CN111771009A - 一种汽车钢及其制造方法 - Google Patents
一种汽车钢及其制造方法 Download PDFInfo
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- CN111771009A CN111771009A CN201880088966.1A CN201880088966A CN111771009A CN 111771009 A CN111771009 A CN 111771009A CN 201880088966 A CN201880088966 A CN 201880088966A CN 111771009 A CN111771009 A CN 111771009A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 174
- 239000010959 steel Substances 0.000 title claims abstract description 174
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 36
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 33
- 238000010791 quenching Methods 0.000 claims abstract description 23
- 230000000171 quenching effect Effects 0.000 claims abstract description 20
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 16
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 15
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 13
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 11
- 239000011159 matrix material Substances 0.000 claims abstract description 8
- 239000011572 manganese Substances 0.000 claims description 33
- 238000001816 cooling Methods 0.000 claims description 23
- 238000000034 method Methods 0.000 claims description 23
- 238000005496 tempering Methods 0.000 claims description 18
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 16
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 10
- 239000010949 copper Substances 0.000 claims description 9
- 239000010936 titanium Substances 0.000 claims description 9
- 239000011651 chromium Substances 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 8
- 239000010955 niobium Substances 0.000 claims description 8
- 238000005242 forging Methods 0.000 claims description 7
- 229910000859 α-Fe Inorganic materials 0.000 claims description 7
- 238000000137 annealing Methods 0.000 claims description 6
