CN113316650A - 具有改进机械性质的高强度钢 - Google Patents

具有改进机械性质的高强度钢 Download PDF

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CN113316650A
CN113316650A CN202080009298.6A CN202080009298A CN113316650A CN 113316650 A CN113316650 A CN 113316650A CN 202080009298 A CN202080009298 A CN 202080009298A CN 113316650 A CN113316650 A CN 113316650A
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strip
range
temperature
steel strip
high strength
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CN113316650B (zh
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P·塞达
S·M·C·范伯赫曼
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Tata Steel Ijmuiden BV
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Tata Steel Ijmuiden BV
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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    • B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
    • B21C47/02—Winding-up or coiling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
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    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0442—Flattening; Dressing; Flexing
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
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    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

本发明涉及具有中等量的C、Mn、Si、Cr和Al的高强度钢带材，其中该钢带材具有以体积％计由以下组成的显微组织：铁素体和贝氏体一起50‑90％，马氏体<15％，残余奥氏体5‑15％，余量为珠光体、渗碳体、析出物和夹杂物一起至多5％。

Description

具有改进机械性质的高强度钢
本发明涉及具有改进机械性质的高强度钢。本发明还涉及可生产这样的高强度钢的方法。
广泛的市场需要在提高的强度下延展性的增强。特别是在汽车工业中，其中立法正在驱动燃料经济性和安全性的改进，趋势是朝向更强的可成形的高强度钢。高强度和超高强度带钢为汽车制造商提供降低白车身重量的潜力和抵消由于向电动和混合动力车辆移动而引起的重量增加的机会。另外，高和超高强度钢在决定现代乘用车的耐撞性方面起到关键作用。
在许多情况下，高强度和超高强度钢的大量应用需要可成形性水平高于对于常规的碳-锰钢而言可预期的水平。成形零件中残余延展性的增强有益于碰撞中的完整性。在近些年已经开发了几种高强度钢型号，其中作为第一近似，认为拉伸伸长率是可成形性和冲击完整性两者的简单度量。然而，最近开发先进高强度钢(AHSS)显示了边缘延展性起到同等重要的作用。
