CN107429364A - 用于热成形的钢 - Google Patents

用于热成形的钢 Download PDF

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CN107429364A
CN107429364A CN201680015376.7A CN201680015376A CN107429364A CN 107429364 A CN107429364 A CN 107429364A CN 201680015376 A CN201680015376 A CN 201680015376A CN 107429364 A CN107429364 A CN 107429364A
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weight
tubing
steel
temperature
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D·N·汉隆
G·C·汉森
S·M·C·范波希门
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Tata Steel Ijmuiden BV
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Abstract

本发明涉及一种热成形钢。根据本发明，用于热成形的钢具有以下组成(重量％)：C：0.12‑0.24，Mn：1.60‑2.50，Si：≤0.195，Cr：≤0.9，Al：≤1.3，P：≤0.02，S：≤0.005，N：≤0.03，B：≤0.0004，O：≤0.008，任选的Ti：≤0.2，Mo：≤0.2，Nb：≤0.2，V：≤0.2，Ca：≤0.05，余量为铁和不可避免的杂质。本发明还涉及一种用这种钢制造的带材，片材或坯料，这种产品的制造方法及其用途。

Description

用于热成形的钢
本发明涉及一种用于热成形的钢。
广泛使用用于热成形的钢(未涂覆和预涂覆的)，特别是在汽车行业。在加热到高于Ac3温度的温度(例如850℃至950℃之间的温度)，在热成形压机中压制并以高于临界淬火速率的淬火速度淬火之后，这些钢获得高机械性能(例如高强度)。在加热之前，对于大多数钢种，这些钢具有良好的成形性和300MPa至500MPa的拉伸强度。在热成形工艺后，这些钢具有非常高的拉伸强度，其可以高于1500MPa，现在高达2000MPa或甚至高于该强度。然而，这些产品的延伸率不是很好，例如延伸率为约5％。高拉伸强度使得热成形产品特别适用于汽车的白车身。
热成形通常用于直接热成形工艺，但也用于间接热成形工艺。热成形(或热冲压)的大致状况由A.Naganathan和L.Penter的Chapter 7:Hot Stamping,in Sheet MetalForming-Processes and Applications,(T.Altan和A.E.Tekkaya编辑),ASMInternational,2012给出。
如该出版物所述，对于汽车用途，常用硼合金钢，特别是钢种22MnB5。钢铁供应商之间的化学组成可能不同，但通常碳的量为约0.22重量％(通常0.20-0.25重量％)，锰的量为约1.27重量％(通常1.00-1.40重量％)，硅的量为约0.25重量％(通常0.10-0.40重量％)，铬的量为约0.15重量％(通常为0.1-0.50重量％)，硼的量为约0.0030重量％(通常0.0020-0.0040重量％)。由于一般的冶金学原因，其它元素应该是低量的，例如硫和磷，其它元素可以少量存在，例如镍、铜、铝、钒和钛。
经常在热成形工艺中使用钢种22MnB5前将其进行预涂覆。常用的预涂层是AlSi涂层。
