CN115261742A - 一种抗拉强度1000MPa热冲压部件及其制造方法 - Google Patents

一种抗拉强度1000MPa热冲压部件及其制造方法 Download PDF

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CN115261742A
CN115261742A CN202110480760.7A CN202110480760A CN115261742A CN 115261742 A CN115261742 A CN 115261742A CN 202110480760 A CN202110480760 A CN 202110480760A CN 115261742 A CN115261742 A CN 115261742A
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equal
1000mpa
percent
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CN115261742B (zh
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刘浩
谭宁
洪继要
毕文珍
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to JP2023566557A priority patent/JP2024515833A/ja
Priority to AU2022263750A priority patent/AU2022263750A1/en
Priority to PCT/CN2022/090627 priority patent/WO2022228574A1/zh
Priority to EP22795043.3A priority patent/EP4332246A1/en
Priority to BR112023021820A priority patent/BR112023021820A2/pt
Priority to KR1020237041326A priority patent/KR20240005821A/ko
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Abstract

一种抗拉强度1000MPa热冲压部件及其制造方法，其化学成分重量百分比为：C 0.05～0.20％，Si 0.02～1.00％，Mn 0.5～2.0％，P≤0.10％，S≤0.05％，Al 0.01～0.30％，Nb 0.01～0.0.04％，Ti 0.01～0.06％，Cr：0.12～0.50％，B0.001～0.05％，其余为Fe及其它不可避免的杂质，且需要同时满足，0.24％≤C+Mn/6≤0.45％，0.05％≤Nb+Ti+B×10≤0.15％。获得的热冲压部件原始奥氏体平均晶粒尺寸≤10μm，VDA冷弯角≥80°，室温冲击韧性≥80J/cm2，屈服强度≥800MPa，抗拉强度≥1000MPa，断裂延伸率≥6％，热冲压部件在具有高强度的同时还获得高韧性，因此可广泛应用于汽车、船舶、机械等行业。

Description

一种抗拉强度1000MPa热冲压部件及其制造方法
技术领域
本发明涉及汽车材料技术领域，具体涉及一种抗拉强度1000MPa热冲压部件及其制造方法。
背景技术
