CN105039847B - 铌合金化tam钢及其制造方法 - Google Patents
铌合金化tam钢及其制造方法 Download PDFInfo
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- CN105039847B CN105039847B CN201510504662.7A CN201510504662A CN105039847B CN 105039847 B CN105039847 B CN 105039847B CN 201510504662 A CN201510504662 A CN 201510504662A CN 105039847 B CN105039847 B CN 105039847B
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- steel
- niobium
- temperature
- tam
- niobium alloy
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- 239000010959 steel Substances 0.000 title claims abstract description 105
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 103
- 239000010955 niobium Substances 0.000 title claims abstract description 23
- 229910052758 niobium Inorganic materials 0.000 title claims abstract description 21
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium Chemical compound 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- 229910052739 hydrogen Inorganic materials 0.000 abstract description 14
- UFHFLCQGNIYNRP-UHFFFAOYSA-N hydrogen Chemical compound data:image/svg+xml;base64,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 data:image/svg+xml;base64,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 [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 abstract description 14
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- SZVJSHCCFOBDDC-UHFFFAOYSA-N Iron(II,III) oxide Chemical compound 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- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound 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Abstract
本发明涉及一种铌合金化TAM钢及其制造工艺，属于金属成分设计与热加工技术领域。本发明一种铌合金化TAM钢，其化学成分按重量百分比计为：C 0.18～0.21％、Si 1.48～1.55％、Mn 1.90～2.20％、P≤0.020％、S≤0.015％、Nb 0.04～0.06％、Al≤0.04％，余量为Fe和不可避免杂质。本发明采用铌合金化方式加入适量的铌，通过铌的碳化物等的析出改善了TAM钢的强韧性，从而提高了含铌TAM钢的综合力学性能，使钢板具有较高的强度和塑性，尤其具有优异的抗氢致延迟断裂性能。本发明含铌TAM钢的生产采用新工艺—Q&P工艺使钢材组织性能更加稳定。
Description
技术领域
[0001] 本发明涉及一种铌合金化ΤΑΜ钢及其制造工艺，属于金属成分设计与热加工技术 领域。
