CN103361547B - 一种冷成型用超高强度钢板的生产方法及钢板 - Google Patents
一种冷成型用超高强度钢板的生产方法及钢板 Download PDFInfo
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- CN103361547B CN103361547B CN201210092207.7A CN201210092207A CN103361547B CN 103361547 B CN103361547 B CN 103361547B CN 201210092207 A CN201210092207 A CN 201210092207A CN 103361547 B CN103361547 B CN 103361547B
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- steel plate
- production
- steel
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- temperature
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 71
- 239000010959 steel Substances 0.000 title claims abstract description 71
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 28
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 title claims abstract description 15
- 238000000034 method Methods 0.000 claims abstract description 60
- 238000000137 annealing Methods 0.000 claims abstract description 32
- 238000010791 quenching Methods 0.000 claims abstract description 24
- 239000000203 mixture Substances 0.000 claims abstract description 15
- 210000001519 tissues Anatomy 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000005266 casting Methods 0.000 claims abstract description 4
- 239000010960 cold rolled steel Substances 0.000 claims abstract description 3
- 238000005097 cold rolling Methods 0.000 claims abstract description 3
- 238000005098 hot rolling Methods 0.000 claims abstract description 3
- 230000000171 quenching Effects 0.000 claims description 15
- 238000005554 pickling Methods 0.000 claims description 10
- 238000001035 drying Methods 0.000 claims description 7
- 238000005275 alloying Methods 0.000 claims description 5
- 238000005246 galvanizing Methods 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 3
- 238000010583 slow cooling Methods 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 229910052710 silicon Inorganic materials 0.000 abstract description 3
- 229910001566 austenite Inorganic materials 0.000 description 21
