

Acta Metall Sin

2018, Vol. 54

Issue (10): 1387-1398 DOI: 10.11900/0412.1961.2018.00100

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Microstructure and Mechanical Properties of an Austenite/Ferrite Laminate Structured High-Manganese Steel

Kai ZHU, Cuilan WU(

), Pan XIE, Mei HAN, Yuanrui LIU, Xiangge ZHANG, Jianghua CHEN

College of Materials Science and Engineering, Hunan University, Changsha 410082, China

Cite this article:

Kai ZHU, Cuilan WU, Pan XIE, Mei HAN, Yuanrui LIU, Xiangge ZHANG, Jianghua CHEN. Microstructure and Mechanical Properties of an Austenite/Ferrite Laminate Structured High-Manganese Steel. Acta Metall Sin, 2018, 54(10): 1387-1398.

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Abstract

Lamianate structured metals have recently attracted extensive interests for their outstanding mechanical properties which are produced by synergetic strengthening of different heterogeneous layers. For Mn-rich maraging steels, austenite can precipitate in the martensite matrix due to Mn segregation during heat treatment, and then the austenite and martensite/ferrite duplex steel is produced. Besides, high Mn TRIP steel is regarded as a promising material for next generation automobile steel because of its high strength and good ductility. In this work, the microstructures and properties of Mn12Ni2MoTi(Al) steels produced by thermo-mechanical process were investigated using XRD, SEM, TEM, EBSD, EPMA, hardness tests and tensile tests. The results showed that laminate structures with austenite/ferrite band alternate arranging along the normal direction were formed in Mn12Ni2MoTi(Al) steels, which were processed by 65% cold-rolling and subsequent annealing at 745 ℃. Both of austenite bands and ferrite bands consist of ultrafine equiaxed grains. Moreover, a small amount of ferrite grains and austenite grains were found inside the austenite bands and ferrite bands, respectively. In the austenite/ferrite laminate structures, the austenite bands show the Brass texture of {110}<112> and Goss- type texture of {110}<001>. The ferrite bands show the rotate Cube texture of {001} <110> and Cube texture of {001}<100>. With the increase of annealing time, the laminate structures first become dominant and then disappear gradually, accompanying with the orientation transition of austenite from the Brass texture into the Goss one. The samples with laminate structures have high yield strength and good ductility. Otherwise, when the laminate structures disappear, the yield strength and ductility of the samples will decrease, and the yield strength deceases more.

Key words: laminate structure high manganese steel thermomechanical process TRIP effect

Received: 19 March 2018

ZTFLH:

TG166.7

Fund: Supported by National Natural Science Foundation of China (Nos.11427806 and 51371081)

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	Articles by authors
	Kai ZHU
	Cuilan WU
	Pan XIE
	Mei HAN
	Yuanrui LIU
	Xiangge ZHANG
	Jianghua CHEN

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https://www.ams.org.cn/EN/10.11900/0412.1961.2018.00100 OR https://www.ams.org.cn/EN/Y2018/V54/I10/1387

Fig.1 Schematic of a sample (ND-section, TD-section and RD-section are perpendicular to the normal direction, the transverse direction and the rolling direction, respectively)

Table 1 The Miller indices and texture components of symbols given in Fig.2

Fig.2 Locations of common textures components of metals in the ψ₂=0° and ψ₂=45° sections (The Miller indices and texture components of symbols are given in Table 1)^[29]

Fig.3 TEM image (a), ND-sectional XRD spectrum (b) and ODFs of texture at ψ₂=0° (c) and ψ₂=45° (d) of 65%CR sample

Fig.4 SEM images of 745 ℃-1 h sample in different sections
(a) ND-section (b) TD-section (c) RD-section (d) low magnified image of the TD-section

Fig.5 The average thickness curves (a) and Vickers hardness curves (b) of bright bands and dark bands in the same samples annealed for different time at 745 ℃ (Inset shows the indentations of different bands)

Fig.6 SEM image (a) and EBSD phase-map (b) of the 745 ℃-1 h sample

Fig.7 XRD spectra of 745 ℃-1 h annealed samples in different sections

Fig.8 The relative volume fraction of γ in the samples annealed at 745 ℃ for different time

Fig.9 EBSD phase-maps (a~f) and IPF-maps (a1~f1) of the samples annealed at 745 ℃ for different time (In the EBSD phase-maps, the red represents the austenite while the green represents the ferrite. In the IPF-maps, different colours represent different directions of grains)
(a, a1) 745 ℃-5 min (b, b1) 745 ℃-30 min (c, c1, e, e1, f, f1) 745 ℃-1 h (d, d1) 745 ℃-24 h

Fig.10 Textures of austenite in the different samples annealed for different time at 745 ℃
(a, a1) 745 ℃-5 min (b, b1) 745 ℃-30 min (c, c1) 745 ℃-1 h (d, d1) 745 ℃-24 h

Fig.11 Textures of ferrite in the different samples annealed for different time at 745 ℃
(a, a1) 745 ℃-5 min (b, b1) 745 ℃-30 min (c, c1) 745 ℃-1 h (d, d1) 745 ℃-24 h

Fig.12 EPMA maps of Mn distribution for different samples
(a) 65%CR (b) 745 ℃-30 min (c) 745 ℃-24 h

Fig.13 TEM images of 745 ℃-1 h (a, c) and 745 ℃-24 h (b, d) samples (a, b) recrystallized grains (c, d) martensite

Fig.14 Tensile stress-strain curves of different samples

Fig.15 EBSD phase-maps (a~d) and IPF-maps (a1~d1) of the 745 ℃-1 h sample with different tensile deformations (In the EBSD phase-maps, the red represents the austenite while the green represents the ferrite. In the IPF-maps, different colours represent different directions of grains)
(a, a1) 0.5% strain (b, b1) 5% strain (c, c1) 10% strain (d, d1) tensile fracture

Fig.16 EBSD phase-map (a) and IPF-map (a1) of the 745 ℃-24 h sample after tensile fracture (In the EBSD phase-maps, the red represents the austenite while the green represents the ferrite. In the IPF-maps, different colours represent different directions of grains)

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