- 238000005097 cold rolling Methods 0.000 claims description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 5
- 238000005554 pickling Methods 0.000 claims description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- 229910052796 boron Inorganic materials 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 239000010960 cold rolled steel Substances 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 239000011733 molybdenum Substances 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 3
- 229910052702 rhenium Inorganic materials 0.000 claims description 3
- WUAPFZMCVAUBPE-UHFFFAOYSA-N rhenium atom Chemical compound [Re] WUAPFZMCVAUBPE-UHFFFAOYSA-N 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 3
- 238000005096 rolling process Methods 0.000 claims description 2
- 230000000717 retained effect Effects 0.000 abstract description 6
- 239000003381 stabilizer Substances 0.000 abstract description 5
- 238000005192 partition Methods 0.000 abstract description 2
- 230000000694 effects Effects 0.000 description 12
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 10
- 239000000126 substance Substances 0.000 description 9
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- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 230000000670 limiting effect Effects 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 230000000930 thermomechanical effect Effects 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
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- 238000004134 energy conservation Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
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- 238000002474 experimental method Methods 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
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- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C21D1/18—Hardening; Quenching with or without subsequent tempering
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Abstract
一种强力且可延展的汽车钢,其包含8‑11重量%的Mn、0.1‑0.35重量%的C、1‑3重量%的Al、0.05‑0.5重量%的V以及余量的Fe。通过调节奥氏体稳定剂的量,可以在室温下获得具有适当相分数的马氏体和奥氏体的双相显微组织。马氏体分配C进入残留的奥氏体晶粒。马氏体基体可以确保更高的汽车钢强度,而具有不同机械稳定性的残留奥氏体晶粒可以改善汽车钢的延展性,同时达到1500MPa的强度和20%的延展性。该汽车钢的制造方法避免了常规Q&P钢的高淬火温度,且因此降低了制造价格并且易于批量制造。
Description
技术领域
本发明总体上涉及一种强力且可延展的汽车钢,以及用于制造这种汽车钢的方法。
背景技术
轻量化汽车对于节能、更少的温室气体排放以及其他方面的环境友好是期望的。因此,轻量化汽车对于全球汽车工业是不可逆转的趋势。可以通过在汽车工业中广泛使用先进高强度钢(AHSS)实现这一点。AHSS主要用于制造汽车的结构部件如B柱。由于高强度,包括双相(DP)钢以及淬火配分(Q&P)钢的AHSS与常规钢相比可以使用更薄的板,从而在不牺牲乘客安全的情况下实现更轻的汽车重量。
目前,DP钢是汽车工业中使用最广泛的AHSS。根据极限抗拉强度,可以将DP钢分为不同等级如DP 580、DP 780和DP 980。因此,DP钢的强度已达到极限(<1GPa)。换句话说,DP钢对汽车的重量减轻的贡献也达到了其极限。DP钢强度有限的根本原因归因于其软铁素体基体。相比之下,Q&P钢中的硬马氏体基体可以克服该缺陷。因此,Q&P钢现已成为AHSS领域的热门研究课题。目前,Q&P钢有两种商业钢等级,包括Q&P 980和Q&P 1180。Q&P钢的发展使进一步减轻汽车重量成为可能。
目前,研究人员的目标是进一步改善Q&P钢的强度,例如改善Q&P钢的强度至1500MPa水平(Q&P 1500)。当前的商业Q&P钢的锰(Mn)含量相对较低。例如,Q&P 980和Q&P1180二者中的Mn含量均在3重量%以下。众所周知,Mn元素是强奥氏体稳定剂。由于Mn含量低,Q&P 980和Q&P 1180二者的最佳淬火温度范围为200-300℃。分配温度一般高于淬火温度。因此,Q&P构思最初在现有的钢铁生产线中遇到了重大困难。此外,Q&P 980和Q&P 1180的强度也接近它们的极限。因此,提高Q&P钢的强度是钢铁工业的下一步。合金设计对改善Q&P钢的性质起着关键作用。目前,研究人员倾向于增加Q&P钢中的Mn元素和碳(C)元素。然而,提出的Q&P钢中的Mn含量大部分在5重量%以下。结果,研究人员仍然不能规避Q&P钢中的高淬火温度。
发明概述
本发明涉及一种包含增加的Mn含量的新的且有利的汽车钢,以及一种用于制造强力且可延展的汽车钢的简单方法。
在本发明的一个方面,提供一种强力且可延展的汽车钢,其基于汽车钢的重量包含8-11重量%范围的锰(Mn)、0.1-0.35重量%范围的碳(C)、1-3重量%范围的铝(Al)、0.05-0.5重量%范围的钒(V)以及余量的铁(Fe)。
优选地,所述汽车钢包含9.5-10.5重量%的Mn、0.18-0.22重量%的C、1.8-2.2重量%的Al、0.08-0.12重量%的V以及余量的Fe。
在示例性实施方案中,强力且可延展的汽车钢包含,以重量百分比计:10重量%的Mn、0.2重量%的C、2重量%的Al、0.1重量%的V和余量的Fe。
优选地,该汽车钢还包含以下元素中的至少一种:0.1-2.0重量%范围的镍(Ni)、0.2-2.0重量%范围的铬(Cr)、0.1-0.5重量%范围的钼(Mo)、0.3-2.0重量%范围的硅(Si)、0.0005-0.005重量%范围的硼(B)、0.02-0.10重量%范围的铌(Nb)、0.05-0.25重量%范围的钛(Ti)、0.25-0.50重量%范围的铜(Cu)以及0.002-0.005重量%范围的铼(Re)。