随着强度提高，拉伸伸长率和/或边缘延展性(作为扩孔比测量)较低。通常，伸长率和边缘延伸率是相矛盾的性质：当改进伸长率时，边缘延展性较低，反之亦然。AHSS片材的优化可成形性因此是伸长率和边缘延展性之间的折中。这对在压机中由AHSS片材形成复杂汽车零件具有影响，而且对在碰撞中零件的可变形性也具有影响。
在高强度钢片材的开发中，尝试了通过在钢中使用较高量的合金化元素来克服这些问题。还可通过使用高合金(主要是锰)添加以稳定奥氏体来实现可成形性的极端增强。实例是中等锰钢和孪生诱发塑性(TWIP)钢。奥氏体比铁素体内在更有延性并且孪晶可提供非常有效的加工硬化机制。这样的钢可在非常高的强度(典型地1000MPa)下实现非常高的伸长率(典型地30-50％)。然而，屈服强度相对低并且需要均匀地施加大的应变以在成形部件中实现高的强度。此外，极高水平的合金使得大规模生产比常规方法更成问题。
本发明的目的是提供考虑到拉伸伸长率和扩孔比的具有优化性质的高强度钢型号。
本发明的另外的目的是提供具有低屈服强度的高强度钢型号。
本发明的另一目的是提供具有相对少量的合金化元素的高强度钢型号。
根据本发明通过提供由以下元素组成(以重量％计)的高强度钢带材来实现这些目的中的一个或多个：C:0.12-0.18，Mn:2.00-2.60，Si:0.30-0.77，Cr:0.10-0.70，Al:<0.39，S:<0.005，N:<0.015，P:<0.03和任选地选自以下的一种或多种元素：Nb:<0.06，Mo:<0.20，Ti:<0.04，V:<0.20，B:<0.004，Ca:<0.004，余量是铁和不可避免的杂质，其中钢带材具有由以下组成的显微组织(以体积％计)：铁素体和贝氏体一起50-90，马氏体<15，残余奥氏体5-15，余量为珠光体、渗碳体、析出物和夹杂物一起至多5，总和合计100体积％。
发明人发现了通过选择合适的合金化策略和通过在加工过程中调节显微组织特征来实现具有高强度的双相钢的平衡性质。
本发明集中于具有优化的可成形性性质的双相钢。为了获得高扩孔比(HEC值)，显微组织不得不含有大量的贝氏体。使用Si作为合金化元素，形成不含碳的贝氏体，其中过量的碳扩散至奥氏体中并使奥氏体稳定。存在残余奥氏体，因为它利于伸长率并因此在成形过程中改进钢片材的可成形性。残余奥氏体是亚稳定的并在成形过程中转变成马氏体，其改进成形零件的强度。然而，较高贝氏体分数不利于伸长率，并且残余奥氏体不利于扩孔。因此，针对具有高强度和良好可成形性的双相钢设计了具有提高的贝氏体分数(有利于HEC，不利于伸长率)并具有残余奥氏体(有利于伸长率，不利于HEC)的平衡显微组织。马氏体的量相对低以提供高的HEC值，并且存在铁素体用于较低的屈服强度。
优选地，以上根据本发明的钢的显微组织由以下的一种或多种组成(以体积％计)：铁素体15-55％，贝氏体35-75％，马氏体<10％(优选1-5％)，残余奥氏体5-10％，余量为珠光体、渗碳体、析出物和夹杂物一起至多5％，总和合计100体积％。这导致钢的优化的可成形性。
铁素体(15-55％)：需要铁素体用于提供可成形和可加工硬化的基材，并且这对于实现双相特征和较低屈服比是重要的。大于这个限度，最终显微组织将不含有足够的贝氏体和/或马氏体，并因此强度将过低。边缘延展性将不充分。小于这个限度，屈服比将过高。
贝氏体(35-75％)：贝氏体提供强度。在硅的存在下贝氏体的转变将碳驱动至奥氏体相，能使碳水平富集在奥氏体相中，从而允许在环境温度下形成(亚)稳定相；这个过程被称为分配。相对于作为强化相的马氏体，贝氏体也具有优势，因为应变的较小的微观尺度局部化，并因此改进抗断裂性，即它改进边缘延展性。小于下限将存在不充足的奥氏体稳定化并且边缘延展性将过低。超过上限，屈服强度将过高。
马氏体(<15％)：在退火的最终淬火过程中形成马氏体。它也提供强度。大于上限，强度将过高和/或边缘延展性过低。一些马氏体优选存在用于实现DP拉伸响应(用于抑制屈服点伸长率)。优选地马氏体<10％，更优选在1和5％之间。
残余奥氏体(5-15)：残余奥氏体通过TRIP效应增强伸长率。小于5％，将不会实现期望的伸长率水平。上限由组成设定。优选地上限是10％。
