J. Mater. Sci. Technol. ›› 2021, Vol. 75: 139-153.DOI: 10.1016/j.jmst.2020.10.022
• Research Article • Previous Articles Next Articles
Jingbin Zhanga, Yinrui Suna, Zhijie Jia, Haiwen Luoc,*(), Feng Liua,b,*()
Received:
2020-05-11
Revised:
2020-07-28
Accepted:
2020-08-02
Published:
2020-10-23
Online:
2020-10-23
Contact:
Haiwen Luo,Feng Liu
About author:
liufeng@nwpu.edu.cn (F. Liu).Jingbin Zhang, Yinrui Sun, Zhijie Ji, Haiwen Luo, Feng Liu. Improved mechanical properties of V-microalloyed dual phase steel by enhancing martensite deformability[J]. J. Mater. Sci. Technol., 2021, 75: 139-153.
Fig. 1. Tensile properties corresponding to different processing routes, where, three temperatures for the inter-critical annealing are applied in PR2 to show the strength-ductility trade-off.
UTS(Ultimate tensile strength), MPa | TE(Total elongation), % | |
---|---|---|
PR1 | 1367 ± 15 | 15.3 ± 0.2 |
PR2-760 °C | 1145 ± 18 | 5.5 ± 0.29 |
PR2-740 °C | 1072 ± 22 | 11.0 ± 0.25 |
PR2-720 °C | 939 ± 14 | 12.6 ± 0.25 |
PR3 | 1448 ± 14 | 4.4 ± 0.37 |
Table 1 Average tensile tests results for each annealing cycle.
UTS(Ultimate tensile strength), MPa | TE(Total elongation), % | |
---|---|---|
PR1 | 1367 ± 15 | 15.3 ± 0.2 |
PR2-760 °C | 1145 ± 18 | 5.5 ± 0.29 |
PR2-740 °C | 1072 ± 22 | 11.0 ± 0.25 |
PR2-720 °C | 939 ± 14 | 12.6 ± 0.25 |
PR3 | 1448 ± 14 | 4.4 ± 0.37 |
Ferrite | Martensite | Retained austenite | V(C,N) | ||||||
---|---|---|---|---|---|---|---|---|---|
Volume fraction (%) | Mean size (μm) | Volume fraction (%) | Mean size (μm) | Volume fraction (%) | Mean size (μm) | Volume fraction (%) | Mean size (μm) | ||
ferrite | martensite | ||||||||
PR1-760 °C | 19.3 | 0.90 | 80.7 | 0.46 | ≈0(<0.2) | --- | 2.0 | 1.2 | 11.7 |
PR2-760 °C | 26.4 | 1.80 | 73.6 | 0.95 | ≈0(<0.2) | --- | 2.1 | 1.7 | 25.9 |
PR2-740 °C | 47.3 | 2.0 | 52.7 | 0.87 | ≈0(<0.2) | --- | 2.0 | 1.7 | 25.0 |
PR2-720 °C | 63.7 | 2.4 | 36.3 | 0.71 | ≈0(<0.2) | --- | 2.0 | 1.8 | 24.3 |
PR3-880 °C | 0 | --- | 100 | 0.21: | ≈0(<0.2) | --- | 0 (solid-solution) | --- |
Table 2 Phase fractions (ferrite, martensite, retained austenite, V(C,N)) along with mean size data for each phase in each annealing cycle.