在本发明的另一方面,提供一种制造汽车钢的方法,其包括:制备包含8-11重量%范围的锰(Mn)和余量的Fe的钢锭;从钢锭提供钢板;等温保持钢板以形成奥氏体;将钢板冷却至室温;在300-400℃的温度下回火钢板;并将钢板淬火至室温。
优选地,所述提供钢板的步骤通过铸造、热轧、锻造和冷轧中的至少一种进行。
优选地,所述等温保持在Ac3-20℃至Ac3+100℃的温度下进行,其中Ac3是铁素体完全转变成奥氏体形式的温度。
优选地,所述等温保持的步骤进行5-20分钟。
优选地,所述室温是在10℃至40℃的范围。
优选地,所述冷却步骤通过空气、油和水中的至少一种进行。
优选地,所述冷却步骤以高于0.5℃/s的第一冷却速率进行。
优选地,所述回火钢板的步骤进行5-10分钟。
优选地,所述淬火钢板的步骤以高于0.5℃/s的第二冷却速率进行。
优选地,所述钢锭还包含0.1-0.35重量%范围的碳(C)、1-3重量%范围的铝(Al)和0.05-0.5重量%范围的钒(V)。
更优选地,所述汽车钢包含基于汽车钢的重量9.5-10.5重量%的Mn、0.18-0.22重量%的C、1.8-2.2重量%的Al、0.08-0.12重量%的V以及余量的Fe。
优选地,所述钢锭还包含镍(Ni)、铬(Cr)、钼(Mo)、硅(Si)、硼(B)、铌(Nb)、钛(Ti)、铜(Cu)和铼(Re)中的至少一种。
在一个优选的实施方案中,一种用于制造强力且可延展的汽车钢的方法包括以下步骤:
(1)提供包含8-11重量%的Mn、0.1-0.35重量%的C、1-3重量%的Al、0.05-0.5重量%的V和余量的Fe的钢锭;
(2)锻造和轧制钢锭以提供厚度为4-6mm的钢板,并冷却钢板;
(3)在500-750℃的温度下分批退火5-10小时;
(4)酸洗以去除钢板中的氧化物层;
(5)冷轧钢板以提供最终厚度为0.8-2mm的冷钢板;
(6)通过热加工处理钢板以获得奥氏体嵌入马氏体基体中的双相显微组织,并以高于0.5℃/s的冷却速率将钢板冷却至室温,其中热加工路线包括在Ac3-20℃至Ac3+100℃的温度范围等温保持钢板,持续5-20分钟的时间段以形成部分或全部奥氏体;和
(7)将钢板在300-400℃的温度范围回火,持续5-20分钟的时间段,并以高于0.5℃/s的冷却速率淬火至室温。
优选地,淬火至室温后马氏体的体积分数在70%至90%的范围。马氏体的体积分数(f)可以通过以下等式f=1-exp(-C1(Ms-T))确定,其中C1是经验参数,Ms是马氏体起始温度,而T是Ms温度以下的温度。这里的T是室温(10-40℃)。Ms温度可以通过以下等式确定:Ms=539-423C-30.4Mn-17.7Ni-12.1Cr-7.5Mo-7.5Si(℃),其中该等式中的元素以质量百分比计。
优选地,通过空气、油或水将钢板冷却至室温。
优选地,通过水将钢板冷却至室温。
根据本发明,通过增加提出的Q&P钢中的Mn含量将淬火温度降低到室温,同时采用常规的低温回火来促进C分配。因此,获得强力且可延展的Q&P钢。通过简单的室温淬火和低温回火工艺制造强力且可延展的Q&P钢将是汽车工业的一大进步。
附图简述
参考以下附图可以更好地理解本实施方案的许多方面。附图中的组件不必按比例绘制,重点在于清楚地说明本实施方案的原理。此外,在附图中,所有视图都是示意性的,并且在所有几个视图中,相同的附图标记表示相应的部分。
图1是根据本发明的一个实施方案的具有Fe-10Mn-0.2C-2Al-0.1V(以重量%计)的化学组成的汽车钢的热机械加工路线的示意图。
图2示出根据示例性实施方案的汽车钢在空气炉中在800℃下等温保持10分钟时的工程应力应变曲线。
图3示出根据本发明的实施方案的汽车钢在空气炉中在850℃下等温保持10分钟时的工程应力曲线。
图4示出根据本发明的实施方案的汽车钢在空气炉中在900℃下等温保持10分钟时的工程应力曲线。
详述
在附图的图中通过示例而非限制的方式示出了本公开内容,在附图中,相同的附图标记表示相同的元件。应当注意,在本公开内容中对“一”或“一个”实施方案的引用不一定是同一个实施方案,并且这种引用可以表示“至少一个”实施方案。
根据本发明,所述强力且可延展的汽车钢包含,以重量百分比计:8-11重量%的Mn、0.1-0.35重量%的C、1-3重量%的Al、0.05-0.5重量%的V、和余量的铁。