随着自然环境恶化和石油能源紧缺问题的日益加剧，绿色和安全成为汽车制造业发展的主要方向。目前相关研究表明随着汽车用钢强度等级的逐渐增加，尤其抗拉强度大于1000MPa的钢板在冷成形过程中，冷冲压成形能力显著恶化，导致成形零件尺寸精度较差甚至部分位置出现开裂。热冲压成形部件具有高强化、成形能力强、回弹量低等特点，因此其产品成为汽车结构轻量化的重要技术解决方案之一。热冲压产品可广泛应用于白车身A/B柱、防撞梁、中通道等安全结构件，因此市场需求量日益增加。
目前市场上应用的热冲压产品集中在1500MPa强度级别，其韧性方面VDA冷弯角约50°，室温冲击韧性约40J/cm2。与其相比1000MPa热冲压产品具有更高的韧性，因此可以应用于对韧性有更高要求的吸能零件。1000MPa级别的高韧性热冲压产品材料性能方面具有更高的碰撞性能，在结构加强件作为吸能区域，其兼具高强度和良好的局部碰撞等优势。目前已公布1000MPa强度级别热冲压用钢获得高强高韧的同时在成分设计添加多数昂贵元素，生产制造多采用复杂的多阶段控制工艺，存在弊端。
中国专利CN107810281B公开了“用于压制硬化的钢和由这样的钢制造的压制硬化的部件”可获得抗拉强度高于950MPa且冷弯角高于75°的压制硬化部件，但其成分设计需要多量微合金元素，且钢板生产过程中采用高温退火处理，部件生产热冲压工艺采用两阶段冷却控制处理等，导致制造工序复杂，实际操作困难较大。
中国专利CN105829562B公开了“一种热压钢板构件、及其制造方法以及热压用钢板”，合金成分添加0.060～0.20％Ti元素，并要求控制全部Ti满足90％的析出，另外工艺上热冲压后冷却采用两阶段冷却，获得热冲压构件仅实现强度980MPa以上，未提及热冲压构件具备高韧性。
中国专利CN104838030B公开了“一种具有增强的韧性的热冲压产品和其制造方法”，其合金成分设计B≤0.001％，主要是借助Mo等其他昂贵合金提高淬火获得马氏体能力实现性能高强化。
综上，目前传统的高强度热冲压用钢存在韧性不足、碰撞吸能效果较差等问题。
发明内容
本发明目的在于提供一种抗拉强度1000MPa高韧性热冲压部件及其制造方法，获得的热冲压部件的屈服强度≥800MPa，抗拉强度≥1000MPa，断裂延伸率≥6％，VDA冷弯角≥80°，室温冲击韧性≥80J/cm2，热冲压部件在具有高强度的同时还获得高韧性，解决了现有高强度热冲压部件韧性不足、碰撞吸能效果较差的问题，使其可广泛应用于汽车、船舶、机械等行业。
为达到上述目的，本发明提供的技术方案是：
一种抗拉强度1000MPa热冲压部件，其化学成分重量百分比为：C：0.05～0.20％，Si：0.02～1.00％，Mn：0.5～2.0％，P≤0.10％，S≤0.05％，Al：0.01～0.30％，Nb：0.01～0.04％，Ti：0.01～0.06％，Cr：0.12～0.50％，B：0.001～0.05％，其余为Fe及其它不可避免的杂质，且需要同时满足：
0.24％≤C+Mn/6≤0.45％；
0.05％≤Nb+Ti+B×10≤0.15％；
所述热冲压部件原始奥氏体平均晶粒尺寸≤10μm，VDA冷弯角≥80°，室温冲击韧性≥80J/cm2。
进一步，所述热冲压部件成分按照重量百分比还可以包括：Ni：0.01～1.0％，Mo：0.01～0.5％，V：0.01～0.5％中一种或几种。
优选的，所述P≤0.05％。
优选的，所述S≤0.01％。
本发明所述热冲压部件的显微组织中马氏体与贝氏体面积占比≥75％，剩余部分由铁素体、残余奥氏体或两者混合构成。
本发明所述热冲压部件的屈服强度≥800MPa，抗拉强度≥1000MPa，断裂延伸率≥6％。
在本发明的成分设计中：
C：是实现强度和硬度提升的关键性元素，碳含量不低于0.05％保证钢板热冲压部件的强度和淬透性，使热冲压部件抗拉强度达到目标要求。另外随着碳含量的增加，热冲压部件的塑性、韧性和焊接性能等会出现恶化，因此，本发明将C含量控制在0.05～0.20％。
