CN105658834A - 用于热成形的钢 - Google Patents

用于热成形的钢 Download PDF

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CN105658834A
CN105658834A CN201480058068.3A CN201480058068A CN105658834A CN 105658834 A CN105658834 A CN 105658834A CN 201480058068 A CN201480058068 A CN 201480058068A CN 105658834 A CN105658834 A CN 105658834A
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steel
tubing
temperature
sheet material
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D.N.汉隆
S·M·C·V·波希门
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Tata Steel Ijmuiden BV
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Priority claimed from EP20130004573 external-priority patent/EP2851440A1/en
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Priority to CN201811022735.9A priority Critical patent/CN109023136A/zh
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Abstract

本发明涉及用于热成形的钢。根据本发明，该用于热成形的钢具有以重量％计的如下组成：C:0.10-0.25,Mn:1.4-2.6,Si:≤0.4,Cr:<1.0,Al:<1.5,P:<0.02,S:<0.005,N:≤0.03,B:<0.0004,O:<0.008和任选地：Ti:<0.3,Mo:<0.5,Nb:<0.3,V:≤0.5,Ca:<0.05,余量为铁和不可避免的杂质。本发明还涉及用这样的钢制备的带材、片材或坯料，用于制备热成形的产品的方法，这样的产品及其用途。

