CN114045440A - 汽车用具有抗氧化性的高强高塑热成形钢及热成形工艺 - Google Patents
汽车用具有抗氧化性的高强高塑热成形钢及热成形工艺 Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 133
- 239000010959 steel Substances 0.000 title claims abstract description 133
- 230000003647 oxidation Effects 0.000 title claims abstract description 37
- 238000007254 oxidation reaction Methods 0.000 title claims abstract description 37
- 238000000034 method Methods 0.000 title claims abstract description 36
- 230000008569 process Effects 0.000 title claims abstract description 29
- 239000000126 substance Substances 0.000 claims abstract description 10
- 229910052796 boron Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 7
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims description 20
- 229910001566 austenite Inorganic materials 0.000 claims description 16
- 239000000758 substrate Substances 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 14
- 229910000734 martensite Inorganic materials 0.000 claims description 10
- 230000000717 retained effect Effects 0.000 claims description 10
- 229910000859 α-Fe Inorganic materials 0.000 claims description 7
- 239000000203 mixture Substances 0.000 claims description 3
- 238000005422 blasting Methods 0.000 abstract description 11
- 238000004519 manufacturing process Methods 0.000 description 7
- 238000001556 precipitation Methods 0.000 description 6
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- 238000003723 Smelting Methods 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000005261 decarburization Methods 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000010301 surface-oxidation reaction Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
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- 238000005728 strengthening Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 229910000712 Boron steel Inorganic materials 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 230000003064 anti-oxidating effect Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