Ferrite | Martensite | Retained austenite | V(C,N) | ||||||
---|---|---|---|---|---|---|---|---|---|
Volume fraction (%) | Mean size (μm) | Volume fraction (%) | Mean size (μm) | Volume fraction (%) | Mean size (μm) | Volume fraction (%) | Mean size (μm) | ||
ferrite | martensite | ||||||||
PR1-760 °C | 19.3 | 0.90 | 80.7 | 0.46 | ≈0(<0.2) | --- | 2.0 | 1.2 | 11.7 |
PR2-760 °C | 26.4 | 1.80 | 73.6 | 0.95 | ≈0(<0.2) | --- | 2.1 | 1.7 | 25.9 |
PR2-740 °C | 47.3 | 2.0 | 52.7 | 0.87 | ≈0(<0.2) | --- | 2.0 | 1.7 | 25.0 |
PR2-720 °C | 63.7 | 2.4 | 36.3 | 0.71 | ≈0(<0.2) | --- | 2.0 | 1.8 | 24.3 |
PR3-880 °C | 0 | --- | 100 | 0.21: | ≈0(<0.2) | --- | 0 (solid-solution) | --- |
Fig. 2. Characterization for hot-rolled (a, b, c, d) and cold rolled (e, f, g, h) bainite microstructure. (a): Secondary-electron images of hot-rolled bainite showed the morphology of bainite lathes; (b): distribution of GBs of high-angle and low-angle types separated by the critical orientational difference as 15 degree in hot-rolled bainite showed two kinds of morphology i.e. massive and acicular existing in the hot-rolled microstructure; (c): TEM characterization of massive BCC phase; (d): TEM characterization of acicular BCC phase. (e): Secondary-electron images of the cold-rolled bainite showed the morphology of distorted bainite lathes. (f): distribution of GBs of high-angle and low-angle types separated by the critical orientational difference as 15 degree in the cold-rolled bainite; (g): low magnified TEM characterization of deformed bainite lathes and dislocation entanglement; (h) high magnified TEM characterization of deformed bainite lathes. Inserts in (c), (d) are diffraction patterns.
Group | Saturation magnetization (emu/g) |
---|---|
Hot-rolled bainite | 184.59 |
Deep-cooled | 186.39 |
Table 3 Saturation magnetization of hot-rolled bainite obtained by PR1 before and after nitrogen deep-cooled.
Group | Saturation magnetization (emu/g) |
---|---|
Hot-rolled bainite | 184.59 |
Deep-cooled | 186.39 |
Fig. 3. Microstructural characterization for the final dual-phase morphology by PR1. (a) secondary electron images showing mixed martensitic phase (lighter area) and ferrite (darker area); (b) magnified part in (a) showing precipitates dispersed in the ferrite and distinct phase boundary represented by yellow dashed-line; (c) distribution of HAGB (high angle grain boundary, separated by the critical orientational difference as 15 degree) and kernel average misorientation (KAM) map of selected area (red rectangle) is inserted in the left top; (d) the orientational distribution figure (ODF) shows every grain’s orientation in microstructure i.e. paralleled to TD (transverse direction), the actual crystal orientation, with the orientation and corresponding color showed in the left bottom and statistic distribution diagram of grain size is inserted in the right top. RD: rolling direction; ND: normal direction.
Group | Saturation magnetization (emu/g) |
---|---|
Dual phase microstructure | 180.61 |
Deep-cooled | 181.78 |
Table 4 Saturation magnetization of the dual phase microstructure obtained by PR1 before and after nitrogen deep-cooled.
Group | Saturation magnetization (emu/g) |
---|---|
Dual phase microstructure | 180.61 |
Deep-cooled | 181.78 |
Fig. 4. TEM results for martensitic phase corresponding to the dual-phase morphology obtained by PR1 (a,b,d,e,f,g,h,i) and dislocation configurations (c) of martensitic phase in PR3, where, TEM bright field image for the blocky area of martensite is shown in (a), whose magnified STEM images (b) corresponds well with EBSD results of the ultra-fine martensitic grains (Fig. 3(c) and (d)). (c) shows the dislocation configuration of martensitic phase in PR3, where dislocation arrays introduced stripes can be observed. Corresponding to the two white frames shown in Fig. 4(b), HRTEM images from [011] axis for undistorted lattice structure, dislocation arrays and distorted lattice structure of blocky area are shown in (d), (e) and (f); coherent nano-sized precipitates exist in undistorted crystal (g); and moreover, typical lamella area in martensite is shown in TEM (a) and BF-STEM (h), in which the white frame corresponds to the HRTEM image (i), showing twins identified by period arrangement of two oriented crystals.