Description

用于热成形的钢
本发明涉及用于热成形的钢。
未涂覆和预涂覆的用于热成形的钢被大量使用，特别是在汽车工业中。在加热至高于Ac3温度的温度(例如介于850℃和950℃之间的温度)、在热成形压机中压制和以高于临界淬火速率的速度淬火之后，这些钢获得高的机械性质(例如高强度)。在加热之前，这些钢具有良好的可成形性和介于300MPa和500MPa之间的拉伸强度，对于大多数级别而言。在热成形工艺之后，这些钢具有非常高的拉伸强度，其可高于1500MPa，并且现在最高达2000MPa。然而，这些产品的延伸率不是非常好，例如约5％的延伸率。高拉伸强度使得热成形的产品特别适合用于汽车车辆的白车身。
热成形通常用于直接的热成形工艺，但是也用于间接的热成形工艺。热成形(或热冲压)的一般描写由A.Naganathan和L.Penter,第7章:HotStamping,inSheetMetalForming-ProcessesandApplications,(T.Altan和A.E.Tekkaya,编辑),ASMInternational,2012给出。
如该出版物所指出的，用于汽车目的，通常使用硼合金化的钢，特别是钢号22MnB5。化学组成在钢供应商之间可不同，但是通常碳的量为约0.22重量％(通常介于0.20重量％和0.25重量％之间)，锰的量为约1.27重量％(通常介于1.00重量％和1.40重量％之间)，硅的量为约0.25重量％(通常介于0.10重量％和0.40重量％之间)，铬的量为约0.15重量％(通常介于0.1重量％和0.50重量％之间)，并且硼的量为约0.0030重量％(通常介于0.0020重量％和0.0040重量％之间)。出于通常的冶金原因，其它元素应为低的，例如硫和磷，并且其它元素可以以少量存在，例如镍、铜、铝、钒和钛。
钢号22MnB5在其用于热成形工艺之前经常被预涂覆。通常使用的预涂层是AlSi涂层。
本发明的目的是优化热成形的产品的机械性质。
本发明的又一目的是提供用于热成形的钢，该钢提供用于热成形的已知钢(例如22MnB5)的替代物。
本发明的另一目的是提供用于热成形的钢，该钢可用于汽车工业而不改变目前使用的设备。
本发明的又一目的是提供用于热成形的钢，该钢使得热成形设备的更有效的使用成为可能。
根据本发明，提供了用于热成形的钢，该钢具有以重量％计的如下组成：
C:0.10-0.25,
Mn:1.4-2.6,
Si:≤0.4,
Cr:≤1.0,
Al:≤1.5,
P:≤0.02,
S:≤0.005,
O:≤0.008,
N:≤0.03,
B:≤0.0004,
和任选地：
Ti:≤0.3,
Mo:≤0.5,
Nb:≤0.3,
V:≤0.5,
Ca:≤0.05,
余量为铁和不可避免的杂质。
发明人发现热成形的产品的机械性质得到优化，因为减少了钢基材中的非金属性成分的数目。非金属性成分降低了基材的均匀性，并且这些不均匀性可导致机械负载的产品的局部应力集中和过早失效。钢中典型的非金属性成分为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和其它需要的化学元素的量来减小所有这些非金属性成分的尺寸和量。
目前通常使用的22MnB5基材组合物包含20至40ppm硼(B)以改进在热成形操作期间的淬透性。为了维持这种元素处于其功能状态，钢制造商向铸件添加钛(Ti)以防止B形成氮化硼(BN)。靠近表面的BN的存在可劣化热浸涂层的品质。通常以与氮(N)的超化学计量比率添加Ti以使添加量的B的效率最大化。还已知硼形成细Fe26(B,C)6复合析出物，其可导致基体中的局部应力集中。因此，发明人从钢组成移除B以限制B基非金属性成分的存在。为了补偿由减少B的量带来的淬透性的损失，发明人添加了锰(Mn)和/或铬(Cr)。
由于Mn与铁基体的相容性，其是有利的金属性组分。此外，添加比常用的22MnB5中更多的Mn降低了钢基材的Ac1和Ac3温度(分别是基材开始转变成奥氏体的温度和基材完全是奥氏体时的温度)。这意味着在热成形之前可利用较低的炉温来将基材奥氏体化。降低炉温是经济上和环境上有利的并且还开拓了对于Zn、Zn合金或Al和Al合金涂层的新工艺机会。对于Zn合金涂层，通常已知增加的炉温降低了热成形的产品的腐蚀性能。对于Al或Al合金涂层，已知高炉温降低部件的可焊接性。能够使用较低炉温的钢组合物因此相对于常用的22MnB5是有利的。
与B相比，Mn确实通过固溶强化来强化基材。此外，Mn添加还降低Ms温度(在冷却时马氏体形成的温度)，这意味着较少的(自)回火((auto-)tempering)将发生并且因此该基材在室温下将具有较高的马氏体强度。由于两种强化机制，发明人宣称他们可降低用于热成形的钢基材中的碳(C)的量并且获得与用22MnB5实现的类似的强度水平。降低C的量对于防止在热成形工艺步骤期间的(自)回火期间的Fe3C形成是有利的。Fe3C析出物可在机械负载期间引入局部不均匀性和应力集中，导致产品的过早失效。此外，由于本发明的钢基材中的较低C含量，热成形的产品的可点焊性将改进。
与Mn类似，Cr提高了淬透性，并且其还降低MS温度。此外，Cr通过固溶强化有助于基材强度。
Si还给出固溶强化贡献。另外，由于Si在碳化物中弱的溶解度，Si阻止(自)回火。
硫(S)是在钢基材中发现的常见元素。钢制造商使用各种脱硫方法来降低S的量，因为其可导致在连铸期间的热脆性。S还可与锰(Mn)一起析出以形成软的MnS夹杂物。在热轧和随后的冷轧期间，这些夹杂物是狭长的并且形成相对大的不均匀性，其可导致过早的失效，特别是在切向方向上负载时。可添加钙(Ca)以球化含S夹杂物和使狭长的夹杂物的量最小化。然而，CaS夹杂物的存在将仍然导致基体中的不均匀性。因此，最好是减少S。
通常以与氧(O)的超化学计量比率将铝(Al)添加至钢，从而通过氧化铝Al2O3的形成降低游离O的可用量来防止在连铸期间的一氧化碳(CO)形成。形成的Al2O3通常形成液体钢顶部上的熔渣，但是在浇铸期间可陷入凝固钢中。在随后的热轧和冷轧期间，该夹杂物将变成分段的并且形成非金属性夹杂物，该非金属性夹杂物导致在对产品进行机械负载时的过早断裂。超化学计量的Al析出物析出为氮化铝(AlN)，该氮化铝还导致钢基体中的局部不均匀性。
