CN104342601B - 一种Rel≥400MPa的含Ti低锰低硅热轧钢及用CSP线生产方法 - Google Patents
一种Rel≥400MPa的含Ti低锰低硅热轧钢及用CSP线生产方法 Download PDFInfo
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- CN104342601B CN104342601B CN201410651492.0A CN201410651492A CN104342601B CN 104342601 B CN104342601 B CN 104342601B CN 201410651492 A CN201410651492 A CN 201410651492A CN 104342601 B CN104342601 B CN 104342601B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 63
- 239000010959 steel Substances 0.000 title claims abstract description 63
- 239000011572 manganese Substances 0.000 title claims abstract description 30
- 229910052748 manganese Inorganic materials 0.000 title claims abstract description 20
- 229910052710 silicon Inorganic materials 0.000 title claims abstract description 20
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 239000010703 silicon Substances 0.000 title claims abstract description 11
- 229910001208 Crucible steel Inorganic materials 0.000 title 1
- 238000001816 cooling Methods 0.000 claims abstract description 21
- 229910000529 magnetic ferrite Inorganic materials 0.000 claims abstract description 15
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 15
- 229910034327 TiC Inorganic materials 0.000 claims abstract description 14
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 7
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 7
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 6
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 5
- 238000010438 heat treatment Methods 0.000 claims abstract description 4
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N silicon Chemical compound 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[Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N manganese Chemical compound 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- 238000005728 strengthening Methods 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound 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- 239000000126 substance Substances 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N tin hydride Chemical compound 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[Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 4
- 229910017083 AlN Inorganic materials 0.000 description 3
- PIGFYZPCRLYGLF-UHFFFAOYSA-N aluminum nitride Chemical compound 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Abstract
