CN101842509A - 用于改进具有高抗拉强度的镀锌钢的成形性的方法及设备 - Google Patents
用于改进具有高抗拉强度的镀锌钢的成形性的方法及设备 Download PDFInfo
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- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 21
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 21
- 238000000034 method Methods 0.000 title claims abstract description 20
- 238000001816 cooling Methods 0.000 claims abstract description 49
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 23
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 21
- 238000010791 quenching Methods 0.000 claims abstract description 8
- 230000015572 biosynthetic process Effects 0.000 claims abstract description 5
- 229910000831 Steel Inorganic materials 0.000 claims description 45
- 239000010959 steel Substances 0.000 claims description 45
- 229910001566 austenite Inorganic materials 0.000 claims description 17
- 238000005496 tempering Methods 0.000 claims description 14
- 229910052799 carbon Inorganic materials 0.000 claims description 13
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 12
- 229910000885 Dual-phase steel Inorganic materials 0.000 claims description 12
- 239000011701 zinc Substances 0.000 claims description 12
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 9
- 229910052725 zinc Inorganic materials 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 8
- 230000000171 quenching effect Effects 0.000 claims description 5
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Abstract
本发明涉及生产具有改进的成形性同时保持高抗拉强度的两相镀锌钢带的方法和设备。本发明包括冷却步骤和再加热步骤。在冷却步骤中，镀锌钢带具有从约300℃到约150℃-250℃的温度降低。该冷却步骤应冷却到初始温度和最终温度之间的差值的最大值为约150℃的程度。该冷却可以通过热水淬火实现，或使用冷却塔或其他方式。再加热步骤应跟随冷却步骤。再加热步骤应将镀锌钢带加热到约340℃-390℃的温度。该再加热造成镀锌钢带中的马氏体在相对低的温度回火，这降低了GI涂层中Fe-Zn相的形成。
Description
背景技术
技术领域
本发明涉及要求高抗拉强度同时保持良好成形性(formability)以及点焊(spot welding)所需性能的镀锌热浸两相钢(galvanized hot dip dual-phase)的制造。
现有技术说明
在现有技术中，具有约650MPa及更低的抗拉强度的两相钢典型地具有良好的加工性能，包括成形性和点焊性。因而，其剪切因子没有限制设计属性。然而，抗拉强度高于约700MPa，比如800MPa(被称为DP800钢)的两相钢可能就不具备良好的加工性能了。
因此工业中对所谓的TRIP级的钢很感兴趣，其具有高抗拉强度同时有良好的成形性，其典型地需要较高的碳含量，例如高于约0.15％，以产生足够量的残余奥氏体。残余奥氏体的碳含量典型地高于约1.2％以在室温下达到稳定。然而，钢合金的这种高碳含量使得不可能达到正常的点焊要求从而满足工业标准。生产具有800MPa抗拉强度同时具有接近DP600标称钢的成形性及焊接性的两相钢的目标到目前为止还是未能实现的。
800MPa两相钢的其它现有技术限制因素包括降低的弯曲性能(其要求更大的弯曲半径)以及由于局部硬马氏体岛形成而减小的扩孔比。