优选地，使用了根据权利要求2或3的更有限的量的元素。将清楚的是，权利要求2和3中指定的更有限的量的元素提供了钢，其中进一步降低了钢基材中的非金属性成分的数目。例如，超化学计量量的Ti将形成氮化钛，其已知为硬的不可变形的夹杂物。通过限制Ti和N的量，TiN夹杂物是有限的。权利要求3显示了可以使用其中不添加硼的用于热成形的钢，使得钢中的硼将仅作为不可避免的杂质存在。尽管将作为杂质存在的硼的量将取决于炼铁工艺中使用的原材料并且还取决于炼钢工艺，但是发明人发现目前获得的硼的杂质水平具有0.0001重量％或1ppm的最大值。
优选地，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，该钢的机械性质总是充足的。
如上所述的用于热成形的钢用于制备具有通常尺寸的带材、片材、坯料或管材，例如具有大于100m的长度、介于800和1700mm之间的宽度和介于0.8和4.0mm之间的厚度的热轧并且任选冷轧的带材。将这样的带材切割成片材和坯料或成形为管材。
优选地，该带材、片材、坯料或管材预涂覆有铝或铝基合金的层，或者预涂覆有锌或锌基合金的层。汽车工业优选预涂覆的坯料和管材用于白车身部件。
优选地，该预涂层包含5至13wt％的硅和/或小于5wt％的铁，余量为铝，该预涂层优选具有每侧介于10和40微米之间的厚度，更优选每侧介于20和35微米之间的厚度。这样的厚度提供了对于涂覆有指定的铝合金的热成形的部件的良好腐蚀防护。
更优选地，该预涂层包含8至12wt％的硅和/或2至5wt％的铁，余量为铝。通常使用这样的铝合金预涂层。
根据另一优选的实施方案，该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<0.18wt％和Fe<15wt％，余量为锌和痕量的其它元素，该预涂层优选具有每侧介于5和15微米之间的厚度，更优选每侧介于6和13微米之间的厚度。这种锌预涂层提供良好的腐蚀性质。
根据又一优选的实施方案，该预涂层包含0.5至4wt％的Al和0.5至3.2wt％的Mg，余量为锌和痕量的其它元素，该涂覆层优选具有每侧介于5和15微米之间的厚度，更优选每侧介于6和13微米之间的厚度。这种预涂层提供了甚至更好的腐蚀性质。
根据本发明，另外提供了使用如上所述的带材、片材、坯料或管材制备热成形的产品的方法，其使用以下步骤：
-例如通过切割带材或片材来提供坯料，或者提供管材
-将该坯料或管材加热至高于钢的Ac1温度、优选高于钢的Ac3温度到至多1000℃的温度的温度
-将加热的坯料或管材运送到热成形压机中
-在压机中将坯料或管材成形为产品
-以高于临界淬火速率(CQR)的平均冷却速率在炉温和Ms温度之间将产品淬火。
CQR定义为用于获得所需的机械性质(Rm>1300MPa)的冷却速率，并且该冷却速率低于临界冷却速率(CCR)，该临界冷却速率是形成100％马氏体的最小冷却速率。
使用这种方法，制备了具有对于汽车用途所需要的机械性质的热成形产品，该产品是未涂覆的或者涂覆的，这取决于所使用的坯料。如上所阐明的，与常用的22MnB5型钢相比，根据本发明的组合物的Ac1和Ac3温度更低。
优选将坯料或管材至少部分加热至高于Ac1温度、优选高于Ac3温度但低于950℃、优选低于900℃的温度。如上所讨论的，由于根据本发明的组合物的Ac1和Ac3温度较低，优选甚至可以使用低于900℃的加热温度。
根据优选的实施方案，在将加热的坯料放到热成形压机中之前将其强制冷却。这样的冷却积极地影响所成形的产品的性质。
本发明还包括使用如上所述的方法制备的产品。这种产品具有通过热成形方法提供的机械性质，如对于汽车或其它用途所需要的。
优选地，如上所述的产品用于机动车辆。出于这种目的，还必须考虑除了机械性质以外的其它性质，例如产品的可焊接性。
将参考以下的实施例阐明本发明。
发明人将多种组合物浇铸成25kg锭子。随后采用900℃的终点温度、630℃的卷绕温度和4mm的热轧规格对这些锭子进行热轧。随后将带材酸洗和冷轧至1.5mm规格。使用膨胀测定法确定了组合物的依赖于组成的Ac3温度、Ms温度和临界冷却速率(CCR)。对于这些测试，在Bahr805A膨胀测定仪中加热样品至900℃的温度，其中从室温到650℃平均加热速率为15℃/s，并且从650-900℃平均加热速率为3℃/s。在900℃下保温3分钟后，以各种冷却速率将样品淬火。在表1中给出了对于各种化学组成获得的数据。
表1
采用通常的测量设备，不能比表1中显示的更精确地测量Ti和B的量。该表显示Ti的量足够低。没有测量O的量，但是已知对于这样的钢类型，在实验室样品中该量小于50ppm。显示在这些钢类型的商业大规模生产期间制备的钢包含小于30ppm的O。
当没有向该钢添加硼时，在实验室条件下制备的其它测试样品显示包含1至3ppm的B。可通过炼钢设备被先前制备的含硼的钢的小污染来解释硼的量的这种变化。没有向其中添加硼的这样的类型的钢的商业大规模生产包含小于2ppm硼的量；通常测得了小于1ppm硼的量。
为了证实非金属性成分的不存在对机械性质的有益影响，发明人进行了热成形试验。采用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秒内运送到压机并且在约780℃的温度下在平坦工具之间进行压制。平坦压制工具具有介于20和80℃之间的温度并且在约20秒期间关闭压机。在刚关闭压机之后，压机中坯料的冷却速率介于50和100℃/s之间。坯料在离开炉后直到达到马氏体起始温度的平均冷却速率高于基材的临界淬火速率，如从表2中的所得机械性质可见的。这些结果还证实了：虽然本发明的基材的碳水平较低，但是屈服强度(Rp)和拉伸强度(Rm)类似于常用的22MnB5。然而，由于减少数目的非金属性成分，本发明的基材均具有比常用的22MnB5更高的总延伸率。
表2
铸件： 炉 运送 Rp Rm Ag A
[序号] [℃] [s] [MPa] [MPa] [％] [％]
6A 2.0Mn 900 8 1126 1536 4.0 6.9
6B 2.2Mn 900 8 1109 1551 3.9 7.1
7A 2.0Mn- 900 8 1111 1519 3.7 6.3
7B 2.0Mn- 900 8 1119 1544 4.1 7.3
8A 1.8Mn- 900 8 1133 1525 3.8 6.6
8B 2.2Mn- 900 8 1137 1550 4.1 7.0
9A 1.6Mn- 900 8 1158 1554 3.8 6.5
9B 1.8Mn- 900 8 1147 1566 3.7 6.4
1A 22MnB5- 900 8 1137 1555 3.7 6.0

