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材料研究学报  2020, Vol. 34 Issue (1): 1-15    DOI: 10.11901/1005.3093.2019.371
  研究论文 本期目录 | 过刊浏览 |
超高强度船体结构钢焊接性的研究现状和趋势
雷玄威1,2,周栓宝2,黄继华2()
1. 江西理工大学材料冶金化学学部 赣州 341000
2. 北京科技大学材料科学与工程学院 北京 100083
Current Status and Development Trend on Weldability of Ultra-high Strength Hull Structure Steel
LEI Xuanwei1,2,ZHOU Shuanbao2,HUANG Jihua2()
1. Faculty of Materials, Metallurgy and Chemistry, Jiangxi University of Science and Technology, Ganzhou 341000, China
2. School of Materials Science and Engineering, University of Science and Technology Beijing, Beijing 100083, China
引用本文:

雷玄威,周栓宝,黄继华. 超高强度船体结构钢焊接性的研究现状和趋势[J]. 材料研究学报, 2020, 34(1): 1-15.
Xuanwei LEI, Shuanbao ZHOU, Jihua HUANG. Current Status and Development Trend on Weldability of Ultra-high Strength Hull Structure Steel[J]. Chinese Journal of Materials Research, 2020, 34(1): 1-15.

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摘要: 

基于对超高强度船体结构钢及其焊接接头力学性能的总结和讨论，揭示了超高强度船体结构钢的焊接性问题，即在大线能量焊接条件下热影响区粗晶区的低温韧性较差。从马-奥(M-A)组元的生成和粒状贝氏体的生成两方面，分析了产生该焊接性问题的本质原因。总结了改善超高强度船体结构钢焊接性的途径：应用氧化物冶金技术、引入Cu沉淀强化和提高Ni含量。综合对当前超高强度船体结构钢研究现状的分析，认为超低C和高Ni含量的设计可成为进一步改善超高强度船体结构钢焊接性的思路。
关键词 ： 评述,  金属材料,  焊接性,  超高强度船体结构钢,  大线能量焊接    
Abstract：

Through studies and discussions on mechanical properties of ultra-high strength hull structural (UHSHS) steels and their weld joints, the problem concerning weldability of UHSHS steels was concluded as poor low temperature toughness in coarse-grained heat affected zone (CGHAZ) under large heat input welding procedure. The root causes of this problem were analyzed on two aspects: the formations of martensite-austenite (M-A) constituents and granular bainite. Current three approaches of oxide metallurgy technology application, Cu precipitation introduction and high Ni content design to improve the weldability of UHSHS steels were summarized. Under comprehensive analyses on the current status of UHSHS steels, it is considered that the design of ultra-low C and high Ni content can further improve the weldability of ultra-high strength hull structural steels.
Key words： review    metalic materials    weldability    ultra-high strength hull structure steel    large heat input welding
收稿日期: 2019-07-26     
ZTFLH:  TG142.4  
基金资助:国家重点基础研究发展计划(613280);国家自然科学基金青年科学基金(51904125)
作者简介: 雷玄威，男，1987年生
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https://www.cjmr.org/CN/10.11901/1005.3093.2019.371      或      https://www.cjmr.org/CN/Y2020/V34/I1/1

Strength

grade

Yield strength

/MPa

Tensile strength

/MPa

Impact toughness

AKV/J

420≥420530~680

≥42

≥46

460≥460570~720
500≥500610~770≥50
550≥550670~830≥55
620≥620720~890≥62
690≥690770~940≥69
表1  超高强度船体结构钢及其焊接接头必须满足的力学性能[5]
SteelsGrade/MPaCSiMnAlNbVTiMoCrNiCu
F460[7]4600.0620.231.470.0400.0940.60
F500[8,9]5000.050.241.480.030.0110.260.28
0.060.361.570.040.0060.0380.020.200.220.530.24
F550[10,11]5500.070.261.100.0330.0360.0170.400.350.39
0.0670.171.510.0360.0260.0040.0120.300.310.700.71
E690[11]6900.080.151.580.0250.0950.0150.300.300.701.00
F690[12]6900.070.231.060.0360.0430.0040.0191.0~1.13.0~3.1
表2  国内民用超高强度船体结构钢的化学成份(质量百分数)
No.