由于钢带材的加工所致可在钢中存在少量的珠光体、渗碳体、析出物和夹杂物，一起至多5％。
此外，根据本发明的钢结合相对少量的碳(0.12-0.18重量％)与相对少量的硅(0.30-0.77重量％)。与含有较高量的碳和/或硅的钢型号相比，这有利于钢片材的生产。
以下讨论合金化策略。
碳(0.12-0.18)：需要碳(C)以获得期望的淬透性和强度水平。它能够稳定残余奥氏体。小于这个范围，游离碳的水平可不足以能够稳定期望分数的奥氏体。结果是可能不会实现期望的伸长率水平。大于这个范围，可焊性变成问题。
锰(2.00-2.60)：锰(Mn)提供显著的固溶强化，稳定奥氏体，并增强淬透性，从而促进在常规退火生产线中可实现的冷却速率下硬转变产物的形成。大于这个范围，损害钢带材表面的可润湿性。还考虑到在铸造过程中较强的偏析和在较高值下带材中马氏体带的形成从而给出这个最大水平。Mn含量小于下限时，使强度和转变行为劣化。
硅(0.30-0.77)：硅(Si)添加提供固溶强化因此能够达到高强度和促进奥氏体的稳定。在过时效过程中Si非常有效地阻止碳化物的形成，因此保持碳固溶用于奥氏体的稳定。铁素体和硬质相例如贝氏体和马氏体在不存在碳化物的情况下表现出改进的延展性。可将未捕集在碳化物中的游离碳分配至奥氏体。为了可接受的可涂布性，Si的施加添加应小于0.77重量％的最大水平。Si是铁素体稳定元素并由此确保适当的转变行为从而制备具有相对低的屈服强度的钢产品。与Mn相比，在铸造过程中Si的偏析对边缘延展性而言较少有害。
铬(0.10-0.70)：铬(Cr)可用于提高淬透性因此阻止在冷却至过时效温度时高温转变产物的形成。因此Cr的添加可允许使用在大规模生产线中较容易实现的较低的冷却速率。因为它的淬透性效应，Cr还有效提高强度。在Cr含量小于下限时，转变行为不足以提供期望的强度水平。施加最大水平以确保不形成过多的马氏体和形成足够的贝氏体。
铝(<0.39)：铝(Al)用于在铸造前使钢水脱氧。此外，少量的Al可用于在冷却停滞(arres t)过程中调节转变温度和动力学。高水平的Al可导致铁素体至奥氏体转变温度范围升高至与传统装置不相容的水平。因此，钢中以Al-氧化物和溶质铝的形式的铝的总量必须小于0.39重量％。
硫(S<0.005)：优选避免硫(S),但是在制钢工艺中不可避免地存在硫。较低的硫含量通常对于边缘延展性和可成形性更好。
氮(N<0.015)：氮(N)的含量被限制为最大0.015重量％，如连续铸造设备中典型的。
磷(P<0.03)：在焊接时磷可使钢变脆，所以量被限制为最大0.03重量％。
任选地，可在钢组成中含有以下元素中一种或多种。Nb(<0.06)、Mo(<0.20)、Ti(<0.04)和V(<0.20)。可使用这些元素以细化热轧中间产物和最终产物中的显微组织。细化的显微组织可导致边缘延展性的进一步改进。这些元素还提供强化效应。
硼(B<0.004)：硼(B)可用于优化转变行为和强度。在奥氏体冷却过程中硼抑制铁素体形成。添加硼改进钢的淬透性。
钙(Ca<0.004)：钙(Ca)的添加主要有益于具有较高S含量的钢。钙的添加改变硫化锰夹杂物的形态。当添加钙时夹杂物变成球状而不是细长形状。避免这些细长的夹杂物有益于边缘延展性。Ca处理还防止硬质氧化铝夹杂物的形成。
根据优选实施方案，C的量为0.13-0.18、优选0.14-0.17(以重量％计)和/或Mn的量为2.00-2.50、优选2.10-2.45、更优选2.15-2.40(以重量％计)。
选择C和Mn的范围使得发现了恰当的平衡以提供适当的转变行为和强度水平。Mn和C是奥氏体稳定元素，如以上阐明的。优选的范围与钢中的其它元素一起提供优化的强度和可成形性。
根据另外优选的实施方案，Si+Cr的量≤1.30，优选地Si+Cr≤1.20，更优选地Si+Cr≤1.10，仍更优选地Si+Cr≤1.00，甚至更优选地Si+Cr≤0.90，最优选地Si+Cr≤0.84(以重量％计)。
Si和Cr是稳定铁素体的元素。对于低屈服强度产物需要铁素体形成，然而，过高的铁素体分数降低强度和/或边缘延展性。因此，Si+Cr≤1.3是确保适当转变行为即相之间恰当平衡(没有形成过多的铁素体)的条件。优选地Si+Cr的量甚至更低以增强钢片材的可生产性。