本发明的目的是优化热成形产品的机械性能。
本发明的另一个目的是提供一种用于热成形的钢，其提供用于热成形的已知钢例如22MnB5的替代。
本发明的另一个目的是提供一种用于热成形的钢，其可以由汽车工业使用，而不改变目前使用的设备。
本发明的另一个目的是提供一种用于热成形的钢，其能够更有效地使用热成形设备。
根据本发明，提供了一种用于热成形的钢，其以重量百分比计具有如下组成：
C：0.12-0.24，
Mn：1.60-2.50，
Si：≤0.195，
Cr：≤0.9，
Al：≤1.3，
P：≤0.02，
S：≤0.005，
N：≤0.03，
B：≤0.0004，
O：≤0.008
并且可选地：
Ti：≤0.2，
Mo：≤0.2，
Nb：≤0.2，
V：≤0.2，
Ca：≤0.05，
其余为铁和不可避免的杂质。
本发明人已经发现，由于钢基材中非金属成分的数量减少，所以热成形产品的机械性能得到优化。非金属成分降低了基材的均匀性，而这些不均匀性可导致局部应力集中和机械负载产品的过早失效。钢中的典型非金属成分是TiN、BN、Fe26(B、C)6、MnS、AlN、CaS、Al2O3、P、Fe3C等。本发明的钢组合物旨在通过减少B、Ti、S、Ca、Al、P和其他所需化学元素的量来减少所有这些非金属成分的尺寸和量。
现在常用的22MnB5基材组合物含有20-40ppm的硼(B)，以改善热成形操作中的淬透性。为了使该元件保持其功能状态，钢厂向铸件中添加钛(Ti)以防止B形成氮化硼(BN)。在表面附近存在BN可劣化通常存在的热浸镀层的品质。通常以与氮(N)的过化学计量比比例加入Ti以使添加量B的效率最大化。还已知硼还形成细的Fe26(B，C)6复杂析出物，其可导致在基体中的局部应力集中。因此，本发明人从钢组合物中减少B以限制B基非金属成分的存在。因此，B的存在量低于0.0004重量％或4ppm。为了通过减少B的量来补偿淬透性的损失，本发明人添加了锰(Mn)和/或铬(Cr)。
由于Mn与铁基体的相容性，Mn是有利的金属成分。此外，添加比常用的22MnB5更多量的Mn减少了钢基材的Aci和Ac3温度(分别为基材开始转变为奥氏体的温度和其为完全奥氏体时的温度)。这意味着在热成形之前可以利用较低的炉温来对基材进行奥氏体化。降低炉温是经济的和环境有利的，也为Zn、Zn合金或Al和Al合金涂层开辟了新的工艺机会。对于Zn合金涂层，通常已知的是，升高的炉温降低了热成形产品的腐蚀性能。对于Al或Al合金涂层，已知高炉温降低了部件的可焊性。因此，使较低炉温的使用成为可能的钢组合物比常用的22MnB5有利。因此，Mn的存在量为1.6-2.5重量％。
与B相反，Mn通过固溶强化来强化基材。此外，Mn添加量也降低了Ms温度(在冷却时形成马氏体的温度)，这意味着会发生较少的(自动)回火，因此基材在室温下将具有较高的马氏体强度。由于这两种强化机理，本发明人声称它们可以减少用于热成形的钢基材中的碳(C)的量，并且获得的强度水平与用22MnB5实现的相似。减少C量有利于在热成形工艺步骤期间在(自动)回火期间防止Fe3C的形成。Fe3C析出物在机械加载时可引起局部不均匀性和应力集中，导致产品过早失效。此外，由于本发明钢基材中较低的C含量，将改善热成形产品的点焊性。因此，C的存在量为0.12-0.24重量％。
与Mn类似，Cr增加了淬透性，同时降低了Ms温度。此外，Cr通过固溶强化来促进基材的强度。Cr的存在量小于0.9重量％。
Si还提供了固溶强化贡献。此外，由于Si在碳化物中的弱溶解性，因此Si阻碍(自动)回火。Si的存在量为最多0.195重量％。较高的量会对表面品质和轧制能力产生负面影响。