在示例性实施方案中,所述强力且可延展的汽车钢包含,以重量百分比计:10重量%的Mn、0.2重量%的C、2重量%的Al、0.1重量%的V和余量的Fe。
根据本发明,C元素在提高汽车钢的强度方面是有效的。同时,C是强奥氏体稳定剂。在本发明中,选择C含量为0.1重量%以上以获得这些效果。然而,当C含量高于0.35重量%时,汽车钢的焊接性能将降低。因此,将C含量选择在0.1重量%至0.35重量%的范围。
根据本发明,Mn元素也是强奥氏体稳定剂。类似地,Mn元素可以提供固溶体强化以改善汽车钢的强度。为了在淬火至室温之后获得适当量的马氏体和奥氏体体积分数,选择在汽车钢中的Mn含量为8重量%以上。然而,Mn含量应不高于11重量%,因为较高的Mn含量不会导致适当量的马氏体并因此不会导致期望的机械性质。因此,将Mn含量选择在8重量%至11重量%的范围。
根据本发明,V元素可以增加汽车钢的强度。同时,V元素可以细化奥氏体晶粒尺寸,并且产生的V析出可以改善汽车钢的抗延迟断裂。选择V的量为0.05重量%以上以获得上述效果。然而,添加V将增加钢的价格。基于上述原因,选择V含量为0.05重量%以上,但优选0.5重量%以下。
根据本发明,Al元素可以抑制回火过程期间渗碳体析出。为了实现该效果,选择Al含量为1重量%以上。然而,如果Al含量高于3重量%,则很有可能具有大的氧化物夹杂和δ-铁素体,并且导致汽车钢的延展性差。基于上述原因,选择Al含量为1重量%以上但3重量%以下。
此外,汽车钢还可以包含以下元素中的至少一种以改善性能:Ni(0.1-2.0重量%)、Cr(0.2-2.0重量%)、Mo(0.1-0.5重量%)和B(0.0005-0.005重量%)。可以包括这些元素以改善汽车钢的淬透性和低温韧性。为了实现这些效果,Ni和Mo的量应高于0.1重量%,Cr的量应高于0.2重量%,并且B的量应高于0.0005重量%。然而,当Ni含量或Cr含量高于2重量%时,或当Mo含量高于0.5重量%时或当B含量高于0.005重量%时,将发生饱和效应,并且汽车钢的价格也将增加。因此,这些元素的量应保持在上述上限以下。
根据本发明,还可以添加Nb(0.02-0.1重量%)和Ti(0.05-0.25重量%)以细化先前的奥氏体晶粒尺寸。Ti可以形成TiN,并抑制BN的形成,因此B原子可以提高汽车钢的淬透性。优选地,Nb的量高于0.02重量%,而Ti的量高于0.05重量%。然而,当Nb含量高于0.1重量%时或当Ti高于0.25重量%时,将发生饱和效应,并且汽车钢的价格也将增加。因此,这些元素的量应保持在上述上限以下。
根据本发明,添加Cu(0.25-0.50重量%)是为了改善汽车钢的强度。为了实现该效果,选择Cu的量为0.25重量%以上。然而,当Cu的量高于0.5重量%时,钢将具有差的热轧性能并且焊接能力将降低。因此,Cu的量应保持在上述上限以下。
根据本发明,添加Si(0.3-1.0重量%)是为了改善汽车钢的抗氧化性和耐腐蚀性。Si元素还可以抑制回火过程期间渗碳体的析出。为了实现该效果,选择Si的量为0.3重量%以上。然而,当Si的量高于1.0重量%时,钢将具有坚固的氧化物层,其将在热轧过程期间嵌入表面。因此,表面质量、热延展性、焊接能力和疲劳性质将降低。因此,Si的量应保持在上述上限以下。
根据本发明,添加Re(0.25-0.50重量%)是为了改善汽车钢中颗粒的形态和尺寸分布。为了实现该效果,选择Re的量为0.002重量%以上。然而,当Re的量高于0.005重量%时,将发生饱和效应,并且汽车钢的价格也将增加。因此,Re的量应保持在上述上限以下。
根据本发明,可将钢锭铸造、热轧或冷轧以制造汽车钢。对于铸造技术,优选使用连续铸造以制造板坯。对于热轧,优选将板坯在1100-1250℃的温度下加热,并通过5-20道次将其热轧至50-80mm的厚度以制造厚的热轧板或通过7-10道次通过进一步热轧至4-10mm的厚度而具有薄的热轧板材。对于冷轧,优选在500-750℃的温度下采用分批退火5-10小时以软化热轧板。通过5-12道次冷轧以提供最终厚度为0.8mm至2mm的冷轧板。如果在酸洗后可以将热轧板直接冷轧至目标厚度(0.8mm至2mm),则可以省去先前的分批退火步骤,以节省能源和成本。钢铁工业中的其他常规热机械加工技术如锻造和镀锌也可以在这里使用以制造汽车钢。