在这方面，优选的是Si的量为0.30-0.70、更优选0.35-0.65、仍更优选0.40-0.60(以重量％计)，和/或其中Cr的量为0.15-0.65、更优选0.20-0.60、仍更优选0.25-0.60(以重量％计)，和/或其中Al的量<0.10、更优选<0.05(以重量％计)。这些优选范围为恰当显微组织的形成和钢的良好可生产性提供优化的条件。
通常考虑到这样元素的成本优选少量的任选元素。在这方面，Nb的优选量<0.04、优选地<0.03、更优选地<0.02(以重量％计)，Ti的优选量<0.03、更优选地<0.020、最优选地<0.01(以重量％计)，B的优选量<0.002、优选地<0.001、最优选地<0.0006(以重量％计)，V的优选量<0.10、优选地<0.05、最优选地<0.02(以重量％计)，和Mo的优选量<0.10、优选地<0.05、最优选地<0.02(以重量％计)。
还预见了Nb、Mo、Ti、V和B中一种或多种作为杂质存在，因为不需要添加这样的元素来达到按照本发明所需的可成形性。
根据本发明的优选实施方案，高强度钢带材具有以下性质中一种或多种：拉伸强度(Rm)在950-1200MPa、优选980-1180MPa的范围内，屈服强度(Rp)在平整轧制之前≤620MPa、优选≤600MPa，总伸长率(AJIS5)>12％，扩孔能力(HEC)>15％。
伸长率和扩孔的这些下限在压机中成形期间，尤其是当组合时，提供钢的非常好的可成形性。
优选地总伸长率(AJIS5)>13％、更优选地>14％、最优选地>15％。高强度钢，尤其是具有至少950MPa的拉伸强度的钢的这种高伸长率水平在与高HEC值和少量的合金化元素组合时是例外。
优选地扩孔能力(HEC)>20％、更优选地>25％、最优选地>30％。这样的高HEC值非常有利于钢的可成形性。
发明人发现了根据本发明的高强度钢带材当如以上限定的机械性质满足以下条件时具有优异的可成形性：(AJIS5×HEC×Rm)/Rp≥550、优选地(AJIS5×HEC×Rm)/Rp≥600、更优选地(AJIS5×HEC×Rm)/Rp≥650、最优选地(AJIS5×HEC×Rm)/Rp≥700。式(AJIS5×HEC×Rm)/Rp有效地结合最重要的机械性质使得应高的性质AJIS5、HEC和Rm与应低的Rp结合。
根据优选实施方案，高强度钢带材涂覆有基于锌的涂层，涂覆的带材具有在平整轧制之后屈服强度Rp≤740MPa、优选地在平整轧制之后Rp≤720MPa、更优选地在平整轧制之后Rp≤700MPa。由于在热浸涂覆浴中用锌涂覆所致，钢的屈服强度变得更高。
本发明根据第二方面涉及生产根据本发明第一方面的高强度钢带材的方法，包括以下步骤：
·铸造具有根据本发明第一方面组成的钢并热轧为具有2.0-4.0mm厚度的带材并在500-650℃范围内的卷绕温度(CT)下卷绕；
·以40-80％的压下量冷轧带材；
·将带材加热至在Ac3-30℃至Ac3+30℃范围内的温度T1以形成完全或部分奥氏体的显微组织，优选使用在5-25℃/s范围内的平均加热速率HR；
·随后将带材保持在T1下持续10-90s的时间段t1，之后使用在2-12℃/s范围内的冷却速率CR1缓慢冷却带材至在570-730℃、优选600-730℃范围内的温度T2；
·然后使用在20-70℃/s范围内的冷却速率CR2将带材快速冷却至在380-470℃、优选400-450℃范围内的温度T3，之后保持带材在T3±50℃之间的温度T4下持续25-100s的时间段t2，其中在时间段t2结束时T4在T3±30℃之间，之后以至少4℃/s的冷却速率CR3冷却钢带材至小于300℃的温度；
·以小于0.5％的压下量平整轧制带材。
发明人发现了通过使用这种方法，可生产具有所需要的显微组织的钢带材。
根据本发明的第三方面，提供生产根据本发明第一方面的高强度钢带材的方法，包括以下步骤：
·铸造具有根据本发明第一方面组成的钢并热轧为具有2.0-4.0mm厚度的带材并在500-650℃范围内的卷绕温度(CT)下卷绕；
·以40-80％的压下量冷轧带材；