硫(S)是钢基材中常见的元素。钢厂使用各种脱硫方法减少S的量，因为它可导致连铸期间的热短路。S也可以与锰(Mn)析出以形成软MnS夹杂物。在热轧和随后的冷轧期间，这些夹杂物被拉长的，并且形成相对较大的不均匀性，这可导致过早的失效，特别是当在切线方向加载时。可以加入钙(Ca)以使含S的夹杂物球化，并使细长夹杂物的量最小化。然而，CaS夹杂物的存在仍将会导致基体中的不均匀性。因此，最好减少S。S不应该以高于0.005重量％的量存在。Ca的存在量应小于0.05重量％。
铝(Al)通常以与氧(O)过化学计量比的比例加入到钢中，以通过形成氧化铝Al2O3减少游离O的可用量来防止在连铸期间一氧化碳(CO)的形成。形成的Al2O3通常在液态钢的顶部形成渣料，但在铸造期间可夹带在凝固钢中。在随后的热和冷轧期间，这种夹杂物将变为分段的，并形成非金属夹杂物，其导致机械加载该产品时的过早失效。过化学计量比的Al以氮化铝(AlN)形式析出，这也导致钢基体中的局部不均匀性。因此，Al的存在量应小于1.3重量％。
氮(N)和氧(O)也应以低含量存在，因为这些元素与其他元素形成夹杂物。在钢中应存在小于0.02重量％的P且小于0.008重量％的O。
一些元素可以任选地存在于钢中。由于不需要形成TiN氮化物(因为B不必再是游离元素)，因此Ti可以以低于0.2重量％的量存在，并且可根本不添加Ti。Mo、Nb和V也是如此。
对于上述元素，实践中，Si、Cr和Al的下限为0.001重量％，且通常Si和Cr的下限为0.01重量％，对Al为0.005重量％。对于S、N和P，下限为1ppm(0.0001重量％)，且实践中下限通常为0.001重量％。
优选地，使用根据权利要求2或3的更受限量的元素。显然，如权利要求2和3所述的更受限量的元素提供了其中钢基材中的非金属成分的数量进一步减少的钢。例如，过化学计量的Ti将形成钛氮化物，其被称为硬的、不可变形的夹杂物。通过限制Ti和N的量，限制了TiN夹杂物。
权利要求书显示，可以使用其中不加硼的用于热成形的钢，使得钢中的硼仅作为不可避免的杂质存在。尽管将会作为杂质存在的硼的量将取决于在炼铁期间使用的原料，并且还取决于炼钢工艺，但本发明人已经发现，现在获得的硼的杂质水平通常具有0.0001重量％或1ppm的最大值。
优选Mn和Cr的量使得Mn+Cr≥2.5重量％，优选Mn+Cr≥2.6重量％。对于这些量，钢的机械性能总是足够的。
将如上所述的用于热成形的钢用来制造具有通常尺寸的带材、板材、坯料或管材，例如长度大于100m，宽度为800-1700mm，厚度为0.8-4.0mm的热轧和任选冷轧的带材。将这种带材切割成片材和坯料或成形为管材。
优选地，带材、片材、坯料或管材预涂覆有铝或铝基合金层，或预涂覆有锌或锌基合金层。汽车工业中优选预涂覆的坯料和管材用于白车身部件。
优选地，预涂层包含5至13重量％的硅和/或小于5重量％的铁，余量为铝，预涂层优选具有每侧10至40微米，更优选每侧20至35微米的厚度。这种厚度为涂覆有特定铝合金的热成形部件提供了良好的腐蚀防护。
更优选地，预涂层包含8至12重量％的硅和/或2至5重量％的铁，余量为铝。常用这种铝合金预涂层。
根据另一个优选实施方案，预涂层是通过热处理锌层获得的铁-锌扩散涂层，该锌层包含Al<0.18重量％和Fe<15重量％，余量是锌和痕量的其它元素，预涂层优选具有每侧5至15微米的厚度，更优选每侧6至13微米的厚度。这种锌预涂层提供了良好的腐蚀性能。
根据另外的优选实施方案，预涂层包含0.5至4重量％的Al和0.5至3.2重量％的Mg，余量为锌和痕量的其它元素，涂层优选具有每侧5至15微米的厚度，更优选每侧6至13微米的厚度。该预涂层提供甚至更好的腐蚀性能。
根据本发明，还提供了一种使用以下步骤，使用如上所述的带材、片材、坯料或管材制造热成形产品的方法：
-提供坯料，例如通过切割带材或片材或管材
-将坯料或管材加热到高于钢的Ac1温度，优选高于钢的Ac3温度的温度，至最高1000℃的温度
-将加热的坯料或管材输送到热成形压机中
-在压机中将坯料或管材成形为产品