Si：添加一定量的Si能溶于铁素体和奥氏体中提高热冲压部件强度和硬度，当Si的含量超过1.0％之后，影响热冲压部件的可镀性，因此，本发明将Si含量控制在0.02～1.0％。
Mn：具有脱氧和脱硫作用，还能提高热冲压部件的硬度和强度。Mn是奥氏体强稳定化元素，其作用仅次于Ni元素，可显著增加热冲压部件的淬透性，为了保证热冲压部件的强度，钢中Mn含量不低于0.5％。另外Mn含量高于2.0％，会恶化热冲压部件的可制造性和可焊接性，因此，本发明将Mn含量控制在0.5～2.0％。
C+Mn/6是合金成分碳当量的重要组成，碳当量是反应材料强度、韧性和焊接性能的充分体现。合金成分C+Mn/6＜0.24％，热冲压部件不能保证具有较高的抗拉强度，且材料获得马氏体能力不足；合金成分C+Mn/6＞0.48％热冲压部件马氏体组织C、Mn含量较高，易获得较高碳马氏体，会显著恶化材料韧性，另外碳当量高于0.45％会显著降低焊接性能，因此，本发明控制0.24％≤C+Mn/6≤0.45％。
P、S：P和S都是有害元素，P元素偏析会导致热冲压部件出现冷脆现象；高温状态下S偏析会降低塑性甚至导致热脆现象发生。本发明设计主要目的是显著提高材料韧性，需要控制P≤0.05％，S≤0.01％。
Al：作为脱氧元素，热冲压部件中最好含有0.01％以上的Al，但是，如果热冲压部件中含有较多的Al，会形成粗大的氧化物，恶化热冲压部件的综合性能。因此，本发明Al含量控制在0.01～0.3％。
Nb：是重要的微合金元素，一方面Nb起到固溶强化作用；另一方面Nb和C、N都有极强的结合力，能与之形成稳定的化合物，细化晶粒，提高热冲压部件的强度、韧性，同时使热冲压部件具有良好的冷弯性能，且Nb的碳氮化物作为氢陷阱可降低氢致延迟开裂敏感性。因此，本发明中Nb含量控制在0.01～0.04％，低于0.01％细化晶粒效果不足，高于0.04％产品成本较高。
Ti：是重要的微合金元素，其与氮、氧、碳具有较强的亲和力，是一种良好的脱氧和固定氮有效元素，避免硼与氮形成BN。另外Ti起到细化晶粒的效果，可提升材料韧性。但是Ti含量太高，易形成块状的氮化物恶化韧塑性能。因此，本发明Ti含量控制在0.01～0.06％，可提高热冲压部件的韧塑性能。
B：主要作用是极大地增加钢的淬透性，从而节约其他昂贵的金属。B的添加有提高淬透性具有最佳的范围区间，高于一定量则淬透性增加效果不明显，因此，本发明中B含量控制在0.001～0.05％。
其中成分Nb、Ti、B元素从不同角度显著细化热冲压部件晶粒组织，Nb/Ti析出碳氮化合物在热冲压部件生产中均能细化晶粒，B提高淬透性，两者组合作用提高韧性。Nb/Ti具有相似的效果，添加含量数量级一致，但是微量的B就可达到显著提高淬透性的效果，若合金成分Nb+Ti+B×10＜0.05％，热冲压部件组织不能得到显著细化，尤其原始奥氏体平均晶粒尺寸大于10μm，不能实现高韧性；合金成分Nb+Ti+B×10＞0.15％，一方面合金含量再增加细化效果不明显，另一方面增加合金成本，因此，本发明控制0.05％≤Nb+Ti+B×10≤0.15％。
Cr：有效提高热冲压部件的淬透性，与Mn作用类似，进一步提高热冲压部件的强度和韧性，而且添加Cr元素可防止后续热冲压加热过程中高温表面氧化，因此本发明Cr含量控制在0.12～0.5％。
Ni、Mo和V：均为稳定的保证热冲压部件强韧性能的有效元素。Ni可以提高钢的强度，降低钢的低温脆性转变温度，对提高冲击韧性具有重要意义。Mo能显著提高钢的淬透性，细化奥氏体晶粒，防止回火脆性，提高热冲压部件强度和韧性。V通过细小碳氮化物形式细化奥氏体晶粒，提高钢的韧性。因此，Ni、Mo、V均能保证热冲压部件在具有高强度的同时具有良好的的韧性。