·将带材加热至在Ac3-30℃至Ac3+30℃范围内的温度T1以形成完全或部分奥氏体的显微组织，优选使用在5-25℃/s范围内的平均加热速率HR；
·随后将带材保持在T1下持续10-90s的时间段t1，之后使用在2-12℃/s范围内的冷却速率CR1缓慢冷却带材至在570-730℃、优选600-730℃范围内的温度T2；
·然后使用在20-70℃/s范围内的冷却速率CR2将带材快速冷却至在380-470℃、优选400-450℃范围内的温度T3，之后保持带材在T3±50之间的温度T4下持续25-100s的时间段t2，其中在时间段t2结束时T4在T3±30℃之间；
·之后在镀锌浴中热浸涂覆钢带材以提供具有锌涂层或基于锌的涂层的带材，之后以至少4℃/s的冷却速率CR3冷却经涂覆的钢带材至小于300℃的温度；
·以小于0.5％的压下量平整轧制经涂覆的带材。
通过使用按照本发明第三方面的方法，生产镀锌高强度钢片材。基于锌的涂层可例如含有0.7-5％Al和/或0.3-5％Mn。
根据本发明的第四方面，提供生产根据本发明第一方面的高强度钢带材的方法，包括以下步骤：
铸造具有根据权利要求1-13中任一项的组成的钢并热轧为具有2.0-4.0mm厚度的带材并在500-650℃范围内的卷绕温度(CT)下卷绕；
·以40-80％的压下量冷轧带材；
·将带材加热至在Ac3-50℃至Ac3+40℃范围内的温度T1以形成完全或部分奥氏体的显微组织，优选使用在1-25℃/s范围内的平均加热速率HR；
·随后将带材保持在T1下持续至多90s的时间段t1，之后使用在0.5-12℃/s范围内的冷却速率CR1缓慢冷却带材至在570-730℃、优选600-730℃范围内的温度T2；
·然后使用在5-70℃/s范围内的冷却速率CR2将带材快速冷却至在330-470℃、优选400-450℃范围内的温度T3，之后保持带材在T3±50℃之间的温度T4下持续25-100s的时间段t2，其中在时间段t2结束时T4在T3±30℃之间；
·任选地之后在镀锌浴中热浸涂覆钢带材以提供具有锌涂层或基于锌的涂层的带材；
·之后以至少4℃/s的冷却速率冷却经涂覆的钢带材至小于300℃的温度；
·以小于0.5％的压下量平整轧制经涂覆的带材。
发明人发现了通过使用根据本发明第四方面的这种方法能够生产具有所需要的显微组织的钢带材，其中对于温度、时间以及加热和冷却速率设置的要求宽泛。
将参考以下实例阐明本发明。使用如以下表1中给出的组成铸造了九种合金，元素的量以重量％为单位给出。表中未显示的元素作为杂质存在。
表1：钢组成(以重量％计)
I/C 合金 C Mn Si Cr Al S N Si+Cr
I A 0.135 2.210 0.480 0.530 0.032 0.001 0.004 1.010
I B 0.147 2.150 0.554 0.574 0.031 0.001 0.001 1.128
C C 0.145 2.256 0.104 0.549 0.032 0.001 0.006 0.653
I D 0.163 2.381 0.556 0.100 0.034 <0.001 0.003 0.656
I E 0.163 2.378 0.566 0.251 0.032 <0.001 0.003 0.817
I F 0.163 2.177 0.558 0.247 0.043 <0.001 0.004 0.805
I G 0.163 2.206 0.411 0.401 0.208 <0.001 0.003 0.812
I H 0.161 2.209 0.410 0.407 0.209 0.001 0.003 0.817
I I 0.145 2.210 0.516 0.555 0.031 <0.001 0.004 1.071
Figure BDA0003163584480000091
Figure BDA0003163584480000101
在表1中，第一栏I表示按照本发明的合金，然而C表示对比例的合金。
表2中给出合金的相变温度。在表2中提供大于所述温度显微组织完全由奥氏体组成的温度(Ac3)，贝氏体开始(BS)温度和马氏体开始(MS)温度(以℃计)：
表2：相变温度