获得钢板后,采用热加工路线获得奥氏体嵌入马氏体基体的双相显微组织。钢板在Ac3-20℃至Ac3+100℃的温度范围等温保持,持续5至20分钟的时间段,以形成部分或全部奥氏体。Ac3是指铁素体完全转变成奥氏体的温度。该过程可以在将热轧产品冷却至室温之后或直接在热轧过程之后采用。然后以高于0.5℃/s的冷却速率将板冷却至室温。冷却介质可以是水、油、空气或钢铁工业中的其他常规冷却介质。根据本发明的化学组成,淬火至室温后,存在大量的具有一些残留的奥氏体和/或少量铁素体的马氏体。
然后将钢板在300至400℃的温度范围回火,持续5-10分钟的时间段,最后以高于0.5℃/s的冷却速率淬火至室温。冷却介质可以是水、油、空气或钢铁工业中的其他常规冷却介质。回火过程用于使C从马氏体分配到残留奥氏体,从而使奥氏体可以具有适当的机械稳定性,并用于提供连续转变诱发的塑性(TRIP)效应,以改善汽车钢的延展性。另外,回火过程有利于减轻淬火至室温期间马氏体转变诱发的剩余应力。使用浸镀锌(dipgalvanized,GI)或合金化热浸镀锌(hot-dip galvannealed,GA)的Zn涂层可用于制造用于汽车应用的镀锌(galvanized)或合金化镀锌(galvannealed)钢板。另外,根据汽车工业的要求,没有Zn涂层的钢板也可用于汽车应用。值得一提的是,化学组成应设计成在淬火至室温后具有70%-90%的马氏体的体积分数。如果马氏体的体积分数在60%以下,则应降低Mn含量。降低C含量以获得更大的马氏体的体积分数是不期望的,因为降低C含量将显著降低马氏体基体的强度。如果马氏体的体积分数高于90%,则应增加Mn含量和/或C含量。基于先前关于马氏体强度的原因,优选增加C含量以获得较少的马氏体基体。淬火至室温后,具有不同Mn和C含量的汽车钢中马氏体的体积分数(f)可以通过以下等式f=1-exp(-C1(Ms-T))确定,其中C1是从大量统计数据获得的经验参数,并且可以选择为-0.011,Ms为马氏体起始温度,T为Ms温度以下的温度,此处T为室温(10-40℃)。Ms温度可以通过以下等式确定:Ms=539-423C-30.4Mn-17.7Ni-12.1Cr-7.5Mo-7.5Si(℃),其中元素以质量百分比计。
实施发明的最佳方式
以下是说明实施本发明的方法的实施例。这些实施例不应被解释为限制性的。
实施例1
该实施例用于说明具有Fe-10Mn-0.2C-2Al-0.1V(重量%)组成的汽车钢的制造方法。
(1)提供钢锭,将钢锭锻造成厚度为12mm的钢板,并冷却钢板;
(2)酸洗以除去钢板中的氧化物层;
(3)将钢板在800℃、850℃或900℃的温度下等温保持10分钟;并通过浸入水中将钢板冷却至室温;
(4)将钢板在300℃、350℃或400℃的温度下回火10分钟,并通过浸入水中淬火至室温。
图1是获得汽车钢的拉伸试样的热加工路线的示意图。加工路线包括退火以获得部分或全部奥氏体,然后进行室温淬火(RT-Q)以获得马氏体,并且最后进行低温回火以实现C分配。从厚度为12mm的锻造大钢板材线切割厚度为4mm的ASTM次标准拉伸试样。
比较例1
该比较例用于说明具有Fe-0.2C-1.5Mn-1.5Si(重量%)组成的现有技术的汽车钢的制造过程。
(1)提供钢锭,将钢锭锻造并热轧成4mm厚的钢板,并冷却钢板;
(2)在600℃之间分批退火1小时;
(3)酸洗以去除钢板中的氧化物层;
(4)冷轧钢板以提供最终厚度为1.5mm的冷钢板;
(5)将钢板在860℃下等温保持5分钟,然后以5℃/s缓慢冷却至约725℃;然后将钢以50℃/s快速淬火至280℃,然后再加热并在350℃下保持10s,然后以50℃/s淬火至室温。
与比较例1相比,本发明大大简化了加工路线。例如,比较例1应精确地控制温度以实现期望的铁素体、马氏体和奥氏体的显微组织。相比之下,本发明仅涉及室温淬火以具有马氏体和奥氏体。此外,如下面讨论的,本发明提供了具有比比较例1的机械性质更好的机械性质的钢。
通过举例说明,从以下实施例中可以更好地理解本发明及其许多优点。以下实施例显示了本发明的一些方法、应用、实施方案和变体。当然,它们不应被认为是对本发明的限制。可以相对于本发明进行许多改变和修改。
