CN111492078A - 经冷轧和热处理的钢板、其生产方法和这样的钢用于生产车辆部件的用途 - Google Patents
经冷轧和热处理的钢板、其生产方法和这样的钢用于生产车辆部件的用途 Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 52
- 239000010959 steel Substances 0.000 title claims abstract description 52
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 8
- 238000000034 method Methods 0.000 title claims description 14
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 35
- 239000011572 manganese Substances 0.000 claims abstract description 22
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 20
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 17
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 15
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 15
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 14
- 150000001247 metal acetylides Chemical class 0.000 claims abstract description 14
- 229910052742 iron Inorganic materials 0.000 claims abstract description 12
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 10
- 239000000203 mixture Substances 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 239000010703 silicon Substances 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 239000010955 niobium Substances 0.000 claims abstract description 6
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 6
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- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 5
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- 239000010936 titanium Substances 0.000 claims abstract description 5
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- 229910052796 boron Inorganic materials 0.000 claims abstract description 3
- 229910052802 copper Inorganic materials 0.000 claims abstract description 3
- 239000010949 copper Substances 0.000 claims abstract description 3
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- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 3
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- 239000012535 impurity Substances 0.000 claims abstract 2
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- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 10
- 238000005096 rolling process Methods 0.000 claims description 10
- 239000010960 cold rolled steel Substances 0.000 claims description 8
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 7