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- 230000003111 delayed effect Effects 0.000 description 1
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- 229910052742 iron Inorganic materials 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
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- 230000007847 structural defect Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000003856 thermoforming Methods 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
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Abstract
本发明提供一种汽车用具有抗氧化性的高强高塑热成形钢及热成形工艺,所述热成形钢的化学成分质量百分比如下:C:0.35%‑0.50%、Si:≤0.20%、Mn:1.50%‑2.50%、P:0.050%‑0.10%、S≤0.004%、Als:0.02%‑0.06%、Nb:0.03%‑0.07%、Ti:0.020%‑0.050%、V:0.08%‑0.15%、Cr:1.50%‑3.20%、Mo:0.10%‑0.30%、B:≤0.0040%、N≤0.005%,余量为Fe和不可避免杂质。本发明提供的热成形钢具有高抗氧化和高强高塑性,热成形时不需进行气氛保护,热成形后不需进行抛丸处理。
Description
技术领域
本发明涉及汽车用钢技术领域,具体而言是一种汽车用具有抗氧化性的高强高塑热成形钢及热成形工艺。
背景技术
近年来,随着车身用新材料不断研发并在车身上获得应用,但1000MPa以上级别的冷冲压用超高强钢板,受到易开裂和回弹大等问题的制约,往往用于制造形状简单的构件。而热成形钢采用热成形工艺在奥氏体区成形,回弹量较小,能够满足装配精度的要求,通过保压淬火可得到1500MPa级别及以上的超高强构件,有效的简化了车身结构和零部件设计,更大幅度的降低了车重。
目前,市场上热成形钢按表面状态可分为带涂层热成形钢和无涂层热成形钢,其中无涂层钢在加热炉中加热时易于在钢表面形成氧化铁皮,并发生脱碳情况,影响钢的性能,因此其在加热时需要采用保护气氛,同时在热成形后要进行喷丸处理,增加成本和工序;而涂层钢是在钢板表面带有一层铝硅涂层或锌基涂层,可以有效阻止钢在加热过程中的表面脱碳和氧化,且钢在热成形后可免除喷丸工序,但相对于无涂层钢,涂层热成形钢的成本较高。目前,现有技术大批量生产和使用的热成形钢的强度级别为1500MPa级,但其热成形后延伸率仅在6-9%左右,还没有一种较好的技术能够使热成形后钢在保持较低成本的同时解决表面氧化脱碳问题,并避免喷丸工序,同时热成形后钢还具有超高的强度和良好的塑性。
公开号为CN106811689B的专利中提出了一种抗拉强度≥2000MPa的热成形钢的制备方法,其热轧基板具有较低的强度和较高的延伸率,有利于热成形前的剪切落料,同时其热成形后钢板的抗拉强度可达到2000MPa以上,但其化学成分中Si含量较高,不利于获得良好的表面质量,同时仅采用传统热成形工艺,仍需要气体保护和喷丸,热成形后钢板的强度虽然较高,但其延伸率低于9%。
公开号为CN106119693B的专利中提出了一种用薄板坯直接轧制的抗拉强度≥2100MPa热成形钢及生产方法,钢板经冶炼、热轧和热成形工艺处理后,抗拉强度可达到2100MPa以上,但钢板的生产工艺及热成形工艺均采用传统工艺控制,且热成形后钢板的延伸率低于6%,不具备高强高塑的性能特点,更不满足免气体保护和免抛丸的全流程低成本工艺要求。