-在炉温和Ms温度之间以高于临界淬火速率(CQR)的平均冷却速率将该产品淬火。
定义CQR为获得所需机械性能(Rm>1300MPa)的冷却速率，其低于作为形成100％马氏体的最小冷却速率的临界冷却速率(CCR)。
使用该方法制造了具有汽车用途所需的机械性能的热成形产品，取决于所使用的坯料，该产品是未涂覆的或涂覆的。如上所述，与常用的22MnB5型钢相比，对于根据本发明的组合物，Ac1和Ac3温度较低。
优选地，至少部分将坯料或管材加热至高于Ac1温度的温度，优选高于Ac3温度，但低于950℃，优选低于900℃。由于根据本发明的组合物的Ac1和Ac3温度较低，如上所述，优选甚至可使用低于900℃的加热温度。
根据优选实施方案，在将加热的坯料放入热成形压机之前，将其强制冷却。这种冷却有利地影响成形产品的性能。
本发明还包括使用上述方法制备的产品。该产品具有如汽车或其他用途所需的由热成形方法提供的机械性能。
优选地，将如上所述的产品用于机动车辆中。对于这个目的，除了机械性能之外，还必须考虑其它性能，例如产品的可焊性。
将参考以下实施例阐述本发明。
发明人将多种组合物铸造成25kg的锭。随后以900℃的最终温度，630℃的卷取温度和4mm的热轧规格(gauge)热轧这些锭。随后将带材酸洗并冷轧至1.5mm规格。使用膨胀计测定组合物的组成依赖性Ac3温度，Ms温度和临界冷却速率(CCR)。对于这些试验，将样品在Bahr805A膨胀计中加热至900℃的温度，其中以15℃/s的平均加热速率从室温升至650℃且以3℃/s的平均加热速率从650至900℃。在900℃下均热3分钟后，将样品淬火。在表1中对于各种化学组成给出了获得的数据。
表1
对于通常的测量设备，不能比表1中所示的更精确测量Ti和B的量。该表显示Ti的量足够低。未测量O的量，但是已知对于这种钢类型，在实验室样品中的量小于50ppm。已显示在这些钢类型的商业全规模制造期间制造的钢含有少于30ppm的O.
在钢中未加入硼时，在实验室条件下制造的其他试验样品显示含有1-3ppm的B。可以通过对先前制造的含硼钢的炼钢设备的小的污染来解释硼的量的这种变化。这种没有添加硼的钢类型的商业全规模制造含有少于2ppm的硼；通常测得少于1ppm硼的量。
为了证明不存在非金属成分对机械性能的有益影响的效果，发明人进行了热成形试验。以5分钟的总炉时间将1.5mm规格的钢坯料加热至900℃。将坯料从炉中取出，在10秒内输送到压机中，并在约780℃的温度下在平型工具(flat tool)之间压制。平型压制工具的温度为20-80℃，且将压机关闭约20秒。在关闭压机后，压机中的坯料的冷却速度为50-100℃/s。如从表2中的所得机械性能可以看出，离开炉后直到达到马氏体开始温度，坯料的平均冷却速率高于基材的临界淬火速率。这些结果也表明，即使本发明的基材的碳水平较低，屈服强度(RP)和拉伸强度(Rm)也与常用的22MnB5相似。然而，由于非金属成分减少的数量，本发明的基材77A和77B与常用的22MnB5相比具有更高的总延伸率。
表2
铸造: 组成ID 炉温 运输时间 Rp Rm Ag A
[No.] [℃] [s] [MPa] [MPa] [％] l％]
77A 0.07Si 900 8 1168 1566 3.5 6.2
77B 0.19Si 900 8 1181 1573 3.8 6.7
80 0.06Si 900 8 1096 1508 3.5 6.0
1A 22MnB5-Lab 900 8 1137 1555 3.7 6.0

Claims (15)

1.用于热成形的钢，以重量％计具有以下组成：
C:0.12-0.24,
Mn:1.60-2.50,
Si:≤0.195,
Cr:≤0.9,
Al:≤1.3,
P:≤0.02,
S:≤0.005,
N:≤0.03,
B:≤0.0004,
O:≤0.008
和任选的:
Ti:≤0.2,