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- JZLMRQMUNCKZTP-UHFFFAOYSA-N molybdenum tantalum Chemical compound [Mo].[Ta] JZLMRQMUNCKZTP-UHFFFAOYSA-N 0.000 claims 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 abstract description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract description 2
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 2
- 239000011733 molybdenum Substances 0.000 abstract description 2
- 229910052715 tantalum Inorganic materials 0.000 abstract description 2
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 abstract description 2
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- 230000015572 biosynthetic process Effects 0.000 description 4
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- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
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- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 2
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- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical compound [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- KCZFLPPCFOHPNI-UHFFFAOYSA-N alumane;iron Chemical compound [AlH3].[Fe] KCZFLPPCFOHPNI-UHFFFAOYSA-N 0.000 description 1
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- ZMIGMASIKSOYAM-UHFFFAOYSA-N cerium Chemical compound [Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce] ZMIGMASIKSOYAM-UHFFFAOYSA-N 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C21—METALLURGY OF IRON
- 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
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- 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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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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Abstract
本发明涉及经冷轧和热处理的钢板,以重量%表示,其组成包含以下元素:0.1%≤碳≤0.6%,4%≤锰≤20%,5%≤铝≤15%,0%≤硅≤2%,铝+硅+镍≥6.5%,并且可能包含以下任选元素中的一者或更多者:0.01%≤铌≤0.3%,0.01≤钛≤0.2%,0.01%≤钒≤0.6%,0.01%≤铜≤2.0%,0.01%≤镍≤2.0%,铈≤0.1%,硼≤0.01%,镁≤0.05%,锆≤0.05%,钼≤2.0%,钽≤2.0%,钨≤2.0%,剩余部分由铁和通过加工引起的不可避免的杂质构成,其中所述钢板的显微组织以面积分数计包含10%至50%的奥氏体,所述奥氏体相任选地包含晶内κ碳化物,剩余部分为规则铁素体和D03结构的有序铁素体(Fe,Mn,X)3Al,任选地包含最高达2%的晶内κ碳化物(Fe,Mn,)3AlCx,所述钢板呈现出高于或等于900MPa的极限抗拉强度。本发明还涉及制造方法和这样的等级用于制造车辆部件的用途。
Description
本发明涉及低密度钢及其制造方法,所述低密度钢具有大于或等于900MPa的抗拉强度和大于或等于9%的均匀延伸率,适用于汽车行业。
环境限制迫使汽车制造商不断减少其车辆的CO2排放。为此,汽车制造商有几种选择,其中他们的主要选择是减轻车辆的重量或改善其发动机***的效率。经常通过这两种方法的组合实现进步。本发明涉及第一种选择,即减轻机动车辆的重量。在这个非常特定的领域,存在双路线替代方案:
第一路线包括在提高钢的机械强度水平的同时减小钢的厚度。遗憾的是,该解决方案由于某些汽车部件的刚度的禁止降低和出现对乘客造成不舒适条件的声学问题,更不用说与机械强度增加有关的延展性的不可避免的损失而具有其局限性。
第二路线包括通过使钢与其他较轻金属合金化来降低钢的密度。在这些合金中,称为铁-铝合金的低密度合金具有有吸引力的机械特性和物理特性,同时使得可以显著减轻重量。在这种情况下,低密度意指小于或等于7.4的密度。
JP 2005/015909描述了低密度TWIP钢,其具有高于20%的非常高的锰含量并且还包含最高达15%的铝,导致更轻的钢基体,但所公开的钢在轧制期间呈现出高变形阻力和可焊性问题。
本发明的目的是使得可获得同时具有以下特性的经冷轧的钢板:
-小于或等于7.4的密度,
-大于或等于900MPa并且优选等于或大于1000MPa的极限抗拉强度,
-大于或等于9%的均匀延伸率。
优选地,这样的钢还可以具有良好的成形适用性(特别是对于轧制)以及良好的可焊性和良好的可涂覆性。
本发明的另一个目的还在于使得可获得与常规工业应用相容同时对制造参数变化稳健的用于制造这些板的方法。
该目的通过提供根据权利要求1所述的钢板来实现。钢板还可以包括根据权利要求2至3所述的特征。另一个目的通过提供根据权利要求4所述的方法来实现。另一方面通过提供根据权利要求5至7所述的部件或车辆来实现。
为了获得本发明的期望的钢,组成非常重要;因此,在以下描述中提供了组成的详细说明。
碳含量为0.10%至0.6%并且充当重要的固溶强化元素。碳还增强κ(kappa)碳化物(Fe,Mn)3AlCx的形成。碳是奥氏体稳定元素并且引发马氏体转变温度Ms的强烈降低,使得确保了大量的残余奥氏体,从而提高了可塑性。将碳含量保持在上述范围内确保为钢板提供所需的强度和延展性水平。碳还允许在仍获得一些TRIP效应的同时降低锰含量。
锰含量必须为4%至20%。该元素是γ相生成元素(gammagenous)。锰含量与铝含量之比将对在热轧之后获得的组织具有强烈影响。添加锰的目的本质上是获得除铁素体之外还包含奥氏体的组织并使所述组织在室温下稳定。在锰含量低于4的情况下,奥氏体将不够稳定,存在在从退火作业线离开时在冷却期间过早转变成马氏体的风险。此外,添加锰增加D03畴(domain),允许在较高温度下和/或在较低量的铝下获得足够的D03析出。高于20%,铁素体的分数减小,这不利地影响本发明,因为这可能使得更难以达到所需的抗拉强度。在一个优选的实施方案中,锰的添加将被限制于17%。
铝含量为5%至15%,优选5.5%至15%。铝为α相生成元素(alphagenouselement)并因此倾向于促进铁素体的形成,特别是D03结构的有序铁素体(Fe,Mn,X)3Al(X为溶解在D03中的任何溶质添加物,例如Ni)的形成。铝具有2.7的密度并且对机械特性具有重要影响。随着铝含量增加,机械强度和弹性极限也增加,虽然由于位错迁移率降低导致均匀延伸率降低。低于4%,由于铝的存在引起的密度降低变得益处减小。高于15%,有序铁素体的存在增加超出预期极限并且不利地影响本发明,因为其开始赋予钢板脆性。优选地,铝含量将被限制于小于9%,以防止形成另外的脆性金属间析出。
除了上述限制之外,在一个优选的实施方案中,锰、铝和碳含量遵循以下关系:
0.3<(Mn/2Al)×exp(C)<2。
低于0.3,存在奥氏体量太低,可能导致延展性不足的风险。高于2,奥氏体体积分数可能变得高于49%,从而降低D03相析出的可能性。
硅是允许降低钢的密度且在固溶硬化中也有效的元素。硅还具有使D03相对于B2相稳定的正面效果。硅含量被限制于2.0%,因为高于该水平,该元素倾向于形成产生表面缺陷的强粘性氧化物。表面氧化物的存在损害了钢的可湿性,并且可能在可能的热浸镀锌操作期间产生缺陷。在一个优选的实施方案中,硅含量将优选被限制于1.5%。
本发明人已发现,硅、铝和镍的累积量必须至少等于6.5%以获得允许达到目标特性的D03的所需析出。
铌可以作为任选元素以0.01%至0.3%的量添加到本发明的钢中以提供晶粒细化。晶粒细化允许获得强度与延伸率之间的良好平衡,并且被认为有助于改善的疲劳性能。但是,铌倾向于在热轧期间阻碍再结晶,因此并不总是期望的元素。因此铌被保持为任选元素。
以与铌类似的方式,钛可以作为任选元素以0.01%至0.2%的量添加到本发明的钢中以提供晶粒细化。钛还具有使D03相对于B2相稳定的正面效果。因此,未作为氮化物、碳化物或碳氮化物析出的未结合部分的钛将使D03相稳定。
钒可以作为任选元素以0.01%至0.6%的量添加。当添加时,钒可以在退火期间形成细小的碳氮化物化合物,这些碳氮化物提供另外的硬化。钒还具有使D03相对于B2相稳定的正面效果。因此,未作为氮化物、碳化物或碳氮化物析出的未结合部分的钒将使D03相稳定。
铜可以作为任选元素以0.01%至2.0%的量添加以提高钢的强度和改善其耐腐蚀性。需要最少0.01%以获得这样的效果。然而,当其含量高于2.0%时,这可能使表面外观劣化。
镍可以作为任选元素以0.01%至2.0%的量添加以提高钢的强度和改善其韧性。镍还有助于形成有序铁素体。需要最少0.01%以获得这样的效果。然而,当其含量高于2.0%时,其倾向于使B2稳定,这对D03形成是不利的。
其他元素例如铈、硼、镁或锆可以按以下比例单独添加或者组合添加:REM≤0.1%,B≤0.01,Mg≤0.05和Zr≤0.05。直至所示的最大含量水平,这些元素使得可以使铁素体晶粒在凝固期间细化。
最后,可以添加钼、钽和钨以进一步使D03相稳定。它们可以单独添加或者组合添加直至最大含量水平:Mo≤2.0,Ta≤2.0,W≤2.0。超过这些水平,延展性受到损害。