公开号为CN103255340B的专利中提出了一种汽车用高强韧性热成形钢板及其制备方法,钢板化学成分中C:0.1-0.5%,Si:0.5-1.5%,Mn:1.2-2.4%,Ti:0.01-0.05%,B:0.001-0.005%,S:≤0.01%,P:≤0.01%,热成形后钢板的抗拉强度达到1600MPa,延伸率达到16%,综合性能良好,且合金成本较低。但钢板需要在加热过程中进行变形,然后进行两次淬火,获得最终的组织和力学性能,其热成形工艺复杂,在现有设备上无法实现,同时其在进行加热时同样需要进行气体保护,热成形后需要进行喷丸处理。
综上,开发具有良好抗氧化性能的汽车用高强高塑热成形和热成形工艺具有良好的应用前景。
发明内容
根据上述技术问题,而提供一种汽车用具有抗氧化性的高强高塑热成形钢及热成形工艺。
本发明采用的技术手段如下:
一种汽车用具有抗氧化性的高强高塑热成形钢,所述热成形钢的化学成分质量百分比如下:C:0.35%-0.50%、Si:≤0.20%、Mn:1.50%-2.50%、P:0.050%-0.10%、S≤0.004%、Als:0.02%-0.06%、Nb:0.03%-0.07%、Ti:0.020%-0.050%、V:0.08%-0.15%、Cr:1.50%-3.20%、Mo:0.10%-0.30%、B:≤0.0040%、N≤0.005%,余量为Fe和不可避免杂质。
热成形钢的组织由铁素体、马氏体和残余奥氏体组成。
铁素体的体积分数为4%-10%、马氏体的体积分数为78%-90%、残余奥氏体的体积分数为6%-12%。
热成形钢的抗氧化速率≤0.1g/(m2·h),抗氧化性级别达到1级,抗拉强度≧2000MPa,屈服强度≧1400MPa,延伸率≥12.0%,钢的表面无完全脱碳,脱碳层厚度≤15μm,热成形钢的厚度为0.8mm-12.0mm。
本发明公开的热成形钢的成分主要作用为:
C:C是钢强度的保证,有利于增加钢的淬透性。碳含量过低,钢在热冲压后强度达不到预期目标;碳含量过高,热成形后钢的强度过高,塑性下降。除此以外,C含量的增加可以降低钢的相变温度,使奥氏体化温度降低,有利于获得免抛丸表面,同时,C含量增加有利于钢在热成形保压过程中产生足够含量的过冷奥氏体,提高塑性。因此本发明中C的最优范围为0.35%-0.50%。
Si:Si在钢中为无碳化物析出元素,对热成形冷却和保压过程中碳化物析出具有良好的抑制作用,进而保证残余奥氏体含量和稳定性。然而,Si含量过高会使热成形基板表面出现大量氧化铁皮、色差等缺陷,影响热成形部件表面质量,同时,过高的Si元素扩大两相区,提高奥氏体化温度,使钢在较高的温度进行保温,易于恶化钢的表面。因此本发明提出的Si的含量为≤0.20%。
Mn:Mn在本热成形钢中主要作用为提高钢的淬透性,降低相变温度,使钢在较低的温度进行奥氏体化得以实现;Mn含量过高会恶化钢的组织均匀性,易于使组织中出现严重的带状组织缺陷。因此本发明中选定Mn含量为1.50%-2.50%。
P:P在本热成形钢板中的作用与Si相似,能够抑制渗碳体生成,增加残余奥氏体稳定性;同时P能够使马氏体板条细化,且均匀分布,提高韧性。本发明中P含量为0.050%-0.10%。
S:S在本热成形钢中是有害元素,S会形成MnS夹杂,恶化钢板显微组织和力学性能,因此发明中限定S≤0.004%。
Als:Als(酸溶铝)在冶炼过程中起到脱氧定氮作用,但Als过多会导致大量的铝系夹杂。本发明中Als的范围为0.020%-0.060%。
Cr:Cr是提高钢淬透性元素,在本发明中,Cr元素的主要作用为提高钢的高温抗氧化性,同时提高钢的回火稳定性,保证钢在保压温度范围内不出现回火马氏体。最佳的Cr含量在1.50%-3.20%之间。
Mo:Mo是中强碳化物形成元素,能够提高钢的强度和韧性。本发明中,Mo能够降低马氏体转变温度,显著提高残余奥氏体稳定性,同时,Mo元素的添加增加了钢的抗氧化性。本发明中Mo含量为0.10%-0.30%。
Nb、V:Nb和V在钢中主要起细晶强化、析出强化等作用。在本发明中,两者通过纳米级细小碳化物弥散析出,能够有效钉扎原始奥氏体晶界,进而细化热成形后钢板中的各相组织,提高综合性能。同时,弥散析出的碳化物能够作为氢陷阱,钉扎钢中可扩散氢,提高抗延迟断裂性能。此外,V与N形成的VN析出可以抑制BN析出,避免因B析出导致的强度降低。本发明中Nb含量为0.030%-0.070%,V含量为0.080%-0.15%。
Ti:Ti在硼钢中主要用于固定氮,以保证硼的淬透效果得以发挥。此外,Ti还可与C元素性能细小碳化物析出,降低热成形后组织中马氏体的硬度和强度,有利于提高钢板塑性和韧性。本发明中Ti含量在0.020%-0.050%之间。
B:钢中加入硼能显著提高钢的淬透性,且在淬火后可以保证钢强度的稳定性。B含量过高易于与钢中的N形成B的化合物,降低钢板的性能。因此本发明中B含量为≤0.0040%。