Grade

/MPa

CSiMnNiMoCrVTi
945[13,14]4400.140.601.001.000.10.500.05
0.120.541.051.150.110.520.04
921[15]5900.110.270.482.720.231.020.060.026
0.10.20.412.660.251.030.060.016
921A[16,17]5900.070.290.432.650.260.06
0.10.240.462.780.241.110.07
980[18,19]785≤0.130.2~0.40.3~0.64.8~5.30.2~0.35
0.09~0.130.2~0.30.5~0.64.4~4.50.36~0.440.5~0.7
表3  国内舰船用钢的主要化学成份(质量百分数)
No.Grade/MPCSiMnNiMoCuCrAlV
HY80[20,21]5500.160.260.232.930.340.0111.430.030.005
0.120.200.292.420.410.081.490.01
HY85[22]5900.080.250.52.10.30.50.540.03
HY100[23,24]6900.170.220.32.350.250.131.32
0.160.210.262.660.410.151.470.02
HY130[25]8900.120.200.704.800.450.50
表4  国外HY系列钢的主要化学成份(质量百分数)
No.Grade/MPCSiMnNiMoCuCrAlNbV
HSLA80[26,27]5500.0440.320.650.871.120.770.0130.077
0.050.341.001.770.5101.230.610.0250.0370.01
HSLA100[28,29]6900.060.250.843.470.581.540.740.0230.030.004
0.050.350.823.410.601.610.550.03
HSLA115[30]7850.050.220.973.370.561.290.640.020.020.01
HSLA130[31]8900.070.370.793.330.581.720.570.0230.005
表5  国外HSLA系列钢的主要化学成份(质量百分数)
SteelsYield strength/MPaTensile strength/MPaCharpy absorbed energy/J
F460[35] (460 MPa grade)495 (≥460)599 (570~720)AKV–60℃ 335 (≥46)
F500[36] (500 MPa grade)580 (≥500)655 (610~770)AKV–60℃ 194 (≥50)
F550[11] (550 MPa grade)610 (≥550)660 (670~830)AKV–60℃ 212 (≥55)
E690[37] (690 MPa grade)730 (≥690)820 (770~940)AKV–40℃ 210 (≥69)
F690[38] (690 MPa grade)766 (≥690)804 (770~940)AKV–60℃ 230 (≥69)
921A[39] (590 MPa grade)630 (≥590)710 (685~845)AKV–60℃ 180 (≥59)
980[40] (785 MPa grade)939 (≥785)1002AKV–20℃ 149 (≥78.5)
HY80[25] (550 MPa grade)760 (≥550)813 (670~830)AKV–45℃ 250 (≥55)
HY85[41] (590 MPa grade)959 (685~845)AKV–50℃ 226 (≥59)
HY100[25] (690 MPa grade)689 (≥690)814 (770~940)
HY130[25] (890 MPa grade)896 (≥890)986
HSLA100[42] (690 MPa grade)833 (≥690)938 (770~940)AKV–50℃ 179 (≥69)
HSLA115[30] (785 MPa grade)972 (≥785)997AKV–84℃ 100 (≥78.5)
HSLA130[31] (890 MPa grade)896 (≥890)986
表6  几种不同超高船体结构钢的力学性能(对应中国船级社标准)
图1  国内民用超高强度船体结构钢合金总含量的变化趋势
图2  国内民用超高强度船体结构钢碳当量的变化趋势
Steels

Heat input

/kJ·cm–1

Welding method

Tensile strength

/MPa

Fault location

CCS standard

/MPa

F460[45]364Electrogas arc welding584, 586Base metal≥570
F500[36]53Submerged arc welding580Base metal≥610
F550[11]50Submerged arc welding620~664Base metal≥670
E690[11]50Submerged arc welding796~822Base metal≥770
F690[38]35Submerged arc welding798, 809Base metal≥770
表7  大热量输入条件下超高船体结构钢焊接接头的强度
Steels