背景技术
[0002] ΤΑΜ钢，又称TRIP型退火马氏体钢（TRIP-aided Annealed Martensite Matrix)， 是 Q&P 钢的一种。汽车用Q&P( Quenching and Part it ioning)钢作为第三代 AHSS( Advanced High Strength Steels)钢，具有天然优势，达到了强度与塑性的良好匹配，实验室数据显 示，汽车用Q&P钢的强度在lOOOMPa以上，并且延伸率达到18%以上，完全能胜任保险杠（防 撞横梁）、侧防撞梁(W型)等部件的要求。ΤΑΜ钢最大的特点是突破了传统TRIP钢的多边形铁 素体基体或者贝氏体基体组织，使用了板条马氏体在两相区重新加热时形成的退火板条马 氏体组织，配合以板条间片状残余奥氏体，获得了优异的力学性能。这类钢一般可通过加入 Nb、V和Ti，利用析出物进行强化。而Nb是一种强碳氮化物形成元素，能够细化晶粒，与其它 元素一起既能提高钢的强度也能改善钢的韧性。Nb亦可经济有效地提高钢的氢致延迟断裂 的阻力。近年来，超高强度钢的开发以及氢致延迟断裂问题的日益突出，Nb在改善超高强度 钢的耐氢致延迟断裂方面的作用也得到大量的研究。
[0003] 其中，相变诱发塑性钢(TRIP钢)之所以比其他高强度钢性能优异的原因是根据钢 的合金化合相变原理，采用特定的化学成分和独特的热处理工艺，充分运用钢中"相变诱发 马氏体效应"的结果。当钢中含有一定量的奥氏体形成元素，再经过两相区(α+γ)温度内临 界退火和在随后的中温贝氏体等温淬火，从而得到较大量的残余奥氏体，当钢受到载荷作 用发生变形时，就会使钢中的残余奥氏体进行诱发马氏体相变，导致钢的强度，塑性显著提 高，即为"TRIP效应"。
[0004] 而对于钢热处理的新工艺一一Q&P工艺，与传统的淬火-回火工艺不同，其是为了 得到稳定的残余奥氏体，应用钢中含Si，A1(甚至P)元素，以阻碍Fe 3C的析出，使碳自马氏体 分配到奥氏体，奥氏体应富碳，在再次冷却时不会转变为马氏体，为高强度钢兼具韧性提供 新的有效工艺。同时，稳定的奥氏体薄膜在马氏体束周围形成后，减少氢致裂纹扩展速率， 从而提高了钢抗氢致延迟断裂性能。
[0005] 现有技术中对TRIP钢的研究大多采用不添加铌的普通钢，而且工艺仅仅使用传统 工艺，其制备的TRIP钢的综合力学性能，例如强度和塑性，尤其是其抗氢致延迟断裂性能， 均还不能满足第三代汽车用钢的要求。
发明内容
[0006] 本发明所要解决的第一个技术问题是提供一种具有更好的强度和塑性，尤其是具 有优异的抗氢致延迟断裂性能的铌合金化ΤΑΜ钢。
[0007] 铌合金化ΤΑΜ钢，其化学成分按重量百分比计为：C 0.18~0.21%、Si 1.48~ 1.55%、]^1.90~2.20%、？彡0.020%、5彡0.015%、他0.04~0.06%^1彡0.04%，余量为 Fe和不可避免杂质。
[0008] 进一步的，作为优选的技术方案，上述所述铌合金化ΤΑΜ钢，其化学成分按重量百 分比计为：C 0.1963%、Si 1.53%、Mn 2.13%、P 0.0067%、S 0.0056%、Nb 0·05%、Α1 0.0088%，余量为Fe和不可避免杂质。
[0009] 上述所述铌合金化ΤΑΜ钢，其屈服强度RP〇. 2> 500MPa，抗拉强度Rm> 1050MPa，断后 伸长率A>25%，强塑积RmXA>25GPa· %。
[0010] 进一步的，作为优选的技术方案，上述所述银合金化ΤΑΜ钢，钢的屈服强度¥.2 = 709MPa，抗拉强度Rm=1148MPa，断后伸长率Α = 30·1%，强塑积RmXA = 34.6GPa · %。
[0011 ]上述所述银合金化ΤΑΜ钢，其金相组织为马氏体基体+残余奥氏体+贝氏体/铁素体 的混合组织。
[0012] 本发明由于采用新型铌合金化成分设计的板坯含铌的碳化物等的析出改善了ΤΑΜ 钢的强韧性，从而提高了含铌ΤΑΜ钢的综合力学性能，尤其表现在含铌钢具有优异的抗氢致 延迟断裂性能，本钢种可充分利用攀钢钒钛磁铁矿资源。通过系统、科学地掌握钢材中各种 组织缺陷和析出物的氢陷阱潜力，建立起储氢钢铁材料和超高强度钢的抗氢致延迟断裂的 解决方案，无论是对于第三代汽车用钢的开发与应用具有重要意义，对未来氢能源的利用 提供战略性材料储备技术，促进国民经济可持续发展，维护国家能源安全提供材料保障。同 时可使我国在这一领域的研究处在国际前沿，形成具有自主知识产权的材料设计和控制技 术。
