材料科学与技术 ›› 2018, Vol. 34 ›› Issue (5): 737-744.DOI: 10.1016/j.jmst.2017.11.020
所属专题： High Strength Alloys-2018； Stainless Steel & High Strength Steel 2018
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收稿日期:2017-08-11修回日期:2017-09-22接受日期:2017-10-01出版日期:2018-05-10发布日期:2018-05-04
Formation mechanism and control methods of acicular ferrite in HSLA steels: A review
Yi Shao, Chenxi Liu*(
), Zesheng Yan, Huijun Li, Yongchang Liu*()
- State Key Lab of Hydraulic Engineering Simulation and Safety, School of Materials Science and Engineering, Tianjin University, Tianjin 300350, China
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Received:2017-08-11Revised:2017-09-22Accepted:2017-10-01Online:2018-05-10Published:2018-05-04 -
Contact:Liu Chenxi,Liu Yongchang
引用本文
. [J]. 材料科学与技术, 2018, 34(5): 737-744.
Yi Shao, Chenxi Liu, Zesheng Yan, Huijun Li, Yongchang Liu. Formation mechanism and control methods of acicular ferrite in HSLA steels: A review[J]. J. Mater. Sci. Technol., 2018, 34(5): 737-744.
Fig. 1. Phase transformation fractions, determined by dilatometric measurements, as a function of temperature during continuous cooling, in the X65 pipeline steel specimens austenitized at the different temperatures from 850 °C to 1000 °C [28].
Fig. 2. Optical micrographs of X65 pipeline steel specimens after continuous cooling, with the different austenitizing temperatures as: (a) 850 °C, (b) 900 °C, (c) 950 °C and (d) 1000 °C [28].
Fig. 3. Optical micrographs of the Nb-bearing HSLA steel specimens after quenching (with a rate of 13 °C/s), with different austenitizing temperatures as: (a) 1050 °C, (b) 1200 °C [45].
Fig. 4. The phase transformation fraction, f, as fitted by the analytical phase transformation model as a function of the transformation temperature of HSLA steel samples subjected to various cooling rates: (a) 700 °C/min, (b) 900 °C/min and (c) 1100 °C/min [49].
| Cooling rate (°C/min) | v0 (m/s) | QI (kJ/mol) |
|---|---|---|
| 700 | 9.3 × 10-2 | 98.3 |
| 900 | 10.3 × 10-2 | 84.5 |
| 1100 | 8.6 × 10-2 | 72.1 |
Table 1 Kinetics parameters for interface-controlled growth stage as determined by fitting the JMAK model [49].
| Cooling rate (°C/min) | v0 (m/s) | QI (kJ/mol) |
|---|---|---|
| 700 | 9.3 × 10-2 | 98.3 |
| 900 | 10.3 × 10-2 | 84.5 |
| 1100 | 8.6 × 10-2 | 72.1 |
Fig. 5. The phase fractions of acicular ferrite and martensite as a function of temperature for specimens with different cooling rates (martensite transformation is indicated by circles) [57].
Fig. 6. Volume fraction of acicular ferrite, as fitted by the displacive phase transformation model as a function of the isothermal time for the different isothermal temperatures in a HSLA steel [61].
Fig. 7. Schematic illustration of intercritical heat treatment.
Fig. 8. Optical micrographs of the specimens after (a) directly slow cooling (10 °C/min)[47], (b) directly medium cooling (500 °C/min)[57], (c) directly fast cooling/quenching (6000 °C/min) [57], and (d) intercritical normalizing treatment [69] (P: pearlite; F: polygonal ferrite; LB: lower bainite; M: martensite; AF: acicular ferrite).
Fig. 9. Scanning microscope photographs of the samples after (a) quenching +intercritical quenching [73], (b) quenching +intercritical normalizing [73], and (c) normalizing + intercritical normalizing[66] (WC: water cooling, AC: air cooling).
Fig. 10. Optical micrograph of the specimen after (a) step quenching +tempering [74] and (b) step normalizing +tempering [69].
Fig. 11. Effect of austenitizing temperatures on (a) impact energy and (b) yield tensile ratio of the samples after directly quenching +tempering (QT), step quenching +tempering (SQT) and intercritical quenching +tempering (IQT) [74].
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