综合考虑钢的合金成本和元素效果饱和度，本发明还可以包含Ni：0.01～1.0％，Mo：0.01～0.5％，V：0.01～0.5％中一种或几种合金成分。
本发明成分主要采用低碳微合金化设计思路，通过C固溶强化和C/Mn复合提高淬透性确保热冲压部件强度要求，添加微量Nb、Ti、B等微合金元素进一步显著细化热冲压部件晶粒尺寸，包括原始奥氏体晶粒尺寸，获得高强度、高韧性热冲压部件。优选地部分添加Ni、Mo、V等合金元素，进一步提高热冲压部件强度和韧性。
本发明所述的抗拉强度1000MPa热冲压部件的制造方法，包括如下步骤：
1)冶炼、铸造
按照上述成分冶炼、铸造成板坯；
2)热轧、卷取、酸洗
所述板坯加热出炉温度为1100～1260℃，终轧温度为830～880℃；
卷取温度为580～650℃，后经酸洗获得热轧板坯；
3)冷轧、退火
冷轧总压下量为40～80％，退火温度为720～780℃；
4)热冲压成形
退火后钢板加热温度Ac3～960℃，加热时间2～10min；随后转移至模具进行冲压成形，成形温度≥700℃；
之后以大于30℃/s冷却速率冷却至200℃以下，获得热冲压部件。
进一步，步骤3)中，所述退火后钢板组织中呈网状弥散分布的马氏体和碳化物颗粒面积占比为10～40％，且单个马氏体或碳化物颗粒面积小于25μm2。
更进一步，步骤3)中，所述退火后钢板组织中80％以上颗粒纵横比为0.5～2.0。
又，所述步骤3)退火后，对钢板进行涂覆，获得带有镀层的钢板，且所述镀层单面重量平均值为20～120g/m2。
优选的，所述镀层为纯锌镀层、锌铁合金镀层、含有Al和Mg的锌系合金镀层或铝硅合金镀层。
进一步，所述步骤4)热冲压成形前，将钢板与其它强度级别热冲压部件用钢通过激光拼焊技术焊接在一起，形成拼焊部件。
按照上述成分制备钢坯，经过热轧、冷轧、退火获得无镀层钢板，或经过热轧、冷轧、退火后，以任意方式对钢板进行涂覆获得带镀层钢板。
本发明针对热冲压部件生产工艺进行控制，热轧坯料加热出炉温度1100～1260℃，如果加热温度低于1100℃，微合金元素不能充分溶解，很难保证热冲压部件的强度。如果加热温度高于1260℃，热冲压部件的组织容易粗化，恶化韧性。控制终轧温度在830～880℃，保证终轧在奥氏体未再结晶区间轧制，细化晶粒组织，进一步提高热冲压部件的韧性。
由于本发明中添加有微量的Nb、Ti微合金元素，为了使铌钛碳化物在卷取过程中析出较多，卷取温度控制在580～650℃，可获得较高比例的呈现纳米尺度分布NbC、TiC析出，获得的NbC、TiC抑制后续热冲压加热过程中原始奥氏体晶粒长大，有利于细化原始奥氏体晶粒尺寸。卷取温度低于580℃，铌钛碳化物未能达到良好的析出效果，热轧后钢板强度较高不利于后续冷轧变形，造成冷轧制造难度加大；卷取温度高于650℃，一方面热轧过程晶粒长大速率加快造成晶粒粗大，不利于全流程晶粒细化控制，另一方面钢板表面局部会出现氧化，不利于后续酸洗工艺控制，且会影响钢板的可镀性。
冷轧总压下量控制在40～80％，如果冷轧总压下量小于40％，组织破碎程度较低导致晶粒细化效果不明显，如果冷轧总压下量大于80％，钢板内部残余硬度较大，且带状组织较多，不利于后续生产，并且会显著恶化热冲压部件韧性。
热轧后退火是为了进一步控制钢板的晶粒尺寸和形状，确保热冲压部件能够获得高韧性。基于成分设计，退火温度控制在720～780℃，保证退火后获得的钢板组织中80％以上晶粒近似呈现等轴状，即晶粒形状纵横比值满足0.5～2.0，较高比例的等轴状晶粒可以减少带状组织、细化初始钢板组织，后续热冲压部件组织可以细化，退火温度高于780℃导致晶粒尺寸显著增大。