Fig. 5. Microstructural characterization of the blocky area in martensitic phase corresponding to the dual-phase morphology obtained by PR1 (Fig. 3), where substructure of blocky area in martensitic phase is shown in the bright field STEM (BF-STEM) image (a), low angle dark field STEM (LADF-STEM) image (b) and high angle annular dark field STEM (HAADF-STEM) image (c) from [001] axis of martensite. HRTEM and inverse Fourier transform result of distorted martensitic lattice are respectively shown in (d) and (e), from [001] zone-axis of martensitic lattice.
Fig. 6. Fracture morphology and deformation behavior of the current dual-phase steel by PR1. (a) low-magnified overview of fracture by secondary electron image to show two different fracture areas; (b) magnified center area in white frame of Fig. 6(a); (c) magnified side area in white frame of Fig. 6(a); (c) the crack initiated from deformed martensite split through ferrite observed from TD (transverse direction); (e) BF-STEM image to show high density dislocations in blocky area of martensitic phase and low density of dislocations in ferrite; (f): TEM image to show high density dislocations in blocky area of martensitic phase and corresponding stretched diffraction points in white frame. Inset in (f) is the diffraction pattern.
Fig. 7. The evolution of martensite deformation by SEM images: before tensile (a), before necking (b) and after failure (c). The deformation and local strain after failure can be observed because the martensite grains are stretched along horizontal direction (rolling direction/tensile direction).
Fig. 8. Recrystallization and precipitation in the first-stage annealing of PR1. (a): Secondary electron images of microstructure after 5 min annealing, where, massive and acicular BCC phase sustained their morphology with cementite particles already observed; (b, c): Secondary electron images of microstructure after 7 min annealing, where recrystallized equiaxial fine or coarse ferrite grains and cementite are observed. (d, e): ex-situ TEM results of microstructure after 5 min annealing, where, dislocation walls are found and vanadium carbide precipitates along gathered dislocations; (f): ex-situ TEM results of microstructure after 7 min annealing, where recrystallized and un-recrystallized areas can be observed and the inserted diffraction pattern captured from un-recrystallized area. (g): ex-situ TEM results of microstructure after 7 min annealing, where, vanadium carbides and cementite are surrounded by recrystallized ferrite, and in return, impede the boundary migration. (h) HRTEM image of coherent vanadium carbide in ferrite matrix. (i): diffraction pattern captured from un-recrystallized area.
Fig. 9. In situ TEM observation of reverse austenitic transformation. The first state shown in (a) is set as 0 s, and the following images (b-i) represent 4 s, 7 s, 9 s, 13 s, 18 s, 20 s, 23 s, 34 s respectively in the second-stage isothermal annealing shown in Fig. S3a. The yellow dashed line represents phase boundary while the white dashed line represents grain boundary. Planar phase boundary (PBa) between γ0 and α is firstly observed, with a distance from a VC particle. Initially, PBa arches (b) and reach to touch the VC particle ahead of PBb and PBc, with its central part suddenly touching the VC particle (c, d). The invasion of γ0 into α is dragged down by the VC, in contrast with continuous moving forward and merging together between PBc and PBd (e, f, g), which leaves the VC particle trapped inside the austenite γ0 (h and i).
Fig. 10. Crystallographic analysis of martensitic transformation mechanism. (a) shows the bright field TEM image of adjacent ferrite and martensitic phase acquired from recrystallized microstructure heated to 740 °C then water-quenched in PR1; (b) shows magnified area of ferrite /martensitic phase boundary in (a), where ferrite, martensitic phase and VC are all coherent in between; (c) shows the VC constraint to martensitic phase; (d) presents schematic diagram of reverse austenite transformation following experimental results, which highlighted the continuous coherent N—W (Nishiyama-Wassermann) relationship between VC, ferrite and austenite, with red line as the PB between ferrite and austenite; (e) presents schematic diagram of Bogers-Burgers-Olson-Cohen transformation mechanism: first shear for the stacking order of ABC shift to ABAB, as ε martensite, then another shear for HCP structure to BCT structure; (f) presents schematic diagram of the new shear mechanism proposed based on coherent VC constraint, where the close packed plane between VCs also shear from ABC order to ABAB order, together with simultaneous stretch of close-packed plane and dilatation perpendicular to the close-packed plane, completing the FCC to BCC/BCT transformation.
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