- 229910052799 carbon Inorganic materials 0.000 description 13
- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound 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- 230000000717 retained Effects 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N silicon Chemical compound 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- 239000011701 zinc Substances 0.000 description 1
Abstract
本发明提供一种冷成型用超高强度钢板的生产方法及钢板，该方法包括冶炼、铸造、热轧、冷轧，冷轧钢板在带有快冷处理的连续退火生产线加热到奥氏体温度后保温一段时间，而后进行淬火处理，得到M+A为主要组织的钢板，然后在罩式退火炉内进行分配处理。该钢板的成分质量百分数为：C？0.02％～0.60％，Si？0.05％～3.5％，Mn？0.20％～3.50％，0.005％≤P≤0.50％，S≤0.05％，Al？0.02％～3.00％，Cr≤0.50％，Ni≤3.00％，Cu≤0.50％，Mo≤1.50％，V≤0.50％，Ti≤0.20％，Nb≤0.20％，余量为Fe和不可避免的杂质。采用本发明方法生产的钢板具有强度高、可冷成型的优点，而且有效解决了Q&P钢工业化生产的工艺路线。
Description
技术领域
[0001] 本发明属于金属热处理技术领域，具体设及一种冷成型用超高强度钢板的生产方 法和用该方法生产的超高强度钢板。
背景技术
[0002] 近年来，人们对环保、资源和能源的重视不断加强，对汽车的安全标准要求也不断 提高，为了满足节能和安全的要求，要求汽车向轻量化发展，其中W相变强化为主的先进高 强度汽车用钢的开发和应用已成为世界各大钢铁公司研究的主流课题之一。
[0003] 长期W来，传统的泽火和回火工艺被用于生产含马氏体组织的高强度钢。泽火形 成的马氏体可提高钢的强度，回火消除内应力，使马氏体内析出碳化物和残余奥氏体分解， W调整钢的塑初性。一些研究工作已经掲示：在泽火过程中，马氏体条间的残余奥氏体会增 碳，早期的文献也讨论过碳在马氏体和残余奥氏体间的分配，W及在含娃钢中贝氏体相变 时碳会向奥氏体扩散，形成无碳化物贝氏体，然而由于泽火溫度较低，泽火后仅有少量原子 扩散W及回火时明显发生了其它相变，所W碳由马氏体向残余奥氏体分配W稳定奥氏体的 问题并未引起重视，更没有发展成钢的热处理工艺。
[0004] 最近，开发和研究了含娃和儘的在贝氏体区等溫泽火形成的TRIP钢圧.De Moor，S.Lacroix，L.Samek,J.PenningandJ.G.Speer，DilatometricStudyofthe Quench曰ndP曰rtitioningProcess，The3rdInternstion曰IConferenceonAdv曰need StructuralSteelsGyeongju，Korea,AuguSt22-24,2006]。受此启示，美国人将中碳 高娃钢0). 35C-1. 3Mn-0. 74SD进行泽火处理，再在MS2Mf之间一定溫度等溫，使碳由马氏 体分配至残余奥氏体，W稳定残余奥氏体，提高钢的塑初性[M.J.SANT0FIMIA，L.ZHA0,and J.SIETSMA,MicrostructuralEvolutionofaLow-CarbonSteelduringApplication ofQuenchingandPartitioningHeatTreatmentsafterPartialAustenitization， METALLURGICALANDMATERIALSTRANSACTIONSA，V0LUME40A，JANUARY2009,46-57]。运 一新工艺被称为泽火和分配（Q&P--如enchingandPartitioning)工艺。此工艺引起了 国际上的关注。 阳0化]Q&P处理工艺过程为[徐祖耀，泽火-碳分配-回火（Q-P-T)工艺浅介[J]，金属 热处理，第34卷第6期，2009年6月。]:首先对钢进行奥氏体化（完全奥氏体化，即在Ac3 W上保溫或部分奥氏体化即在Aci~Ac3之间保溫），然后泽火至马氏体转变开始溫度（MJ 与终结溫度（Mf)之间的某一溫度，再进行碳的分配处理，最后冷却至室溫。在泽火溫度等 溫进行碳分配处理，称为一步Q&P法。如果加热到泽火溫度W上进行碳分配处理，称为两步 Q&P法。