退火温度控制在720～780℃，组织中沿着铁素体晶界弥散分布细小的马氏体和碳化物颗粒，马氏体和碳化物均是富碳相，另外面积小于25μm2的细小颗粒物在组织中占比10～40％，显著增加有效晶界面积，富碳相和有效晶界是奥氏体优先形核点，有益于增加奥氏体形核率，促进形核进而细化原始奥氏体晶粒尺寸。组织中马氏体和碳化物颗粒面积占比高于40％，导致退火后钢板性能较高不利于后续落料加工，组织中马氏体和碳化物颗粒面积占比小于10％不能有效增加晶界面积。鉴于上述控制晶粒尺寸才能获得高韧性热冲压部件，钢板需在720～780℃完成退火。
本发明热冲压钢板加热温度低于AC3，钢板组织不能实现完全奥氏体化，加热时间低于2min，钢板奥氏体化程度以及碳化物溶解等不充分；热冲压温度高于960℃或加热时间超过10min，奥氏体晶粒粗大，会造成热冲压部件韧性显著降低。钢板变形温度低于700℃时变形困难且易析出较多铁素体等组织，后续需控制热冲压成形后冷却速度大于30℃/s，是获得马氏体组织的临界冷却速率，淬火冷却至200℃以下，用来保证热冲压部件强度和韧性满足设计要求。
退火完成后获得钢板可以是无镀层裸板，也可以为了减少钢板加热表面氧化铁皮和后续耐腐蚀性能恶劣等的影响，在钢板表面涂覆合金镀层，镀层涂覆量控制在20～120g/m2，镀层涂覆量小于20g/m2时现场生产端控制程度较难而且热冲压部件抗腐蚀效果不佳，镀层涂覆量大于120g/m2，抗腐蚀效果饱和且成本加大。
所述镀层可是纯锌镀层；也可以是锌铁合金镀层，例如Zn-Fe、Zn-Al、Zn-Mg、Zn-Al-Mg等合金镀层；还可以是含有Al和Mg的锌系合金镀层或铝硅合金镀层，例如包含0～4％Fe、5～11％Si、余量为铝及不可避免杂质的铝硅合金镀层。
本发明的有益效果：
本发明成分主要采用低碳微合金化设计思路，通过C固溶强化和C/Mn复合提高淬透性确保热冲压部件强度要求，添加微量Nb、Ti、B等微合金元素，并控制0.24％≤C+Mn/6≤0.45％，0.05％≤Nb+Ti+B×10≤0.15％，显著细化热冲压部件晶粒尺寸，保证热冲压部件的原始奥氏体平均晶粒尺寸≤10μm，改善高强度热冲压部件的韧性，解决现有高强度热冲压部件韧性不足、碰撞吸能效果较差的问题，使其可广泛应用于汽车、船舶、机械等行业。
本发明在制备工艺中，由于本发明采用添加微量的微合金成分，将卷取温度控制在580～650℃，保证NbC、TiC获得较高比例的析出，获得的NbC、TiC抑制后续热冲压加热过程中原始奥氏体晶粒长大，细化原始奥氏体晶粒尺寸；进一步，控制退火温度在720～780℃，保证退火后获得的钢板组织中80％以上晶粒近似呈现等轴状，这样才能保证钢板进行热冲压后原始奥氏体晶粒尺寸得到细化，原始奥氏体平均晶粒尺寸≤10μm，使高强度热冲压部件的韧性得到很大提高，获得热冲压部件的屈服强度≥800MPa，抗拉强度≥1000MPa，且，热冲压部件的VDA冷弯角≥80°，室温冲击韧性≥80J/cm2。
附图说明
图1为本发明实施例热冲压部件扫描电镜显微组织照片。
图2为本发明实施例热冲压部件原始奥氏体组织照片。
图3为本发明实施例退火后钢板金相组织照片。
具体实施方式
下面结合实施例对本发明做进一步说明。
本发明实施例具体成分、工艺参数如表1、表2所示，各实施例热冲压部件性能如表3所示。
图1给出了热冲压部件的扫描电镜显微组织照片。从图1可以看出，本发明获得的热冲压部件的显微组织为马氏体、贝氏体和微量残余奥氏体，其中，马氏体与贝氏体面积占比≥75％。
图2可以观察到原始奥氏体平均晶粒尺寸≤10μm。图3可以观察退火后的钢板组织中约85％晶粒形状纵横比值满足0.5～2.0，其中马氏体与碳化物颗粒呈网状弥散分布，且马氏体与碳化物颗粒面积占比大于25％，单个颗粒面积小于25μm2。