本发明要求保护的板的显微组织以面积分数计包含10%至50%的奥氏体,所述奥氏体相任选地包含晶内(Fe,Mn)3AlCxκ碳化物(intragranular(Fe,Mn)3AlCx kappacarbides),剩余部分为铁素体,所述铁素体包含规则铁素体(regular ferrite)和D03结构的有序铁素体以及任选的最高达2%的晶内κ碳化物。
低于10%的奥氏体,无法获得至少9%的均匀延伸率。
规则铁素体存在于本发明的钢中以赋予钢高可成形性和延伸率,并且还在一定程度上赋予一定的抗疲劳断裂性。
在本发明的框架中,D03有序铁素体由化学计量为(Fe,Mn,X)3Al的金属间化合物限定。有序铁素体以以面积分数计0.1%,优选0.5%,更优选1.0%,并且有利地大于3%的最小量存在于本发明的钢中。优选地,至少80%的这样的有序铁素体的平均尺寸小于30nm,优选小于20nm,更优选小于15nm,有利地小于10nm,或者甚至小于5nm。该有序铁素体在第二退火步骤期间形成,为合金提供强度,由此可以达到900MPa的水平。如果不存在有序铁素体,则无法达到900MPa的强度水平。
在本发明的框架中,κ碳化物由化学计量为(Fe,Mn)3AlCx(其中x严格小于1)的析出物限定。铁素体晶粒内的κ碳化物的面积分数可以达到2%。高于2%,延展性降低,并且未实现大于9%的均匀延伸率。此外,可能发生在铁素体晶界周围κ碳化物的不受控制的析出,因此增加了在热轧和/或冷轧期间的努力。κ碳化物也可以存在于奥氏体相内,优选作为尺寸小于30nm的纳米尺寸的颗粒。
根据本发明的钢板可以通过任何合适的方法获得。然而,优选使用将描述的根据本发明的方法。
根据本发明的方法包括提供具有如上所述的本发明范围内的化学组成的钢的半成品铸件。铸件可以制成锭或者以板坯或薄带的形式连续制作。
为了简化的目的,将以作为半成品的板坯为例进一步描述根据本发明的方法。可以在连铸之后直接对板坯进行轧制,或者可以首先使板坯冷却至室温然后再加热。
经历热轧的板坯的温度必须低于1280℃,因为高于该温度,存在形成粗铁素体晶粒的风险,产生粗铁素体晶粒,这降低了这些晶粒在热轧期间再结晶的能力。初始铁素体晶粒尺寸越大,再结晶越不容易,这意味着必须避免高于1280℃的再加热温度,因为其在工业上是昂贵的并且在铁素体的再结晶方面是不利的。粗铁素体也倾向于放大称为“皱纹状变形(roping)”的现象。
期望在铁素体的存在下以至少一个轧制道次进行轧制。目的是增强使奥氏体稳定的元素向奥氏体的配分,以防止铁素体中的碳饱和,这可能导致脆性。最终轧制道次在高于800℃的温度下进行,因为低于该温度,钢板表现出可轧制性的显著下降。
在一个优选的实施方案中,板坯的温度足够高,使得热轧可以在临界区温度范围内完成,并且终轧温度保持高于850℃。优选850℃至980℃的终轧温度以具有对再结晶和轧制有利的组织。优选在高于900℃的板坯温度下开始轧制,以避免可能施加在轧机上的过大负荷。
然后使以这种方式获得的板以优选小于或等于100℃/秒的冷却速率冷却至卷取温度。优选地,冷却速率小于或等于60℃/秒。
然后在低于600℃的卷取温度下卷取经热轧的钢板,因为高于该温度,存在可能无法将铁素体内的κ碳化物析出控制至最大2%的风险。高于600℃的卷取温度还将导致奥氏体的显著分解,使得难以确保所需量的这样的相。因此,本发明的经热轧的钢板的优选卷取温度为400℃至550℃。
任选的热带退火可以在400℃至1000℃的温度下进行以改善可冷轧制性。热带退火可以为连续退火或分批退火。均热的持续时间将取决于热带退火是连续退火(50秒至1000秒)还是分批退火(6小时至24小时)。
然后以35%至90%的厚度压下量对经热轧的板进行冷轧。
然后使获得的经冷轧的钢板经历两步退火处理以赋予钢目标机械特性和显微组织。
在第一退火步骤中,将经冷轧的钢板以优选大于1℃/秒的加热速率加热至750℃至950℃的保温温度持续小于600秒的持续时间以确保强加工硬化初始组织的大于90%的再结晶率。然后使板冷却至室温,其中优选大于30℃/秒的冷却速率以控制铁素体内或奥氏体-铁素体界面处的κ碳化物。
然后可以例如将在第一退火步骤之后获得的经冷轧的钢板以至少10℃/小时的加热速率再次再加热至150℃至600℃的保温温度持续10秒至1000小时,优选1小时至1000小时,或者甚至3小时至1000小时的持续时间,然后冷却至室温。这样做是为了有效地控制D03有序铁素体的形成,并且可能有效地控制奥氏体内的κ碳化物的形成。保温的持续时间取决于使用的温度。
然后可以通过任何合适的方法(例如电沉积或真空涂覆)用金属涂层例如锌或锌合金来涂覆经冷轧的钢板。喷射气相沉积是用于涂覆根据本发明的钢的优选方法。
还可以对经冷轧的钢板进行热浸涂覆,这意味着对于锌或锌合金涂层再加热至460℃至500℃的温度。应完成这样的处理使得不改变钢板的任何机械特性或显微组织。
实施例
本文中提出的以下测试、实施例、图形示例和表本质上是非限制性的,并且必须仅出于说明的目的而被考虑,并且将显示本发明的有利特征。
用表1中汇总的组成和表2中汇总的工艺参数制备根据本发明和一些比较等级的钢板的样品。这些钢板的相应的显微组织汇总在表3中。
表1-组成
*根据本发明
表2-工艺参数
热轧和冷轧参数
*根据本发明
退火参数
*根据本发明
表3-显微组织
**通过透射电子显微镜检测到的奥氏体中κ析出的早期阶段。奥氏体显微组织在第二热处理之后保持稳定,而没有在其他相如珠光体或贝氏体中分解。
奥氏体和铁素体中的相比例和κ析出通过电子背散射衍射和透射电子显微镜来确定。