I/C 合金 A<sub>C3</sub> B<sub>S</sub> M<sub>S</sub>
I A 820 554 380
I B 820 549 375
C C 810 575 385
I D 820 547 370
I E 825 544 375
I F 830 551 375
I G 835 556 380
I H 845 557 375
I I 820 550 375
使用膨胀测定法测量Ac3和MS温度：使用平均加热速率11℃/s加热样品直至900℃。随后将样品保持在900℃下30s。然后淬火样品。使用JmatPro v10.2工具计算BS温度。
生产根据实施例的高强度钢带材的方法如下。
将铸造钢热轧为4.0mm的厚度并在卷绕温度(CT)下卷绕。以75％的压下量冷轧带材。对于机械性质的测定，使用实验室连续退火模拟器退火带材样品。首先以平均加热速率HR加热带材至温度T1使得获得了部分或完全奥氏体的显微组织。随后将带材保持在T1下持续时间段t1。然后以冷却速率CR1将带材冷区至温度T2，之后以冷却速率CR2额外冷却至温度T3。接下来在过时效时间t2期间将带材保持在温度T4下，在这个情况下等于T3。由于发生转变的潜热和由于自然冷却两者，在这个阶段期间温度T4可变化。然后将带材加热至455℃，其代表通常在450-470℃范围内的Zn浴的温度，并保持在这个温度下大约17s以模拟热浸镀锌步骤。然后以至少4℃/s的速率将带材冷却降至小于300℃。在这之后在空气中将带材冷却至室温。
仅在工厂中生产实施例16中的合金I，工厂中方法设置不同于实验室实施例中的那些，并且直接用常规的镀锌涂覆生产的带材。
表3中给出了生产九个样品使用的冷却速率CT、平均加热速率HR和各个温度时间和冷却速率的值。
表3：生产参数
Figure BDA0003163584480000111
如下测定生产的样品的显微组织。
从膨胀测定法数据使用应用于数据的杠杆定律(混合物的线性定律)使用S.M.C.Van Bohemen在Scr.Mater.69(2013)，第315-318页的文章(参考[1])中导出的bcc和fcc晶格的热收缩的非线性方程评价铁素体、贝氏体和马氏体的体积分数。对于在完全奥氏体化之后冷却而言，T1>Ac3，对于fcc晶格而言可通过在参考[1]中提出的表述从而简单描述没有发生转变的高温范围内测量的热收缩。对于在部分奥氏体化之后冷却而言，T1<Ac3，在高温范围内测量的热收缩根据混合物定律由各个相成分的热膨胀系数(CTE)测定。然后通过膨胀测定法数据与由高温范围内的热膨胀限定的这条线的第一偏差来认定在冷却过程中转变的开始。通过X-射线衍射测量测定残余奥氏体(RA)，并且分数RA被用作膨胀数据的杠杆定律分析中的输入。
表4中给出十六种样品的以这种方式测定的铁素体、贝氏体、马氏体和残余奥氏体的体积分数(以体积％计)。
表4：显微组织
I/C 序号 合金 铁素体 贝氏体 马氏体 残余奥氏体
I 1 A 30 57 4 9
I 2 A 22 65 4 9
I 3 A 25 64 3 8
I 4 B 40 50 4 6
I 5 B 38 51 4 7
C 6 C 50 <u>32</u> <u>16</u> 2
C 7 C 29 60 <u>10</u> 1
I 8 D 66 23 1 10
I 9 E 62 24 4 10
I 10 F 22 66 2 10
I 11 F 63 24 4 9
I 12 G 52 37 4 7
I 13 G 70 18 3 9
I 14 H 63 25 4 8
I 15 HJ 75 13 3 9
I 16 I 50 40 5 5
如下测定样品的性质。
使用伺服液压控制测试机按照ISO 6892的方式测定拉伸性质屈服强度(Rp)、拉伸强度(Rm)和总伸长率(AJIS5)。仅对于合金I，实施例16没有使用总伸长率AJIS5而是标准伸长率A80。
使用ISO 16630中描述的测试方法在具有冲孔的样品上进行扩孔测试以测定HEC值，其中定位样品使得冲压边缘上的毛刺存在于远离锥形冲头的上侧。
表5中给出以这种方式测定的十六个样品的性质。
表5：性质
Figure BDA0003163584480000131