N:N的含量越低越好,但过低会导致生产困难,增加成本,因此本发明中N含量≤0.005%。
本发明中,通过添加C、Mn、Cr、Mo等合金元素,降低奥氏体化温度,提高了钢的淬透性,有利于抑制钢的氧化,同时,降低了钢热成形后的临界冷却速率,可进行厚规格热成形钢的生产;另外,通过化学成分和热成形工艺配合,在空冷阶段获得一定含量的铁素体,并在冷却后的保压阶段获得一定含量稳定性较好的残余奥氏体,提高钢的塑性;成分中Si和P元素的添加,抑制了碳化物析出,保证了钢中残余奥氏体含量,提高了钢的力学性能;另外,钢成分中的Cr、Mo元素起到抗氧化作用,使钢可以在无保护气氛条件下进行加热和保温,热成形后可以不经喷丸直接进行后续工序生产。
本发明还公开了一种汽车用具有抗氧化性的高强高塑热成形钢的热成形工艺,包括如下步骤:
(1)将含有上述成分的热成形基板放入到温度为AC3-AC3+30℃的加热炉中进行加热及保温,保温时间为180s-300s;目的为使热成形基板完全奥氏体化,并使其具有较小的原始奥氏体晶粒尺寸。同时,较低的奥氏体化温度有利于减轻热成形基板表面氧化;
(2)将加热后的热成形基板由加热炉中取出进行空冷,空冷至Ar3温度后停留3s-5s后放入到热成形模具中进行变形和冷却,冷却速度≥10℃/s,冷却至250℃-300℃后进行保压,保压时间为60s-90s,保压后将成形的部件取出空冷至室温,得到热成形钢。
上述热成形基板是经冶炼、热轧和冷轧后获得。冶炼的成分及其质量百分比为上述一种汽车用具有抗氧化性的高强高塑热成形钢的成分及其质量百分比。
本发明提供钢板在进行热成形时不需进行气氛保护,热成形后不需进行抛丸处理,可直接进行后续工序,其全流程成本低于目前热成形产品。
较现有技术相比,本发明具有以下优点:
(1)通过本发明提供的化学成分和热成形工艺配合,获得高强高塑热成形钢,钢的抗拉强度≧2000MPa,延伸率达到并超过12%;
(2)通过添加Cr元素,提高钢板高温抗氧化性能,钢板抗氧化速率≤0.1g/(m2·h),抗氧化性级别达到1级,钢板在进行热成形时不需进行气氛保护,热成形后不需进行抛丸处理,可直接进行后续工序;
(3)提出的热成形钢和热成形工艺在现有设备上可以实现,无需进行设备改造,且成本较低。
基于上述理由本发明可在汽车用钢等领域广泛推广。
具体实施方式
需要说明的是,在不冲突的情况下,本发明中的实施例及实施例中的特征可以相互组合。所描述的实施例仅仅是本发明一部分实施例,而不是全部的实施例。以下对至少一个示例性实施例的描述实际上仅仅是说明性的,决不作为对本发明及其应用或使用的任何限制。基于本发明中的实施例,本领域普通技术人员在没有做出创造性劳动前提下所获得的所有其他实施例,都属于本发明保护的范围。
本发明提供了一种汽车用具有抗氧化性的高强高塑热成形钢,热成形钢的化学成分质量百分比如下:C:0.35%-0.50%、Si:≤0.20%、Mn:1.50%-2.50%、P:0.050%-0.10%、S≤0.004%、Als:0.02%-0.06%、Nb:0.03%-0.07%、Ti:0.020%-0.050%、V:0.08%-0.15%、Cr:1.50%-3.20%、Mo:0.10%-0.30%、B:≤0.0040%、N≤0.005%,余量为Fe和不可避免杂质。
热成形钢的组织由铁素体、马氏体和残余奥氏体组成。
铁素体的体积分数为4%-10%、马氏体的体积分数为78%-90%、残余奥氏体的体积分数为6%-12%。
热成形钢的抗氧化速率≤0.1g/(m2·h),抗氧化性级别达到1级,抗拉强度≧2000MPa,屈服强度≧1400MPa,延伸率≥12.0%,钢的表面无完全脱碳,脱碳层厚度≤15μm,热成形钢的厚度为0.8-12.0mm。
本具体实施方式中提出的抗氧化性能优良的高强热成形钢经冶炼、热轧和冷轧后,获得热成形基板,热成形基板的厚度为0.8mm-12.0mm。然后进行热成形工艺处理,热成形工艺具体包括以下步骤:
(1)将热成形基板放入到温度为AC3-AC3+30℃的加热炉中进行加热及保温,保温时间为180s-300s;目的为使热成形基板完全奥氏体化,并使其具有较小的原始奥氏体晶粒尺寸。同时,较低的奥氏体化温度有利于减轻热成形基板表面氧化;
(2)将加热后的热成形基板由加热炉中取出进行空冷,空冷至Ar3温度后停留3s-5s后放入到热成形模具中进行变形和冷却,冷却速度≥10℃/s,冷却至250℃-300℃后进行保压,保压时间为60s-90s,保压后将成形的部件取出空冷至室温,得到热成形钢。