[0006] 国内[徐祖耀.钢热处理的新工艺[J].热处理，2007,22(1) :1，董辰，江海涛，陈 雨来，唐获，程知松，热处理工艺对Q&P钢微观组织及力学性能的影响[J]，上海金属，第31 卷第 4期 2009 年 7 月]、国外[MatlockDK，KraussG.SpeerJG.Microstruc^resand PropertiesofDirectCooledForgingSteels[J].MaterialsProcessingTechnology， 2001，117 :324;MatlockDK，BrautigamVE，SpeerJG.ApplicationoftheQuenching andPartitioning(Q&P)ProcesstoaMedium-CarbonHighSiMicroalloyedBar Steel[J].MaterSciForum，2003,4262432:1089;S.S.Nayak，R.Anumolu，R.D.K.Misra， K.H.Kim，D.L.Lee，Microstructure-hardnessrelationshipinquenchedand partitionedmedium-carbonandhigh-carbonsteelscontainingsilicon，Materials ScienceandEngineeringA498(2008)442-456 ;A.J.Clarke*，J.G.Speer,M.K.Miller， 民.E.Hackenberg，D.V.Edmonds，D.K.Matlock，F.C.民izzo,K.D.Clarke，E.DeMoor，Carbon partitioningtoaustenitefrommartensiteorbainiteduringthequenchand partition(Q&P)process：Acriticalassessment，ActaMaterialia56 (2008) 16-22]的 材料工作者近年来都致力于Q&P钢的工艺及成分、组织的研究工作，但一般都仅限于实验 室研究，没有工业生产方面的报道。
发明内容
[0007] 本发明的目的在于克服上述现有技术所存在的不足，提供一种可实现Q&P钢板生 产的冷成型用超高强度钢板的生产方法，W及应用该方法生产出的具备冷成型性能的超高 强度钢板。
[0008] 本发明是运样实现的，该冷成型用超高强度钢板的生产方法包括冶炼、铸造、热 牵L冷社，其特点是冷社钢板在带有快冷处理的连续退火生产线加热到奥氏体溫度后保溫 一段时间，而后进行泽火处理，得到M+A为主要组织的钢板，然后在罩式退火炉内进行分配 处理。
[0009] 本发明生产方法所述钢板的成分质量百分数为：C0. 02%~0. 60%，SiO. 05%~ 3. 5%，Mn0. 20 % ~3. 50 %，0. 005 %《P《0. 50 %，S《0. 05 %，A10. 02 % ~3. 00 %， Cr《0. 50 %，Ni《3. 00 %，Cu《0. 50 %，Mo《1. 50 %，V《0. 50 %，Ti《0. 20 %， Nb《0. 20%，余量为化和其它不可避免的杂质。
[0010] 本发明生产方法所述连续退火生产线的加热溫度为700~900°C，保溫时间10 秒-180秒，泽火冷却速度在30°C/s~2000°C/s,泽火后钢板的溫度控制在室溫~400°C， 然后在此溫度保溫20秒-300秒后缓冷至室溫；所述罩式退火炉内进行分配处理的溫度为 200~600°C，分配处理的时间为IOmin~10化。
[0011] 本发明生产方法可W依据钢板合金元素含量的多少选择对钢板的酸洗、烘干处理 在连续退火处理后还是在罩式退火炉分配处理后，W及对酸洗烘干后的钢板是否进行电锻 儀或电锻锋处理。
[0012] 采用本发明方法生产的冷成型用超高强度钢板的成分质量百分数为：C0. 02%~ 0. 60%，Si0. 05%~3. 5%，Mn0. 20%~3. 50%，0. 005%《P《0. 50%，S《0. 05%，A1 0. 02%~3. 00%，Cr《0. 50%，Ni《3. 00%，Cu《0. 50%，Mo《I. 50%，V《0. 50%， Ti《0. 20%，Nb《0. 20%，余量为化和其它不可避免的杂质。