以上实例显示使用按照本发明的合金和使用按照本发明的加工步骤，生产样品，其具有所需要的机械性质拉伸强度和屈服强度，和高的总伸长率与HEC值的所需增强组合。
本发明合金和样品还显示使用合理的低的硅和铬的总量，其可小于1.3重量％，可获得具有合适的高性质的高强度钢带材。硅和铬的总量可甚至小于0.85重量％，如通过表1中的合金D至H显示，该合金可导致具有12至19％的总伸长率和19至36％的HEC值的高强度钢型号。
数据的分析揭示本发明实施例的区别可由单一要求获得，即：(AJIS5×HEC×Rm)/Rp≥550。这个表述对于具有上面限定的组成范围和工艺限制的本发明适用。参见实施例7：它具有权利要求内的所有性质(Rp、Rm、AJIS5、HEC)；但是公式显示区别。
可通过这个公式评定钢的总可成形性。这个公式强调实现期望冲压性能所需的优化性质的重要性：对于具有低屈服强度的高强度钢的高伸长率和高HEC。所以，这不仅是优化高伸长率或高扩孔能力，而是两者一起。

Claims (16)

1.高强度钢带材，以重量％计由以下元素组成：
C 0.12-0.18
Mn 2.00-2.60
Si 0.30-0.77
Cr 0.10-0.70
Al<0.39
S<0.005
N<0.015
P<0.03
和任选地选自以下的一种或多种元素：
Nb<0.06
Mo<0.20
Ti<0.04
V<0.20
B<0.004
Ca<0.004
余量为铁和不可避免的杂质，
其中该钢带材具有以体积％计由以下组成的显微组织：
铁素体和贝氏体一起50-90
马氏体<15
残余奥氏体5-15，
余量为珠光体、渗碳体、析出物和夹杂物一起至多5，
总和合计100体积％。
2.根据权利要求1所述的高强度钢带材，其中该钢带材具有以体积％计由以下一种或多种组成的显微组织：
铁素体 15-55
贝氏体 35-75
马氏体<10、优选1-5
残余奥氏体 5-10
余量为珠光体、渗碳体、析出物和夹杂物一起至多5，
总和合计100体积％。
3.根据权利要求1或2所述的高强度钢带材，其中C的量为0.13-0.18、优选0.14-0.17(以重量％计)，和/或其中Mn的量为2.00-2.50、优选2.10-2.45、更优选2.15-2.40(以重量％计)。
4.根据权利要求1、2或3所述的高强度钢带材，其中Si+Cr的量≤1.30，优选Si+Cr≤1.20，更优选Si+Cr≤1.10，仍更优选Si+Cr≤1.00，甚至更优选Si+Cr≤0.90，最优选Si+Cr≤0.84(以重量％计)。
5.根据前述权利要求中任一项所述的高强度钢带材，其中Si的量为0.30-0.70、更优选0.35-0.65、仍更优选0.40-0.60(以重量％计)，和/或其中Cr的量为0.15-0.65、更优选0.20-0.60、仍更优选0.25-0.60(以重量％计)，和/或其中Al的量<0.10、更优选<0.05(以重量％计)。
6.根据前述权利要求中任一项所述的高强度钢带材，其中Nb的量<0.04、优选<0.03、更优选<0.02(以重量％计)，和/或其中Ti的量<0.03、更优选<0.020、最优选<0.01(以重量％计)。
7.根据前述权利要求中任一项所述的高强度钢带材，其中B的量<0.002、优选<0.001、最优选<0.0006(以重量％计)，和/或其中V的量<0.10、优选<0.05、最优选<0.02(以重量％计)，和/或其中Mo的量<0.10、优选<0.05、最优选<0.02(以重量％计)。
8.根据前述权利要求中任一项所述的高强度钢带材，其中Nb、Mo、Ti、V和B中一种或多种作为杂质存在。
9.根据前述权利要求中任一项所述的高强度钢带材，其中该钢带材具有以下性质中的一种或多种：
拉伸强度(Rm)在950-1200MPa、优选980-1180MPa的范围内
屈服强度(Rp)在平整轧制之前≤620MPa、优选≤600MPa
总伸长率(AJIS5)>12％
扩孔能力(HEC)>15％。
10.根据权利要求9所述的高强度钢带材，其中总伸长率(AJIS5)>13％、优选>14％、更优选>15％。
11.根据权利要求9或10所述的高强度钢带材，其中扩孔能力(HEC)>20％、优选>25％、更优选>30％。