Mo:≤0.2,
Nb:≤0.2,
V:≤0.2,
Ca:≤0.05,
余量为铁和不可避免的杂质。
2.根据权利要求1的钢，其中：
C:0.15-0.23和/或
Mn:1.70-2.40和/或
Si:≤0.19和/或
Cr:0.15-0.80和/或
Al:≤1.0和/或
P:<0.02和/或
S:≤0.005和/或
N:≤0.01和/或
B:≤0.0004和/或
O:≤0.008和/或
和任选的:
Ti:≤0.1和/或
Mo:≤0.1和/或
Nb:≤0.1和/或
V:<0.1和/或
Ca:≤0.01
余量为铁和不可避免的杂质。
3.根据权利要求1的钢，其中：
C:0.17-0.22和/或
Mn:2.00-2.30和/或
Si:0.02-0.10和/或
Cr:0.30-0.70和/或
Al:<0.10和/或
P:<0.015和/或
S:<0.003和/或
N:<0.006和/或
B:<0.0003和/或
O:≤0.008和/或
和任选的:
Ti:<0.05和/或
Mo:<0.05和/或
Nb:<0.05和/或
V:<0.05和/或
Ca:0.01-0.050
余量为铁和不可避免的杂质。
4.根据权利要求1的钢，其中：
C:0.19-0.22和/或
Mn:2.00-2.25和/或
Si:0.03-0.08和/或
Cr:0.60-0.70和/或
Al:0.015-0.055和/或
P:<0.015和/或
S:<0.003和/或
N:<0.006和/或
B:<0.0003和/或
O:≤0.008和/或
和任选的:
Ti:<0.01和/或
Mo:<0.015和/或
Nb:<0.005和/或
V:<0.01和/或
Ca:0.013-0.050
余量为铁和不可避免的杂质。
5.用根据前述权利要求中任一项所述的钢制造的带材、片材，坯料或管材。
6.根据权利要求5所述的带材、片材、坯料或管材，其预涂有铝或铝基合金层，或预涂覆有锌或锌基合金层。
7.根据权利要求6所述的带材、片材、坯料或管材，其中所述预涂层包含5至13重量％的硅和/或少于5重量％的铁，余量为铝，所述预涂层优选具有每侧10-40微米，更优选每侧20至35微米的厚度。
8.根据权利要求7所述的带材、片材、坯料或管材，其中所述预涂层包含8至12重量％的硅和/或2至5重量％的铁，余量为铝。
9.根据权利要求6所述的带材、片材、坯料或管材，其中所述预涂层是通过热处理锌层获得的铁-锌扩散涂层，该锌层包含Al<0.18重量％和Fe<15重量％，余量是锌和痕量的其它元素，所述预涂层优选具有每侧5至15微米的厚度，更优选每侧6至13微米的厚度。
10.根据权利要求6所述的带材、片材、坯料或管材，其中所述预涂层包含0.5至4重量％的Al和0.5至3.2重量％的Mg，余量为锌和痕量的其它元素，所述预涂层优选具有每侧5至15微米的厚度，更优选每侧6至13微米的厚度。
11.使用根据权利要求6至10中任一项所述的带材、片材、坯料或管材，使用以下步骤制造热成形产品的方法：
-提供坯料，例如通过切割带材或片材或管材
-将坯料或管材加热到高于钢的Ac1温度，优选高于钢的Ac3温度的温度，至最高1000℃的温度
-将加热的坯料或管材输送到热成形压机中
-在压机中将坯料或管材成形成产品
-在炉温和Ms温度之间以高于临界淬火速率(CQR)的平均冷却速率将该产品淬火。
12.根据权利要求11所述的方法，其中将所述坯料或管材至少部分加热至高于Ac1，优选高于Ac3但低于950℃，优选低于900℃的温度。
13.根据权利要求11或12所述的方法，其中在将加热的坯料或管材放入热成形压机中之前将其强制冷却。
14.使用根据权利要求11-13中任一项所述的方法制造的产品。
15.根据权利要求14的产品在机动车辆中的用途。
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