图2示出Fe-10Mn-0.2C-2Al-0.1V(重量%)的工程应力应变曲线。将拉伸样品在空气炉中于800℃下等温保持10分钟,然后水淬冷至室温。然后将拉伸样品在300℃下回火10min,或在350℃下回火10min,或在400℃下回火5min,或在400℃下回火10min。然后在回火后在水中将拉伸样品淬火。拉伸测试是在室温下对标距长度为32mm的拉伸样品进行的。在拉伸测试期间,网格速度为1.2mm/min。曲线①对应于在300℃下回火10分钟的拉伸试样。曲线②对应于在350℃下回火10分钟的拉伸试样。曲线③对应于在400℃下回火5分钟的拉伸试样。曲线④对应于在400℃下回火10分钟的拉伸试样。曲线⑤对应于从比较例1获得的拉伸试样。
图3示出Fe-10Mn-0.2C-2Al-0.1V(重量%)的工程应力应变曲线。将拉伸样品在空气炉中于850℃下等温保持10分钟,然后水淬冷至室温。然后将拉伸样品在300℃下回火10min,或在350℃下回火10min,或在400℃下回火5min,或在400℃下回火10min。然后在回火后在水中将拉伸样品淬火。拉伸测试是在室温下对标距长度为32mm的拉伸样品进行的。在拉伸测试期间,网格速度为1.2mm/min。曲线①对应于在300℃下回火10分钟的拉伸试样。曲线②对应于在350℃下回火10分钟的拉伸试样。曲线③对应于在400℃下回火5分钟的拉伸试样。曲线④对应于在400℃下回火10分钟的拉伸试样。曲线⑤对应于从比较例1获得的拉伸试样。
图4示出Fe-10Mn-0.2C-2Al-0.1V(重量%)的工程应力应变曲线。将拉伸样品在空气炉中于900℃下等温保持10分钟,然后水淬冷至室温。然后将拉伸样品在300℃下回火10min,或在350℃下回火10min,或在400℃下回火5min,或在400℃下回火10min。然后在回火后在水中将拉伸样品淬火。拉伸测试是在室温下对标距长度为32mm的拉伸样品进行的。在拉伸测试期间,网格速度为1.2mm/min。曲线①对应于在300℃下回火10分钟的拉伸试样。曲线②对应于在350℃下回火10分钟的拉伸试样。曲线③对应于在400℃下回火5分钟的拉伸试样。曲线④对应于在400℃下回火10分钟的拉伸试样。曲线⑤对应于从比较例1获得的拉伸试样。
在本发明的实施方案中,在800℃至900℃的温度下部分或全部奥氏体化和在300℃至400℃的温度下的低温回火可以实现汽车钢的优异机械性质。这表明本发明汽车钢的加工窗口宽,且因此易于工业制造。具体地,在850℃下全部奥氏体化10分钟,并在300℃下回火10分钟,可以获得优异的拉伸性质。该奥氏体化温度可以在现有的钢铁工业中直接实现,这表明该专利中的汽车钢可以在减少障碍的情况下进行批量制造。汽车钢的屈服强度在600-950MPa范围,优选在800-950MPa范围。汽车钢的拉伸强度在1280-1670MPa范围,优选在1500-1670MPa范围。汽车钢的伸长率在19-26%范围,优选在21-23%范围。优选地,在850℃下奥氏体化10分钟并且在300℃下回火10分钟可以实现910MPa的屈服强度、1505MPa的拉伸强度和21.5%的总伸长率。更重要的是,本发明的汽车钢具有高强度、无屈服点伸长、无应变时效和高应***化率。这些特征对于在汽车工业中的应用是期望的。本发明汽车钢的拉伸强度高于现有的商业汽车钢如DP780、Q&P980和Q&P1180。此外,该汽车钢还具有良好的延展性(约20%)和大的后均匀伸长率(post-uniform elongation)(约7%)。后均匀伸长率影响扩孔性能,其是汽车工业中非常重要的评估准则。对于本领域的技术人员而言,大的后均匀伸长率也表明本发明汽车钢具有良好的断裂韧性,这对于使用期间汽车钢的安全性非常重要。
除了Fe-10Mn-0.2C-2Al-0.1V(重量%)的化学组成外,本发明的实施方案还包含用于机械测试的其他组成。选择化学组成的主要指导准则是在室温下马氏体的体积分数在70%-90%范围,以便马氏体可以将C分配到残留的奥氏体中,以实现特制的机械稳定性。化学组成的详细信息可见于表1。
表1
样品G1-G11对应于不同的化学组成。实验表明,具有通过本发明提出的方法制造的这些化学组成的汽车钢都可以实现优异的机械性质,并且比常规汽车钢更好。