Claims (15)

1.用于热成形的钢，该钢具有以重量％计的如下组成：
C:0.10-0.25,
Mn:1.4-2.6,
Si:≤0.4,
Cr:≤1.0,
Al:≤1.5,
P:≤0.02,
S:≤0.005,
N:≤0.03,
B:≤0.0004,
O:≤0.008,
和任选地：
Ti:≤0.3,
Mo:≤0.5,
Nb:≤0.3,
V:≤0.5,
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:0.12-0.23和/或
Mn:1.6-2.5和/或
Si:≤0.3和/或
Cr:≤0.8和/或
Al:≤0.5,并且优选Al≤0.1
O:≤0.005和/或
N:≤0.01和/或
B:≤0.0003,并且优选B≤0.0002和/或
Ti:≤0.1和/或
Mo:≤0.2和/或
Nb:≤0.1和/或
V:≤0.2和/或
Ca:≤0.01。
3.根据权利要求1或2的钢，其中：
C:0.15-0.21和/或
Mn:1.8-2.4和/或
Si:≤0.2和/或
Cr:≤0.7,优选Cr0.2－0.7和/或
Al:≤0.05和/或
N:≤0.006和/或
Ti:≤0.02和/或
Mo:≤0.08和/或
Nb:≤0.02和/或
V:≤0.02和/或
B:≤0.0001,并且优选B≤0.00009。
4.根据权利要求1、2或3的钢，其中Mn+Cr≥2.5重量％，优选Mn+Cr≥2.6重量％。
5.采用根据前述权利要求任一项的钢制备的带材、片材、坯料或管材。
6.根据权利要求5的带材、片材、坯料或管材，预涂覆有铝或铝基合金的层，或预涂覆有锌或锌基合金的层。
7.根据权利要求6的带材、片材、坯料或管材，其中预涂层包含5至13wt％的硅和/或小于5wt％的铁，余量为铝，该预涂层优选具有每侧介于10和40微米之间的厚度，更优选每侧介于20和35微米之间的厚度。
8.根据权利要求7的带材、片材、坯料或管材，其中该预涂层包含8至12wt％的硅和/或2至5wt％的铁，余量为铝。
9.根据权利要求6的带材、片材、坯料或管材，其中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<0.18wt％和Fe<15wt％，余量为锌和痕量的其它元素，该预涂层优选具有每侧介于5和15微米之间的厚度，更优选每侧介于6和13微米之间的厚度。
10.根据权利要求6的带材、片材、坯料或管材，其中预涂层包含0.5至4wt％的Al和0.5至3.2wt％的Mg，余量为锌和痕量的其它元素，该预涂层优选具有每侧介于5和15微米之间的厚度，更优选每侧介于6和13微米之间的厚度。
11.使用根据权利要求6-10中任一项的带材、片材、坯料或管材制备热成形的产品的方法，其使用以下步骤：
-例如通过切割带材或片材来提供坯料，或者提供管材
-将该坯料或管材加热至高于钢的Ac1温度、优选高于钢的Ac3温度到至多1000℃的温度的温度
-将加热的坯料或管材运送到热成形压机中
-在压机中将坯料或管材成形为产品
-以高于临界淬火速率(CQR)的平均冷却速率在炉温和Ms温度之间将产品淬火。
12.根据权利要求11的方法，其中将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的方法，其中在将加热的坯料或管材放到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中任一项的方法制备的产品。
15.根据权利要求14的产品在机动车辆中的用途。
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