[0013] 本发明选择上述各特征及其具体参数的原因如下：
[0014] 连续退火生产线+罩式退火炉内分配处理钢板的方法获得超高强度钢板的原因 在于，现有的连续退火生产线，一般均没有再加热功能，且不能够提供足够长的分配处理时 间。
[0015] 钢板在连续退火生产线加热到奥氏体溫度保溫一段时间，而后进行泽火处理，得 到M+A为主要组织的钢板，钢板在连续退火生产线加热的溫度为700~900°C，保溫时间 10秒-180秒，泽火冷却的速度在30°C/s~2000°C/s,泽火后钢板的溫度控制在室溫~ 400°C，然后在此溫度保溫20秒-300秒后缓冷至室溫。加热到奥氏体区保溫，目的在于得到 均匀的奥氏体组织；低于700°C，钢板不能奥氏体化，高于900°C，将使奥氏体晶粒粗大化， 并引起钢板强度的下降，易引起炉内断带；泽火速度低于30°C/s,将不能得到M+A组织；必 须得到M+A为主要组织的原因在于，可在随后的分配过程中实现C原子由M向A中的分配， 得到富碳的A，泽火溫度控制在室溫~400°C，溫度过低得到的A量较少，溫度过高M的量较 少，甚至不能产生M，M的量较少必然导致A中的C含量不足。
[0016] 连续退火后的钢板在罩式炉内分配处理，分配处理的溫度为200~600°C，分配处 理的时间为IOmin~10化。分配溫度低于200°C，钢中C原子的活动能力不足，达不到C原 子再分配的效果，高于600°C，将使得M发生分解，降低钢板的强度。
[0017] 依据合金元素含量的多少选择对连续退火处理后的钢板进行酸洗、烘干处理，也 可W对酸洗烘干后的钢板进行电锻儀或电锻锋处理。当钢板中的Si、Mn等合金元素含量 较高时，严重恶化钢板的表面状态，并且影响后处理工艺，此时可W对钢板进行酸洗处理， 除去钢板表面的氧化物；对钢板进行电锻儀或电锻锋处理的目的在于增加钢板的热浸锻性 能。在分配处理后再进行酸洗、电锻可进一步提高表面质量，同时电锻儀、锋处理可W提高 钢板的防腐蚀能力。
[0018] 钢板中的C含量控制在CO. 02%~0. 60%，C可W稳定奥氏体，碳含量过低钢板强 度不足，且在分配的过程没有足够的C原子向残余奥氏体中富集，得到的残余奥氏体稳定 性不足，含量过高将对成型性能、焊接性能不利。
[0019] Si含量控制在0. 05%~3. 5%，Si含量过低，不能够阻碍渗碳体的析出，起到稳定 奥氏体的作用，娃含量过高，将引起钢板表面在退火过程中的选择性氧化，生成的氧化物影 响钢板的表面质量及后处理工艺。
[0020] Mn含量控制在0. 20%~3. 50%,Mn是奥氏体稳定化元素，Mn含量过低，钢的强度 和泽透性均不足，Mn含量过高可能导致奥氏体体积增多，Mn含量过高钢的带状组织十分严 重，影响性能的均一性。
[0021] P含量《0.50%，一定含量的P可W部分替代Si的功能，同时起到强化作用，但含 量过高将引起钢的硬化，含量过低将使冶炼成本大量增加。 阳0巧S含量《0. 05%，越少越好，依据炼钢能力及经济性来确定。 阳023]Al含量控制在0. 02%~3. 00%，Al元素具有Si元素的作用，但是含量过高将引 起炼钢、连铸过程的诸多问题，如氧化物夹杂、水口阻塞等。
[0024] 化《0. 50%，一定的化含量可W右移C曲线，降低泽火的临界冷却速度，但含量 过高，泽透性增加，引起泽火后残余奥氏体量的降低甚至消失。
[00巧]Ni《3. 00%，一定的儀含量可W提高钢的综合机械性能，提高奥氏体的稳定性， 含量过高造成成本上升。 阳0%] 化《0. 50%，化元素是很强的奥氏体形成元素，在渗碳体中也不溶解，有利于残 余奥氏体的形成，可提高残余奥氏体的含量，另外可W提高强度，同时提高耐腐蚀性能。
[0027]Mo《1.50%，Mo是一种铁素体形成元素，并降低贝氏体转变起始溫度，同时强烈 延迟奥氏体向铁素体和珠光体的相变，含量过高造成成本上升。 阳02引 V《0. 50 % ,Ti《0. 20 %，Nb《0. 20 %，运立种元素都具有析出强化的作用，但含 量不宜过高。实际需要添加时可W选择一种或两种。
[0029] 采用本发明方法生产的钢板具有强度高、可冷成型的优点，而且有效解决了Q&P 钢工业化生产的工艺路线。
具体实施方式
[0030] 下面通过实施例对本发明作进一步的说明。 阳03U 实施例1 :
[0032] 钢的化学成分如表1所示，连续退火工艺为820°C保溫60秒，W100°C每秒的速度 冷却到200°C保溫60秒后卷取，罩式炉内分配溫度为400°C，分配处理的时间为化，钢板性 能见表2。 阳〇3引实施例2 :