12.根据前述权利要求9-11中任一项所述的高强度钢带材，其中适用以下条件：(AJIS5×HEC×Rm)/Rp≥550、优选地(AJIS5×HEC×Rm)/Rp≥600、更优选地(AJIS5×HEC×Rm)/Rp≥650、最优选地(AJIS5×HEC×Rm)/Rp≥700。
13.根据前述权利要求中任一项所述的高强度钢带材，其中该钢带材涂覆有基于锌的涂层，经涂覆的带材具有在平整轧制之后屈服强度Rp≤740MPa、优选地在平整轧制之后Rp≤720MPa、更优选地在平整轧制之后Rp≤700MPa。
14.生产根据前述权利要求1-13中任一项的高强度钢带材的方法，包括以下步骤：
·铸造具有权利要求1-13中任一项的组成的钢并热轧为具有2.0-4.0mm厚度的带材并在500-650℃范围内的卷绕温度(CT)下卷绕；
·以40-80％的压下量冷轧带材；
·将带材加热至在Ac3-30℃至Ac3+30℃范围内的温度T1以形成完全或部分奥氏体的显微组织，优选使用在5-25℃/s范围内的平均加热速率HR；
·随后将带材保持在T1下持续10-90s的时间段t1，之后使用在2-12℃/s范围内的冷却速率CR1缓慢冷却带材至在570-730℃、优选600-730℃范围内的温度T2；
·然后使用在20-70℃/s范围内的冷却速率CR2将带材快速冷却至在380-470℃、优选400-450℃范围内的温度T3，之后保持带材在T3±50℃之间的温度T4下持续25-100s的时间段t2，其中在时间段t2结束时T4在T3±30℃之间，之后以至少4℃/s的冷却速率CR3冷却钢带材至小于300℃的温度；
·以小于0.5％的压下量平整轧制经涂覆的带材。
15.生产根据前述权利要求1-13中任一项的高强度钢带材的方法，包括以下步骤：
·铸造具有根据权利要求1-13中任一项的组成的钢并热轧为具有2.0-4.0mm厚度的带材并在500-650℃范围内的卷绕温度(CT)下卷绕；
·以40-80％的压下量冷轧带材；
·将带材加热至在Ac3-30℃至Ac3+30℃范围内的温度T1以形成完全或部分奥氏体的显微组织，优选使用在5-25℃/s范围内的平均加热速率HR；
·随后将带材保持在T1下持续10-90s的时间段t1，之后使用在2-12℃/s范围内的冷却速率CR1缓慢冷却带材至在570-730℃、优选600-730℃范围内的温度T2；
·然后使用在20-70℃/s范围内的冷却速率CR2将带材快速冷却至在380-470℃、优选400-450℃范围内的温度T3，之后保持带材在T3±50之间的温度T4下持续25-100s的时间段t2，其中在时间段t2结束时T4在T3±30℃之间；
·之后在镀锌浴中热浸涂覆钢带材以提供具有锌涂层或基于锌的涂层的带材，之后以至少4℃/s的冷却速率冷却经涂覆的钢带材至小于300℃的温度；
·以小于0.5％的压下量平整轧制经涂覆的带材。
16.生产根据前述权利要求1-13中任一项的高强度钢带材的方法，包括以下步骤：
·铸造具有根据权利要求1-13中任一项的组成的钢并热轧为具有2.0-4.0mm厚度的带材并在500-650℃范围内的卷绕温度(CT)下卷绕；
·以40-80％的压下量冷轧带材；
·将带材加热至在Ac3-50℃至Ac3+40℃范围内的温度T1以形成完全或部分奥氏体的显微组织，优选使用在1-25℃/s范围内的平均加热速率HR；
·随后将带材保持在T1下持续至多90s的时间段t1，之后使用在0.5-12℃/s范围内的冷却速率CR1缓慢冷却带材至在570-730℃、优选600-730℃范围内的温度T2；
·然后使用在5-70℃/s范围内的冷却速率CR2将带材快速冷却至在330-470℃、优选400-450℃范围内的温度T3，之后保持带材在T3±50℃之间的温度T4下持续25-100s的时间段t2，其中在时间段t2结束时T4在T3±30℃之间；
·任选地之后在镀锌浴中热浸涂覆钢带材以提供具有锌涂层或基于锌的涂层的带材；
·之后以至少4℃/s的冷却速率冷却经涂覆的钢带材至小于300℃的温度；
·以小于0.5％的压下量平整轧制经涂覆的带材。
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