D03析出通过用电子显微镜的衍射和通过如在“Materials Science andEngineering:A,第258卷,第1-2期,1998年12月,第69-74页,Neutron diffraction studyon site occupation of substitutional elements at sub lattices in Fe3 Alintermetallics(Sun Zuqing,Yang Wangyue,Shen Lizhen,Huang Yuanding,ZhangBaisheng,Yang Jilian)”中描述的中子衍射来确定。
对来自试验E的样品进行一些显微组织分析,在图1(a)和图1(b)上再现了D03结构的图像:
(a)D03结构的暗视场像
(b)相应的衍射图、晶带轴(zone axis)[100]D03。箭头表示用于(a)中的暗视场像的反射。
然后评估这些钢板的特性,结果汇总在表4中。
表4-特性
屈服强度YS、抗拉强度TS、均匀延伸率UE和总延伸率TE根据2009年10月公开的ISO标准ISO 6892-1来测量。密度根据ISO标准17.060通过测比重(pycnometry)来测量。
实施例表明,根据本发明的钢板由于其特定组成和显微组织是唯一显示出所有目标特性的钢板。
Claims (7)
1.一种经冷轧和热处理的钢板,以重量百分比表示,其组成包含以下元素:
0.10%≤碳≤0.6%
4%≤锰≤20%
5%≤铝≤15%
0%≤硅≤2%
铝+硅+镍≥6.5%
并且可能包含以下任选元素中的一者或更多者:
0.01%≤铌≤0.3%
0.01%≤钛≤0.2%
0.01%≤钒≤0.6%
0.01%≤铜≤2.0%
0.01%≤镍≤2.0%
铈≤0.1%
硼≤0.01%
镁≤0.05%
锆≤0.05%
钼≤2.0%
钽≤2.0%
钨≤2.0%
剩余部分由铁和通过加工引起的不可避免的杂质构成,其中所述钢板的显微组织以面积分数计包含10%至50%的奥氏体,所述奥氏体相任选地包含晶内κ碳化物,剩余部分为规则铁素体和D03结构的有序铁素体(Fe,Mn,X)3Al,任选地包含最高达2%的晶内κ碳化物(Fe,Mn)3AlCx,所述钢板呈现出高于或等于900MPa的极限抗拉强度。
2.根据权利要求1所述的经冷轧和热处理的钢板,其中铝、锰和碳的量为使得0.3<(Mn/2Al)×exp(C)<2。
3.根据权利要求1至2所述的经冷轧和热处理的钢板,其中所述钢板呈现出小于或等于7.4的密度和高于或等于9%的均匀延伸率。
4.一种生产经冷轧和热处理的钢板的方法,包括以下步骤:
-提供具有根据权利要求1至2所述的组成的经冷轧的钢板,
-在小于600秒期间将所述经冷轧的钢板加热至750℃至950℃的均热温度,然后使所述板冷却至室温,
-在10秒至1000小时期间将所述钢板再加热至150℃至600℃的均热温度,然后使所述板冷却。
5.根据权利要求1至3中任一项生产的钢板或者根据权利要求4所述的方法生产的钢板用于制造车辆的结构部件或***件的用途。
6.一种根据权利要求5所述的部件,通过所述钢板的柔性轧制得到。
7.一种车辆,包括根据权利要求5或6中任一项获得的部件。
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US20230105826A1 (en) | 2023-04-06 |
US11549163B2 (en) | 2023-01-10 |
CA3082063C (en) | 2023-02-28 |
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CN111492078B (zh) | 2023-11-17 |
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WO2019122960A1 (en) | 2019-06-27 |
WO2019123239A1 (en) | 2019-06-27 |
EP3728678A1 (en) | 2020-10-28 |
JP2021507110A (ja) | 2021-02-22 |
KR20230118708A (ko) | 2023-08-11 |
ES2968626T3 (es) | 2024-05-13 |
HUE064787T2 (hu) | 2024-04-28 |
PL3728678T3 (pl) | 2024-03-11 |
RU2751718C1 (ru) | 2021-07-16 |
ZA202002478B (en) | 2021-08-25 |
US20210123121A1 (en) | 2021-04-29 |
MA51317B1 (fr) | 2024-01-31 |
KR20200080317A (ko) | 2020-07-06 |
MA51317A (fr) | 2021-03-31 |
US12060629B2 (en) | 2024-08-13 |
BR112020009287A2 (pt) | 2020-10-27 |
UA126092C2 (uk) | 2022-08-10 |
JP7138710B2 (ja) | 2022-09-16 |
MX2020006341A (es) | 2020-09-03 |
EP3728678B1 (en) | 2023-11-22 |
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