本发明的实施例的具体成分、热成形工艺参数及热成形后钢的组织和性能见表1~3。
表1本发明实施例的化学成分(wt,%)
表2本发明实施例的热成形工艺
表3本发明实施例的组织及性能参数
本具体实施方式中通过新型化学成分和热成形工艺配合,获得高强高塑热成形钢,钢的抗拉强度≥2000MPa,延伸率≥12%;通过添加Cr、Mo等元素,提高钢的抗氧化性能,钢抗氧化速率≤0.1g/(m2·h),抗氧化性级别达到1级,钢在进行热成形时不需进行气氛保护,热成形后不需进行抛丸处理,可直接进行后续工序;而且提出的钢板和热成形工艺全流程成本低于目前热成形部件生产成本,且在现有设备上可以实现,无需进行设备改造。
最后应说明的是:以上各实施例仅用以说明本发明的技术方案,而非对其限制;尽管参照前述各实施例对本发明进行了详细的说明,本领域的普通技术人员应当理解:其依然可以对前述各实施例所记载的技术方案进行修改,或者对其中部分或者全部技术特征进行等同替换;而这些修改或者替换,并不使相应技术方案的本质脱离本发明各实施例技术方案的范围。
Claims (10)
1.一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述热成形钢的化学成分质量百分比如下:C:0.35%-0.50%、Si:≤0.20%、Mn:1.50%-2.50%、P:0.050%-0.10%、S≤0.004%、Als:0.02%-0.06%、Nb:0.03%-0.07%、Ti:0.020%-0.050%、V:0.08%-0.15%、Cr:1.50%-3.20%、Mo:0.10%-0.30%、B:≤0.0040%、N≤0.005%,余量为Fe和不可避免杂质。
2.根据权利要求1所述的一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述热成形钢的组织由铁素体、马氏体和残余奥氏体组成。
3.根据权利要求2所述的一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述铁素体的体积分数为4%-10%、所述马氏体的体积分数为78%-90%、所述残余奥氏体的体积分数为6%-12%。
4.根据权利要求1所述的一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述热成形钢的抗拉强度≧2000MPa。
5.根据权利要求1所述的一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述热成形钢的抗氧化速率≤0.1g/(m2·h)。
6.根据权利要求1所述的一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述热成形钢的屈服强度≧1400MPa。
7.根据权利要求1所述的一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述热成形钢的延伸率≥12.0%。
8.根据权利要求1所述的一种汽车用具有抗氧化性能的高塑热成形钢,其特征在于,所述热成形钢的表面无完全脱碳,脱碳层厚度≤15μm。
9.根据权利要求1所述的一种汽车用具有抗氧化性的高强高塑热成形钢,其特征在于,所述热成形钢的厚度为0.8mm-12.0mm。
10.一种汽车用具有抗氧化性的高强高塑热成形钢的热成形工艺,其特征在于,包括如下步骤:
(1)将含有权利要求1~9任一权利要求所述成分的热成形基板放入到温度为AC3-AC3+30℃的加热炉中进行加热及保温,保温时间为180s-300s;
(2)将加热后的热成形基板由加热炉中取出进行空冷,空冷至Ar3温度后停留3s-5s后放入到热成形模具中进行变形和冷却,冷却速度≥10℃/s,冷却至250℃-300℃后进行保压,保压时间为60s-90s,保压后将成形的部件取出空冷至室温,得到所述热成形钢。
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CN109972061A (zh) * | 2019-04-26 | 2019-07-05 | 北京科技大学 | 热冲压成形用抗氧化超高强钢板及其低温热成形工艺 |
CN110643909A (zh) * | 2019-04-26 | 2020-01-03 | 北京科技大学 | 热冲压成形用抗氧化超高强钢板及其低温热成形工艺 |
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