从表3性能可以看出，本发明制备热冲压部件的屈服强度≥800MPa，抗拉强度≥1000MPa，VDA冷弯角≥80°，室温冲击韧性≥80J/cm2，断裂延伸率≥6％。
Figure BDA0003049156390000091
Figure BDA0003049156390000101
Figure BDA0003049156390000111

Claims (12)

1.一种抗拉强度1000MPa热冲压部件，其化学成分重量百分比为：C：0.05～0.20％，Si：0.02～1.00％，Mn：0.5～2.0％，P≤0.10％，S≤0.05％，Al：0.01～0.30％，Nb：0.01～0.04％，Ti：0.01～0.06％，Cr：0.12～0.50％，B：0.001～0.05％，其余为Fe及其它不可避免的杂质，且需要同时满足：
0.24％≤C+Mn/6≤0.45％；
0.05％≤Nb+Ti+B×10≤0.15％；
所述热冲压部件原始奥氏体平均晶粒尺寸≤10μm，VDA冷弯角≥80°，室温冲击韧性≥80J/cm2。
2.如权利要求1所述的抗拉强度1000MPa热冲压部件，其特征在于，所述热冲压部件成分按照重量百分比还可包括：Ni：0.01～1.0％，Mo：0.01～0.5％，V：0.01～0.5％中一种或几种。
3.如权利要求1所述的抗拉强度1000MPa热冲压部件，其特征在于，所述P≤0.05％。
4.如权利要求1所述的抗拉强度1000MPa热冲压部件，其特征在于，所述S≤0.01％。
5.如权利要求1～4任一项所述的抗拉强度1000MPa热冲压部件，其特征在于，所述热冲压部件的显微组织中马氏体与贝氏体面积占比≥75％，剩余部分由铁素体、残余奥氏体或两者混合构成。
6.如权利要求1～5任一项所述的抗拉强度1000MPa热冲压部件，其特征在于，所述热冲压部件的屈服强度≥800MPa，抗拉强度≥1000MPa，断裂延伸率≥6％。
7.如权利要求1～6任一项所述的抗拉强度1000MPa热冲压部件的制造方法，其特征在于，包括如下步骤：
1)冶炼、铸造
按照所述成分冶炼、铸造成板坯；
2)热轧、卷取、酸洗
所述板坯加热出炉温度为1100～1260℃，终轧温度为830～880℃；
卷取温度为580～650℃，后经酸洗获得热轧板坯；
3)冷轧、退火
冷轧总压下量为40～80％，退火温度为720～780℃；
4)热冲压成形
退火后钢板加热至Ac3～960℃，加热时间2～10min；随后转移至模具进行冲压成形，成形温度≥700℃；
之后以大于30℃/s的冷却速率冷却至200℃以下，获得热冲压部件。
8.如权利要求7所述的1000MPa热冲压部件的制造方法，其特征在于，步骤3)中，所述退火后钢板组织中呈网状弥散分布的马氏体和碳化物颗粒面积占比为10～40％，且单个马氏体或碳化物颗粒面积小于25μm2。
9.如权利要求7或8所述的1000MPa热冲压部件的制造方法，其特征在于，步骤3)中，所述退火后钢板组织中80％以上颗粒纵横比为0.5～2.0。
10.如权利要求7所述的1000MPa热冲压部件的制造方法，其特征在于，所述步骤3)退火后，对钢板进行涂覆，获得带有镀层的钢板，且所述镀层单面重量平均值为20～120g/m2。
11.如权利要求8所述的1000MPa热冲压部件的制造方法，其特征在于，所述镀层为纯锌镀层、锌铁合金镀层、含有Al和Mg的锌系合金镀层或铝硅合金镀层。
12.如权利要求7或8或9所述的1000MPa热冲压部件的制造方法，其特征在于，所述步骤4)热冲压成形前，将钢板与其它强度级别热冲压部件用钢板通过激光拼焊技术焊接在一起，形成热冲压拼焊部件。
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