Heat input

/kJ·cm–1

Method

AGS of CGHAZ

/μm

fGB in CGHAZfM-A in CGHAZCVN/J
F460[35]50Thermal simulation~60~0.75–0.85AKV–60℃ 74
E550[46]~65Thermal simulation~45~0.80–0.90AKV–40℃ 16
F550[11]50Submerged arc welding~60~0.65–0.75~0.15–0.2055≤AKV–60℃ ≤67
E690[47]50Submerged arc welding~40~0.20–0.35~0.10–0.1540≤AKV–40℃≤47
F690[38,48]~35Thermal simulation~60AKV–60℃ 26
HY85[41]50Thermal simulation~82~0.40–0.50~0.05–0.10AKV–50℃ 27
HSLA80[49]40Submerged arc welding~0.10

AKV–50℃ 62

AKV–50℃ 44

HSLA115[50]33.5Submerged arc weldingAKV–51℃ ≤111
表8  大热量输入条件下超高船体结构钢热影响区粗晶区的夏比冲击功
Steels

Heat input

/kJ·cm-1

Welding methodTensile strength/MPaFault location

CCS standard

/MPa

E690[11]15Submerged arc welding808,818Base metal≥770
E/F690[51]21.4Submerged arc welding825Base metal≥770
921A[52]20Arc welding702Base metal≥685
980[19]11Metal active gas welding930Base metal
HY80[53]21.7Submerged arc weldingYield strength 658Base metal≥550
HSLA100[54]25.6Gas metal arc welding869Base metal≥770
表9  常规热输入条件下超高船体结构钢焊接接头的强度
Steels

Heat input

/kJ·cm-1

MethodAGS of CGHAZ/μmfGB in CGHAZfM-A in CGHAZCVN/J
F460[35]30Thermal simulation~35~0.10–0.20AKV–60℃ 321
E550[46]~20Thermal simulation~35~0.30–0.40AKV–40℃ 128
F550[43]15Submerged arc welding107≤AKV–50℃ ≤252
E/F690[51]21.4Submerged arc welding~60–70~0.05–0.15~0.0585≤AKV–50℃ ≤115
HY85[41]15Thermal simulation~70~0.10–0.20~0.05–0.10AKV–50℃ 81
HSLA80[49]20Submerged arc welding

AKV–50℃ 107

AKV–50℃ 198

HSLA100[42]20Shield metal arc welding~75AKV–50℃ ~130
表10  常规热输入条件下超高船体结构钢热影响区粗晶区的的夏比冲击功
Steels

Heat input

/kJ·cm–1

Welding methodAGS of CGHAZ/μmfGB in CGHAZfM-A in CGHAZCVN/J
E690[47]50Submerged arc welding~25~0.10–0.20~0.05–0.1086≤AKV–40℃ ≤117
表11  快速冷却大线能量热输入条件下超高强度船体结构钢热影响区粗晶区的的夏比冲击功
图3  大线能量输入+快速冷却条件下超高强度船体结构钢E690热影响区的韧性
图4  超高强度船体结构钢热影响区粗晶区的韧性
图5  合金含量的提高对整体自由能和组织转变量影响的示意图
图6  冷却速率对整体自由能和组织转变量影响的示意图
AGS of CGHAZ/μmMicrostructure type
≥50~60A portion of AF or main LLB
≤40~50Main LLB
表12  适合超高强度船体结构钢焊接粗晶粒区的组织类型
图7  GB和UB转变碳浓度梯度的示意图[60]
图8  舰船用钢的焊接性与碳含量、碳当量的Graville关系[42,78]
图9  不同级别超高强度船体结构钢Ni和Cu的含量
图10  新开发的超高强度船体结构钢热影响区粗晶区的组织演化
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