[0013] 本发明所要解决的第二个技术问题是提供一种铌合金化ΤΑΜ钢的制备方法。
[0014]铌合金化ΤΑΜ钢的制备方法，其具体包括传统机械乳制工艺冶炼、热乳、冷乳和新 工艺Q&P工艺：
[0015] a、机械乳制工艺:将钢坯冶炼浇铸成板坯，在1150~1250°C下加热70~90min后， 再热乳乳制成3~5mm厚热乳钢板，再经过冷乳乳制到1~1.5mm，冷乳压下率为65~75%，得 到铁素体+珠光体组织;其中，热乳终乳温度750~850°C，卷取温度650~700°C ;
[0016] b、Q&P工艺:将a步骤得到的冷乳板，先以10 °C /s升温至奥氏体化温度900~920 °C， 保温600s，再以50°C/s降温至室温;然后以10°C/s重新升温至退火温度760~850°C，保温 600s，再以50°C/s降温至配分温度150~450°C，保温50~200s，最后以50°C/s降温至室温， 即得。
[0017] 进一步的，作为更优选的技术方案，上述所述铌合金化ΤΑΜ钢的制备方法：
[0018] a步骤中板坯优选在1200 °C下加热80min后，再热乳乳制成4mm厚热乳钢板，再经过 冷乳乳制得到1.2mm后冷乳钢板，冷乳压下率为70% ;其中，热乳终乳温度优选为800°C，卷 取温度优选为670 °C ;
[0019] b步骤中将a步骤得到的冷乳板，先以10°C/s升温至奥氏体化温度920°C，保温 600s，再以50°C/s降温至室温;然后以10°C/s重新升温至退火温度800°C，保温600s，再以50 °C/s降温至配分温度400°C，保温200s，最后以50°C/s降温至室温，即得本发明金相组织为 马氏体基体+残余奥氏体+贝氏体/铁素体的混合组织ΤΑΜ钢。
[0020] 上述所述优选铌合金化ΤΑΜ钢的制备方法制备的ΤΑΜ钢，其屈服强度RpQ. 2 = 709MPa，抗拉强度Rm=1148MPa，断后伸长率Α = 30·1%，强塑积RmXA = 34.6GPa · %。
[0021] 其中，a步骤中热乳工艺可以采用2050热乳带钢乳机，在冷乳机上冷乳前需要将热 乳钢板酸洗，以除去表面氧化皮及油污。
[0022]本发明采用铌微合金化方式加入适量的铌，通过铌的碳化物等的析出改善了 ΤΑΜ 钢的强韧性，从而提高了含铌ΤΑΜ钢的综合力学性能，使钢板具有较高的强度和塑性，尤其 具有优异的抗氢致延迟断裂性能。本发明含铌ΤΑΜ钢的生产工艺方法，与常见生产方法相比 增加了 一次中间退火过程，使钢材组织性能更加稳定。
具体实施方式
[0023] 铌合金化ΤΑΜ钢，其化学成分按重量百分比计为：C 0.18~0.21%、Si 1.48~ 1.55%、]^1.90~2.20%、？彡0.020%、5彡0.015%、他0.04~0.06%^1彡0.04%，余量为 Fe和不可避免杂质。
[0024]进一步的，作为优选的技术方案，上述所述铌合金化ΤΑΜ钢，其化学成分按重量百 分比计为：C 0.1963%、Si 1·53%、Μη2·13%、Ρ 0.0067%、S 0.0056%、Nb 0·05%、Α1 0.0088%，余量为Fe和不可避免杂质。
[0025] 上述所述铌合金化ΤΑΜ钢，其屈服强度RP〇. 2> 500MPa，抗拉强度Rm> 1050MPa，断后 伸长率A>25%，强塑积RmXA>25GPa· %。
[0026] 进一步的，作为优选的技术方案，上述所述铌合金化ΤΑΜ钢，钢的屈服强度心〇.2 = 709MPa，抗拉强度Rm=1148MPa，断后伸长率Α = 30·1%，强塑积RmXA = 34.6GPa · %。
[0027] 上述所述铌合金化ΤΑΜ钢，其金相组织为马氏体基体+残余奥氏体+贝氏体/铁素体 的混合组织。
[0028] 本发明由于采用新型铌合金化成分设计的板坯含铌的碳化物等的析出改善了ΤΑΜ 钢的强韧性，从而提高了含铌ΤΑΜ钢的综合力学性能，尤其表现在含铌钢具有优异的抗氢致 延迟断裂性能，本钢种可充分利用攀钢钒钛磁铁矿资源。通过系统、科学地掌握钢材中各种 组织缺陷和析出物的氢陷阱潜力，建立起储氢钢铁材料和超高强度钢的抗氢致延迟断裂的 解决方案，无论是对于第三代汽车用钢的开发与应用具有重要意义，对未来氢能源的利用 提供战略性材料储备技术，促进国民经济可持续发展，维护国家能源安全提供材料保障。同 时可使我国在这一领域的研究处在国际前沿，形成具有自主知识产权的材料设计和控制技 术。
[0029] 铌合金化ΤΑΜ钢的制备方法，其具体包括传统机械乳制工艺冶炼、热乳、冷乳和新 工艺Q&P工艺：