一种Rel≥400MPa的含Ti低锰低硅热轧钢，其组分及wt%为：C：0.070%~0.20%，Si：不超过0.05%，Mn：0.10%~0.50%，P：≤0.015%，S：≤0.005%，N：≤0.006%，Als：0.015~0.060%，Ti:0.05~0.20%；用CSP生产步骤：冶炼并连铸成坯；对连铸坯加热；轧制；层流冷却；卷取；自然冷却至室温。本发明提供了一种钢中尺寸小于10nm的TiC比例在50%以上，组织为铁素体+珠光体，或铁素体+贝氏体组织；并通过采用适量的廉价Ti微合金，减少钢中Mn和Si的使用量，可使成本比现有技术降低不低于10%；屈服强度在345~700MPa，抗拉强度在400~800MPa，延伸率≥20%，产品的带状组织明显减轻，延伸率明显提高，表面质量和焊接性能大大提高，产品的综合力学性能得到提升。
Description
技术领域
[0001] 本发明涉及一种低合金高强度结构用钢及生产方法，具体地属于一种Rel彡 400MPa的含Ti低锰低硅热乳钢及用CSP线生产的方法。
背景技术
[0002] 目前国内低合金高强度结构钢涵盖了屈服强度从345MPa到690MPa的系列钢材，在 实际生产中，为了满足钢材强度的需要，在钢中添加了0.60%以上，最高2.0%的合金元素 Μη， 也添加了其它合金元素 Si、Nb、V等合金元素。合金元素 Μη在钢中容易导致板坯中心偏析和 表面铁皮和裂纹等问题，且Μη含量过高也影响材料的焊接性能。另外添加合金元素也直接 增加了钢材的制造成本。近年来，随着Ti微合金化技术的进步，Ti微合金被广泛应用于钢材 的生产中。
[0003] 经检索：中国专利公开号为CN 103614627A的文献，其公开了一种含Ti系列钢的柔 性生产技术，其产品的屈服强度420~680MPa，抗拉强度最高达到760MPa，延伸率最高达到 30%，其化学成分为，C :0.04~0.08%，SK0.05%，Mn:0.60~1.20%，Als:0.02~0.05%，P:< 0.015%，11 :0.07~0.10%，5彡0.010%小彡0.005%，主要工艺参数为加热温度1150~1300°(：，终 乳温度850~950°C，终冷温度550~750°C，层流冷却速度5~50°C/s。
[0004] 还有中国专利公开号为CN 102839321A的文献，其公开了一种屈服强度大于 500MPa的超薄热乳板带及其制造方法，其化学成分为C: 0.02~0.07%，Si :彡0.50%，Mn: 0.50~ 1.40%，Al:0.01~0.20%，P:<0.030%，Ti:0.03~0.11%，N<0.005%，S<0.010%，0<0.004%，S C：0.17-0.20%,Si ： ^0.50%,Μη：0.50-0.90%,A1:0.01-0.20%,P： ^0.030%,Ti :0.03-0.08%, N彡0 · 005%，S彡0 · 010%，0彡0 · 004%，主要工艺参数加热温度1180~1250°C，终乳温度87(K930 °C，层流冷却速率30~70 °C/s，卷取温度560~680 °C。
[0005] 还有中国专利公开号为CN 1785543A的文献，其公开了一种采用Ti微合金化生产 高强耐候钢板的工艺，其化学成分为C: 0 · 04~0 · 07%，Si : 0 · 30~0 · 50%，Mn: 0 · 40~1 · 20%，Alt: 0.025-0.035%,P： ^0.075-0.10%,Ti ： 0.020-0.15%,N^0.006%, S^0.00 5%,0^0.004%,Cu： 0 · 20~0 · 40%，Ni :0 · 15~0 · 35%，Cr: 0 · 3(Mh 50%，0彡0 · 003%，主要工艺参数铸坯入炉温度900~ 1100°C，加热温度 1050~1180°C，终乳温度850~910°C，卷取温度550~650°C。
[0006] 上述三个现有专利存在的主要不足在于钢中添加了较高的Mn Jn高一是对钢材的 力学性能尤其冷弯性能产生不利影响，其二是显著增加了钢材的制造成本。另外，在生产工 艺中，由于采用了较低的冷却速度，因此钢中容易形成较粗大的铁素体组织，降低钢材的强 度，且容易在晶界析出大颗粒的Tie粒子，降低钢材的强度，抑制了钢中Ti的强化作用。
发明内容
[0007] 本发明针对现有技术存在的不足，提供一种钢中尺寸小于l〇nm的Tie比例在50%以 上，组织为铁素体+珠光体，或铁素体+贝氏体组织，屈服强度在345~700MPa，抗拉强度在400 ~800MPa，延伸率彡20%的Rel彡400MPa的含Ti低锰低硅热乳钢及生产方法。
[0008] 实现上述目的的措施：
[0009] 一种Rel彡400MPa的含Ti低锰低硅热乳钢，其组分及重量百分比含量为:C: 0.070% ~0 · 20%，Si :不超过0 · 05%，Μη: 0 · 10%~0 · 50%，P:彡0 · 015%，S:彡0 · 005%，N:彡0 · 006%，A1 s: 0.015~0.060%，11:0.05~0.20%，其余为?6和不可避免的杂质;钢中尺寸小于1011111的11(：比例 在50%以上，组织为铁素体+珠光体，或铁素体+贝氏体组织，屈服强度在345~700MPa，抗拉强 度在400~800MPa，延伸率彡20%。
[0010] 用CSP线生产一种Rel彡400MPa的含Ti低锰低硅热乳钢的方法，其步骤：
[0011] 1)冶炼并连铸成坯；
[0012] 2)对铸坯加热:控制铸坯入炉温度在50~1000°C，出炉温度在1050°C~1250°C，铸坯 在炉时间10~200min;
[0013] 3)进行乳制:控制终乳温度在80(K920°C ;
[0014] 4)进行层流冷却:进行三段层流冷却，前段冷却速率50~200°C/s，中间空冷段冷却 时间2~20s，后段冷却速率5~30°C/s;
[0015] 5)进行卷取，卷取温度控制在580°0650°C ;
[0016] 6)自然冷却至室温。
[0017] 优选地:终乳温度84(K900 °C ;
[0018] 优选地:前段冷却速率70~200°C/s，中间空冷段冷却时间5~20s，后段冷却速率10~ 30°C/s；
[0019] 优选地:卷取温度590~630°C。
[0020] 本发明中各组分及主要工艺的机理及作用