本发明的实施方案基于化学组成的适当设计,通过简单的室温淬火,在室温下获得马氏体和奥氏体的双相显微组织。在低温回火过程期间发生C分配。残留的奥氏体晶粒的稳定性取决于C含量。具有不同机械稳定性的奥氏体晶粒可以提供连续的TRIP效果,以改善延展性。从全部奥氏体区淬火到室温后的相分数取决于合金元素的种类和量。在实施方案中,通过使用奥氏体稳定剂调节马氏体和奥氏体的相分数获得强力且可延展的汽车钢。实施方案中用于制造汽车钢的方法避免了常规Q&P钢的高淬火温度的困难。另外,通过控制先前的奥氏体晶粒尺寸,诸如通过微合金化或不同的奥氏体化温度和时间,还可以在室温下改变马氏体和奥氏体的相分数。因此,它也可以用于优化本发明汽车钢的机械性质。
尽管以特定组合将本公开内容的特征和要素描述为实施方案,但是在本公开内容的原理内,每个特征或要素可以单独使用或以其他各种组合使用,达到由表达所附权利要求的术语的广义一般含义所指示的全部程度。
Claims (13)
1.一种强力且可延展的汽车钢,其基于汽车钢的重量包含8-11重量%范围的锰、0.1-0.35重量%范围的碳、1-3重量%范围的铝、0.05-0.5重量%范围的钒、以及余量的铁。
2.权利要求1所述的汽车钢,其中,所述汽车钢包含9.5-10.5重量%的Mn、0.18-0.22重量%的C、1.8-2.2重量%的Al、0.08-0.12重量%的V、以及余量的铁。
3.权利要求1所述的汽车钢,其中,所述汽车钢还包含10重量%的Mn、0.2重量%的C、2重量%的Al、0.1重量%的V、以及余量的Fe。
4.权利要求1所述的汽车钢,其中,所述汽车钢还包含以下元素中的至少一种:0.1-2.0重量%范围的镍、0.2-2.0重量%范围的铬、0.1-0.5重量%范围的钼、0.3-2.0重量%范围的硅、0.0005-0.005重量%范围的硼、0.02-0.10重量%范围的铌、0.05-0.25重量%范围的钛、0.25-0.50重量%范围的铜、以及0.002-0.005重量%范围的铼。
5.一种制造汽车钢的方法,其包括:制备包含8-11重量%范围的锰和余量的Fe的钢锭;从钢锭提供钢板;等温保持钢板以形成奥氏体;将钢板冷却至室温;在300-400℃的温度下回火钢板;并且将钢板淬火至室温。
6.权利要求5所述的方法,其中,所述从钢锭提供钢板的步骤通过铸造、热轧、锻造和冷轧中的至少一种进行。
7.权利要求5所述的方法,其中,所述等温保持在Ac3-20℃至Ac3+100℃的温度下进行,其中Ac3是铁素体完全转变成奥氏体的温度。
8.权利要求5所述的方法,其中,所述等温保持进行5-20分钟。
9.权利要求5所述的方法,其中,所述冷却以高于0.5℃/s的第一冷却速率进行。
10.权利要求5所述的方法,其中,所述回火钢板的步骤进行5-10分钟。
11.权利要求5所述的方法,其中,所述淬火钢板的步骤以高于0.5℃/s的第二冷却速率进行。
12.一种用于制造强力且可延展的汽车钢的方法,其包括以下步骤:
(1)提供包含8-11重量%的Mn、0.1-0.35重量%的C、1-3重量%的Al、0.05-0.5重量%的V和余量的Fe的钢锭;
(2)锻造和轧制钢锭以提供厚度为4-6mm的钢板,并冷却钢板;
(3)在500-750℃的温度下分批退火5-10小时;
(4)酸洗以去除钢板中的氧化物层;
(5)冷轧钢板以提供最终厚度为0.8-2mm的冷钢板;
(6)通过热加工处理钢板以获得奥氏体嵌入马氏体基体中的双相显微组织,并以高于0.5℃/s的冷却速率将钢板冷却至室温,其中热加工路线包括在Ac3-20℃至Ac3+100℃的温度下等温保持钢板5-20分钟以形成部分或全部奥氏体,其中Ac3是铁素体完全转变为奥氏体的温度;和
(7)将钢板在300-400℃的温度下回火5-20分钟,并以高于0.5℃/s的冷却速率淬火至室温。
13.权利要求12所述的方法,其中,在步骤(7)中,淬火至室温后马氏体的体积分数为70%-90%。
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WO2019134102A1 (en) | 2019-07-11 |
EP3735479A4 (en) | 2021-07-28 |
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