[0030] a、机械乳制工艺:将钢坯冶炼浇铸成板坯，在1150~1250°C下加热70~90min后， 再热乳乳制成3~5mm厚热乳钢板，再经过冷乳乳制到1~1.5mm，冷乳压下率为65~75%，得 到铁素体+珠光体组织;其中，热乳终乳温度750~850°C，卷取温度650~700°C ;
[0031] b、Q&P工艺:将a步骤得到的冷乳板，先以10 °C /s升温至奥氏体化温度900~920 °C， 保温600s，再以50°C/s降温至室温;然后以10°C/s重新升温至退火温度760~850°C，保温 600s，再以50°C/s降温至配分温度150~450°C，保温50~200s，最后以50°C/s降温至室温， 即得。
[0032] 进一步的，作为更优选的技术方案，上述所述铌合金化ΤΑΜ钢的制备方法：
[0033] a步骤中板坯优选在1200 °C下加热80min后，再热乳乳制成4mm厚热乳钢板，再经过 冷乳乳制得到1.2mm后冷乳钢板，冷乳压下率为70% ;其中，热乳终乳温度优选为800°C，卷 取温度优选为670 °C ;
[0034] b步骤中将a步骤得到的冷乳板，先以10°C/s升温至奥氏体化温度920°C，保温 600s，再以50°C/s降温至室温;然后以10°C/s重新升温至退火温度800°C，保温600s，再以50 °C/s降温至配分温度400°C，保温200s，最后以50°C/s降温至室温，即得本发明金相组织为 马氏体基体+残余奥氏体+贝氏体/铁素体的混合组织ΤΑΜ钢。
[0035] 上述所述优选铌合金化ΤΑΜ钢的制备方法制备的ΤΑΜ钢，其屈服强度RpQ.2 = 709MPa，抗拉强度Rm=1148MPa，断后伸长率Α = 30·1%，强塑积RmXA = 34.6GPa · %。
[0036] 其中，a步骤中热乳工艺可以采用2050热乳带钢乳机，在冷乳机上冷乳前需要将热 乳钢板酸洗，以除去表面氧化皮及油污。
[0037] 下面结合实施例对本发明的具体实施方式做进一步的描述，并不因此将本发明限 制在所述的实施例范围之中。
[0038] 实施例1
[0039] 本发明铌合金化ΤΑΜ钢的各成分组成百分比参照表1所示：
[0040] 表1铌合金化ΤΑΜ钢的组成百分比
[0041]
[0042] 按照表1中铌合金化ΤΑΜ钢的各成分组成百分比进行传统机械乳制工艺冶炼、热 车L、冷乳和新工艺Q&P工艺，其传统机械乳制工艺具体工艺参数见表2:
[0043] 表2机械乳制工艺具体工艺参数
[0044]
[0045] 新工艺Q&P工艺具体工艺参数见表3:
[0046] 表3 Q&P工艺具体工艺参数
[0047]
[0048] 按照表1中铌合金化ΤΑΜ钢的各成分组成百分比和表2机械乳制工艺、表3Q&P工艺， 制得的ΤΑΜ钢的力学性能见表4:
[0049] 表4铌合金化ΤΑΜ钢的力学性能
Claims (3)
1. 铌合金化ΤΑΜ钢的制备方法，其特征在于:包括以下步骤： a、 机械乳制工艺:将钢材冶炼浇铸成板坯，在1150~1250°C下加热70~90min后，热乳 得到3~5mm厚热乳钢板，再经过冷乳得到1~1.5mm厚冷乳钢板;其中，热乳终乳温度750~ 850°C，卷取温度650~700°C，冷乳压下率为65~75% ; b、 Q&P工艺:将a步骤得到的冷乳板，先以10°C/s升温至奥氏体化温度900~920°C，保温 600s，再以50°C/s降温至室温;然后以10°C/s重新升温至退火温度760~850°C，保温600s， 再以50°C/s降温至配分温度150~450°C，保温50~200s，最后以50°C/s降温至室温，即得铌 合金化ΤΑΜ钢； 所述铌合金化ΤΑΜ钢的化学成分按重量百分比为:C 0.18~0.21%、Si 1.48~1.55%、 皿111.90~2.20%、？彡0.020%、5彡0.015%、恥0.04~0.06%^1彡0.04%，余量为卩6和不 可避免杂质。
2. 根据权利要求1所述铌合金化ΤΑΜ钢的制备方法，其特征在于:a步骤中板坯在1200Γ 下加热80min后，再热乳乳制成4mm厚热乳钢板，再经过冷乳乳制得到1.2mm厚冷乳钢板;其 中，热乳终乳温度为800 °C，卷取温度为670 °C，冷乳压下率为70 %。
3. 根据权利要求1所述铌合金化ΤΑΜ钢的制备方法，其特征在于:b步骤中奥氏体化温度 为920°C ;退火温度为800°C ;配分温度为400°C，配分温度下保温200s。
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