[0021] C:碳在钢中主要起固溶强化作用，并与钢中的Ti形成TiC细小颗粒，起到固溶强化 和析出强化的作用，有效提高钢材的强度和耐疲劳性能。碳含量低于0.07%时，C的强化作用 太小，碳含量高于〇. 20%时，钢中铁素体含量减少，而珠光体增加，降低钢材的塑性和延伸 性，另外碳含量过高也会影响钢材的焊接性能，因此钢中的C含量选择为0.07%~0.20%。
[0022] Μη: Μη在钢中起固溶强化作用，含量过低，强化作用太小，因此最低Μη含量为 0.05%，Μη含量过高容易在板带厚度中心形成偏析，降低产品延伸性，因此最高Μη含量为 0.50%，且过高Μη含量显著增加钢材制造成本。
[0023] Si: Si含量过高，容易造成表面缺陷，因此最高Si含量限定在0.05%。
[0024] P:P为钢中的杂质元素，易于在晶界偏聚，影响产品的韧性，因此其含量越低越好。 根据实际控制水平，应控制在〇. 015%以下。
[0025] S:S为钢中的杂质元素，易在晶界产生偏聚，且与钢中的Fe形成低熔点的FeS，降低 钢材的韧性，炼钢时应充分去除，应控制在〇. 005%。
[0026] N:N为钢中的杂质元素，降低钢材的韧性，容易和钢中Al、Ti形成A1N和TiN，含量过 高，易形成粗大的A1N和TiN，因此尽量降低其含量，应控制在0.006%以下。
[0027] A1:A1在钢中起到固溶强化作用，且A1在炼钢过程中起到脱氧的作用，因此钢中A1 的最低含量为〇. 015%，但A1含量过高容易与钢中的N形成粗大的A1N颗粒，造成钢材的韧性 降低，因此A1最高含量为0.060%。
[0028] Ti:Ti在钢中起到固溶强化作用，Ti与钢中的C在铁素体基体上形成纳米TiC，提高 铁素体基体的强度和抗疲劳性。Ti还可以与钢中的N形成TiN，组织钢材加热时的晶粒长大。 因此Ti的最低含量为0.05%。但Ti含量过高容易形成粗大的TiC颗粒，和粗大的TiN，从而降 低钢材的韧性，且Ti含量过高增加成本，最高为0.20%。
[0029] 在本发明中，之所以控制层流冷却为三段冷却，且前段冷却速率在50~200°C/s，是 因为前段层流冷却速率太低容易使钢中析出粗大的TiC颗粒，降低钢材的强度，且容易形成 粗大的铁素体晶粒。冷却速率高于200°C/s时，容易造成板带表面应力分布不均，造成板形 不良，且容易产生低温组织，降低钢材的性能。中间空冷2~20s有利于钢中铁素体组织的形 成，提高钢材的韧性。后段冷却速率太低容易形成过多的铁素体组织，降低钢材的强度，太 高容易造成低温组织的形成，不利于钢材的组织控制。之所以卷取温度控制在580~650°C， 是因为在此温度区间，TiC的析出效率最高，且析出的TiC颗粒细小，强化作用最高。温度太 高易于形成粗大的TiC颗粒，降低强化效果，温度太低，则不容易析出，Ti的强化效果同样减 弱。
[0030] 本发明提供了一种钢中尺寸小于10nm的TiC比例在50%以上，组织为铁素体+珠光 体，或铁素体+贝氏体组织;并通过采用适量的廉价Ti微合金，减少钢中Μη和Si的使用量，可 使成本比现有技术降低不低于10%;屈服强度在345~700MPa，抗拉强度在400~800MPa，延伸 率多20%，广品的带状组织明显减轻，延伸率明显提尚，表面质量和焊接性能大大提尚，广品 的综合力学性能得到提升。
具体实施方式
[0031] 下面对本发明予以详细描述：
[0032] 表1为本发明各实施例及对比例的取值列表；
[0033] 表2为本发明各实施例及对比例的主要工艺参数列表；
[0034] 表3为本发明各实施例及对比例性能检测情况列表。
[0035] 本发明各实施例用CSP线按照以下步骤生产：
[0036] 1)冶炼并连铸成坯；
[0037] 2)对铸坯加热：出炉温度在1050°C~1280°C，铸坯在炉时间10~200min;
[0038] 3)进行乳制:控制终乳温度在800~920°C ;
[0039] 4)进行层流冷却:进行三段层流冷却，前段冷却速率50~200°C/s，中间空冷段冷却 时间2~20s，后段冷却速率5~30°C/s;
[0040] 5)进行卷取，卷取温度控制在580°C~650°C ;
[0041] 6)自然冷却至室温。
[0042] 表1本发明实施例化学成分列表(wt%)
[0044] 表2本发明各实施例及对比例的主要工艺参数列表
[0045] 表3本发明各实施例性能检测情况列表
[0047] 从表2可以看出，本发明尺寸小于lOnm的TiC占比在50%以上，组织为铁素体+珠光 体或少量贝氏体，屈服强度在345~700MPa，抗拉强度在400~800MPa，延伸率在20%以上。
[0048] 本申请的具体实施方式仅为例举，并非对本发明技术方案的限制性实施。
Claims (1)
1.用CSP线生产一种Rel彡400MPa的含Ti低锰低硅热乳钢的方法，其步骤： 所述含Ti低锰低硅热乳钢的组分及重量百分比含量为：C: 0.080%~0.20%，Si :不超过 0.05%,Mn：0.10%-0,50%, P ：^0,015%, S： ^0.005%, N： ^0.006%, Als :0.015-0.060%, Ti: 0.11~0.20%，其余为Fe和不可避免的杂质；钢中尺寸小于10nm的TiC比例在50%以上，组织为 铁素体+珠光体，或铁素体+贝氏体组织，屈服强度在345~700MPa，抗拉强度在400~800MPa， 延伸率彡20%; 1) 冶炼并连铸成坯； 2) 对铸坯加热：控制铸坯入炉温度在50~1000°C，出炉温度在1050°C~1250°C，铸坯在炉 时间 l(K200min; 3) 进行乳制:控制终乳温度在800~850°C ; 4) 进行层流冷却：进行三段层流冷却，前段冷却速率70~200°C/s，中间空冷段冷却时间 9~20s，后段冷却速率5~30°C/s; 5) 进行卷取，卷取温度控制在580 °C~640 °C ; 6) 自然冷却至室温。
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