[0034] 钢的化学成分如表1所示，连续退火工艺为880°C保溫80秒，W100°C每秒的速度 冷却到240°C保溫60秒后卷取，罩式炉内分配溫度为350°C，分配处理的时间为化，钢板性 能见表2。 阳03引实施例3 :
[0036] 钢的化学成分如表1所示，连续退火工艺为880°C保溫10秒，W1000°C每秒的速 度冷却到300°C保溫90秒后卷取，罩式炉内分配溫度为200°C，分配处理的时间为50h，钢板 性能见表2。
[0037] 实施例4 :
[0038] 钢的化学成分如表1所示，连续退火工艺为900°C保溫40秒，W200°C每秒的速度 冷却到300°C保溫300秒后卷取，罩式炉内分配溫度为380°C，分配处理的时间为30h，钢板 性能见表2。
[0039] 实施例5 :
[0040] 钢的化学成分如表1所示，连续退火工艺为750°C保溫90秒，W2000°C每秒的速 度冷却到150°C保溫40秒后，酸洗处理，罩式炉内分配溫度为300°C，分配处理的时间为化， 钢板性能见表2。 阳OW 实施例6:
[0042] 钢的化学成分如表1所示，连续退火工艺为850°C保溫180秒，W2000°C每秒的 速度冷却到260°C保溫40秒后，酸洗处理，罩式炉内分配溫度为330°C，分配处理的时间为 12h，钢板性能见表2。 阳0创实施例7 :
[0044] 钢的化学成分如表1所示，连续退火工艺为720°C保溫40秒，W2000°C每秒的速 度冷却到100°C保溫20秒后卷取，罩式炉内分配溫度为150°C，分配处理的时间为10化，退 火后进行酸洗、电锻儀处理，钢板性能见表2。 W45] 实施例8 :
[0046] 钢的化学成分如表1所示，连续退火工艺为920°C保溫30秒，W200°C每秒的速度 冷却到100°C保溫20秒后卷取，罩式炉内分配溫度为300°C，分配处理的时间为20h，退火后 进行酸洗、电锻锋处理，钢板性能见表2。
[0047] 表1本发明实施例钢的化学成分（质量分数）％
W例表2本发明实施例钢的力学性能
Claims (5)
1. 一种冷成型用超高强度钢板的生产方法，包括冶炼、铸造、热乳、冷乳，其特征在于冷 乳钢板在带有快冷处理的连续退火生产线上加热到奥氏体温度后保温一段时间，而后进行 淬火处理，得到M+A为主要组织的钢板，然后在罩式退火炉内进行分配处理；所述钢板的成 分质量百分数为：C0.02%~0.60%，Si0.05%~3. 5%，Μη0.20%~2. 50%，0· 005% 彡Ρ彡 0· 50%，S彡 0· 05%，Α1 0· 60% ~3. 00%，Cr彡0· 50%，Ni彡 3. 00%，Cu彡 0· 50%， Mo彡1. 50%，V彡0. 50%，Ti彡0. 20%，Nb彡0. 20%，余量为Fe和其它不可避免的杂质； 所述连续退火生产线的加热温度为700~900°C，保温时间为：10秒-180秒，淬火冷却速 度在30°C/s~2000°C/s，淬火后钢板的温度控制在室温~400 °C，然后在此温度保温20 秒-300秒，然后缓冷至室温；在所述罩式退火炉内进行分配处理的温度为200~600°C，分 配处理的时间为lOmin~100h。
2. 根据权利要求1所述的冷成型用超高强度钢板的生产方法，其特征在于依据所述钢 板合金元素含量对连续退火处理后的钢板进行酸洗、烘干处理。
3. 根据权利要求1所述的冷成型用超高强度钢板的生产方法，其特征在于对酸洗烘干 后的钢板进行电镀镍、电镀锌或电镀铁处理。
4. 根据权利要求1所述的冷成型用超高强度钢板的生产方法，其特征在于依据所述钢 板合金元素含量对罩式退火炉分配处理后的钢板进行酸洗、烘干处理。
5. -种权利要求1~4中任一权利要求所述方法生产的冷成型用超高强度钢板， 其特征在于所述钢板的成分质量百分数为：C0.02%~0.60%，Si0.05%~3. 5%，Μη 0· 20%~2· 50%，0· 005%彡Ρ彡 0· 50%，S彡 0· 05%，Α1 0· 60%~3. 00%，Cr彡 0· 50%， Ni彡 3. 00%，Cu彡 0· 50%，M〇 彡 1. 50%，V彡 0· 50%，Ti彡 0· 20%，Nb彡 0· 20%，余量为 Fe和其它不可避免的杂质。
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| CN103667884B (zh) * | 2013-12-26 | 2016-06-29 | 北京科技大学 | 1400MPa级低屈强比高延伸率冷轧超高强汽车用钢的制备方法 |
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