Effect of tempering temperature on the microstructure and low-temperature impact toughness of vanadium-contained X80 pipeline steel
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摘要: 为了明确轧后回火温度对含钒X80管线钢低温冲击韧性的影响，通过多种微观结构表征手段，对经过不同轧后回火温度处理的六组试验钢显微结构进行了研究，阐明其与低温冲击韧性之间的关系。结果表明，回火温度由450 ℃提高到650 ℃，钢中纳米尺度析出相尺寸与数量增加，钢中针状/板条状铁素体及粒状贝氏体的尺寸和数量降低，多边形铁素体增多，钢中大角度晶界比例降低，低温冲击韧性主要由析出相的尺寸和数量主导，呈现逐渐降低的变化趋势；而当回火温度升高至700 ℃时，钢中细小析出相数量比例降低，平均尺寸增大，显微组织主要由粗大的多边形铁素体构成，且大角度晶界比例和Σ3晶界占比显著增高，晶界结构特征为该条件下低温冲击韧性的主要影响因素，冲击功大幅提升，高达307.28 J。Abstract: In this paper, in order to clarify the influence of tempering temperature after thermo-mechanical control process on the low-temperature impact toughness of vanadium-contained X80 pipeline steel, the microstructural variation including nano-scale precipitates, microstructure, grain boundaries, and crystallographic characteristics, in experimental steels processed under six different tempering temperatures were investigated by multiple microstructural characterization methods. Furthermore, the relationship between the steel microstructures and low-temperature impact toughness was revealed. The results showed that with increasing tempering temperature from 450 ℃ to 650 ℃, the size and number of nano-scale precipitates in steel increased, while the size and quantity of granular acicular/lath ferrite and bainite decreased. Under these conditions, the low-temperature impact toughness was primarily dominated by the size and quantity of precipitates, exhibiting a gradually decreasing trend. Meanwhile, the number of polygonal ferrite increased and the ratio of high angle grain boundaries decreased. These microstructural changes led to a gradual decrease in low-temperature impact toughness. However, as the tempering temperature increased to 700 ℃, the ratio of fine precipitates in steel decreased and the average size increased. Moreover, the microstructure composed of coarse polygonal ferrite, with a significant increase in the ratio of high angle grain boundaries and Σ3 grain boundaries. Under tempering treatment at 700 ℃, the structural characteristics of grain boundaries were the main factors influencing low-temperature impact toughness. The impact energy of the steel tempered at 700 ℃ has been greatly improved, reaching up to 307.28 J.
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Key words:
- tempering temperature /
- X80 pipeline steel /
- vanadium /
- low temperature toughness
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图 1 试验钢热加工路线示意
Figure 1. Schematic diagram of hot working process for experimental steel
图 2 试验钢冲击试样取样示意
Figure 2. Schematic diagram for sampling impact test specimens of experimental steel
图 3 试验钢中析出相数量与尺寸统计
Figure 3. Statistics of the number and size of precipitates in experimental steels
图 5 试验钢在不同回火温度下回火后的显微组织
Figure 5. Microstructure of experimental steels after tempering at different temperatures
（a）H450；（b）H500；（c）H550；（d）H600；（e）H650；（f）H700
图 6 试验钢在不同回火温度下回火后的晶粒取向
Figure 6. Grain orientation map of experimental steels after tempering at different temperatures
（a）H450；（b）H500；（c）H550；（d）H600；（e）H650；（f）H700
图 7 试验钢在不同回火温度下回火后CSL晶界占比
1-Σ3, 2-Σ5, 3-Σ7, 4-Σ9, 5-Σ11,6-Σ13a, 7-Σ13b, 8-Σ15, 9-Σ17a, 10-Σ17b, 11-Σ19a, 12-Σ19b, 13-Σ21a, 14-Σ21b, 15-Σ23, 16-25a, 17-Σ25b, 18-Σ27a, 19-Σ27b, 20-Σ29a, 21-Σ29b
Figure 7. Distribution of CSL grain boundaries in the experimental steel after tempering at different temperatures
(a) H450; (b) H500; (c) H550; (d) H600; (e) H650; (f) H700
图 8 不同回火温度下回火后在-20 ℃下的冲击功
Figure 8. Impact energy at -20°C after tempering at different temperatures
图 9 不同回火温度下回火后冲击断口宏观形貌
Figure 9. Macroscopic morphology of impact fracture surface of experimental steel after tempering at different temperatures
（a）冲击断口形貌示意；宏观形貌：（b）H450；（c）H500；（d）H550；（e）H600；（f）H650；（g）H700
图 10 不同回火温度下试验钢冲击断口微观形貌
（a）H450钢纤维区；（b）H500钢纤维区；（c）H550钢纤维区；（d）H550钢放射区；（e）H600钢纤维区；（f）H600钢放射区；（g）H650钢纤维区；（h）H650钢放射区；（i）H700钢纤维区
Figure 10. Microscopic morphology of impact fracture surfaces of experimental steels after tempering at different temperatures
表 1 试验用X80管线钢化学成分
Table 1. Chemical composition of experimental X80 pipeline steel
% C Si Mn S Ni Mo Cr V Nb Ti O Al N Fe 0.034 0.15 1.80 0.0040 0.22 0.11 0.25 0.120 0.03 0.005 0.0050 0.03 0.0033 Bal. 
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表 2 试验钢中析出相平均直径
Table 2. Average diameter of precipitates in experimental steels
nm H450 H500 H550 H600 H650 H700 13.76 ± 4.21 13.89 ± 4.33 14.08 ± 5.02 14.83 ± 4.00 14.96 ± 4.91 17.53 ± 5.39
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表 3 试验钢中大角度晶界比例
Table 3. Proportion of high-angle grain boundaries in experimental steels
% H450 H500 H550 H600 H650 H700 29.39 21.7 21.53 20.62 15.35 65.68
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