由于钢板的剪切因子，存在着设计局限。已经注意到，DP800的临界R/T＝8，DP600的临界R/T＝4，从而使得某些设计成功地形成。因而，DP800的更低的R/T值会利于制造设计能力并降低材料定标(material gauging)，伴随着节省重量的机会和降低相关成本。在热浸镀锌生产线(从锌浴温度直接空气冷却到环境室温)中使用不同的合金化钢化学来制备贫合金化的(可点焊的)、可成形的DP800级钢是不可能达到所述成形要求的，这是由于硬的马氏体相在这种传统冷却配置期间形成。
现有技术文献已确定在大约300℃的时效/回火期间形成的较软的马氏体将提高两相钢的弯曲和扩孔性能。因此，对在连续的退火线中所产生的马氏体材料进行回火得到良好的弯曲性能，甚至在含85％的软马氏体的DP980钢中也是如此，而含大约70％的硬马氏体的DP980则与此相反。
发表于1967年的文献(K.R.Kinsman等)中还提到了奥氏体经由奥氏体的位错钉扎获得的热稳定化会产生更多的残余奥氏体。在新形成的马氏体的存在下，由于和界面位错相关的未松弛的应变，碳的化学势在马氏体中、奥氏体中以及界面边界中不同。在时效/再加热期间，碳活性和碳浓度趋于平衡发生调整。
相应的，当钢带快速从300℃冷却到接近M50温度(约50％的奥氏体将形成马氏体)的约250℃。其后，钢带被再加热至高于350℃的时效温度。在时效期间，碳被认为向着包围马氏体核的位错界面处偏析足以钉扎住奥氏体。
B.Cooman和J.Speer早在2006年披露了淬火和配分(partitioning)将增加延展性，这是由于板条间奥氏体(interlath austenite)的有益作用，所述板条间奥氏体是延展性的、韧性的成分。典型地，具有多于8％的残余奥氏体的级别的钢被称为TRIP钢。碳的当量可以由以下等式定义：
C.E.(碳当量)＝C-％+Si-％/30+Mn-％/20+2P-％+4S-％
由于点焊要求C.E.＜0.25％，那么DP800的钢基体碳含量应当低；最大0.10％。这意味着对于图4所示的常规热循环而言，Mn-eq值非常高＞2.7％。因此，对于这样高的Mn％，得到优良的涂层是很难的。Mn合金化的量可以通过每份配方加入0.2％的Mo降低到～2.2％；
Mn-eq＝Mn-％+Cr-％+2.6Mo-％
使用新的镀锌技术，常规技术的涂覆性问题明显地得到消除，淬火另外消除图4中所示的对0.2％Mo合金化的需要。
发明内容
本发明涉及制备具有改进的成形性同时保持高抗拉强度的两相镀锌钢带的方法和设备。利用在热浸镀锌带生产线的锌罐(zinc pot)之后在改进的冷却塔构造和方法中在多个再加热站之间增加的保持温度和时间，获得了所述改善的性能。本发明与现有技术相比包括附加的冷却步骤和附加的再加热步骤。在冷却步骤中，镀锌钢带具有从约300℃到约150℃-250℃的温度降低。该冷却步骤应当冷却至初始温度与最终温度之间相差约150℃的最大程度。可以通过水淬火实现这种冷却，或者使用冷却塔或其他方式来实现这种冷却。再加热步骤应该在冷却步骤之后。再加热步骤应该将镀锌钢带加热到约340℃-390℃的温度。所述再加热使得镀锌钢带中的马氏体在相对低的温度下回火，这样减少了在GI涂层中Fe-Zn相的形成。
附图说明
图1所示的是为了生产具有增强的成形性能的热浸镀锌两相钢，钢带在改进的APC冷却塔中回火和配分的生产线构造流程示意图。
图2是用于钢带热浸镀锌处理中的现有技术冷却塔的生产线构造流程示意图。
图3是本发明的DP800/1000-GI“软马氏体”的时间温度曲线图。
图4是现有技术中控制“硬马氏体”的两相热循环的时间温度曲线图。
图5是本发明实施例中TRIP辅助DP800GI的时间温度曲线图。
图6是不同回火温度(摄氏度)和马氏体硬度的关系曲线图。
发明详细说明
现在参见图1，可以看到本发明改进的冷却塔10的构造和相关方法，以给离开锌罐12的热浸镀锌两相钢带提供回火和配分。冷却塔10具有足够的高度以产生将在下文揭示的本发明的方法中所必须的所需处理和保持时间。冷却塔10构造提供了增加的转移处理回路13。气体喷射冷却器29和30、浸泡部分31和感应加热器32都是现有技术中公知的。
图2公开的是现有技术的传统单冷却回路。传统的冷却塔14只能在锌罐16后提供连续的空气冷却。唯一的感应加热器17用于GA涂覆的产品而不是GI涂覆的产品。同样，在所述单冷却回路的第一程(pass)中，镀锌钢带18会随后穿过GA的浸泡部分19(而不是用于GI的)和气体喷射冷却站20。在回程中，提供，第二套气体喷射冷却器21，这是本领域技术人员所公知和理解的。
相比之下，图1公开了根据本发明的的冷却塔10，其包括另外的处理回路13，该回路允许两个额外的处理程。具有回向辊23A和23B的热水淬火22位于所述回路的第一程的开始处。镀锌钢带11以大约低于300℃进入该水淬火22，水淬后出去是150℃到250℃，最大冷却为150℃。在另一方案中，如果冷却塔的高度超过了50米，那么该热水淬火可以避免或除去。
图1还公开了第一感应再加热器24，用于加热镀锌钢带11至340℃-390℃。在软马氏体两相钢的制备中，所有的奥氏体随后通过热水淬火22或通过高冷却塔在低于Mf温度的温度冷却而完全转化为马氏体。因此，如图所示的通过再加热镀锌带11，镀锌带的马氏体在这样的低温下回火：由于感应加热的是钢而不是涂层，所以所述低温使GI涂层中Fe-Zn相的形成最小化。
图6公开了回火和马氏体硬度的关系，其显示了基于处理箭头所示的温度马氏体的硬度从高于500HV降低到低于350HV，如同通过控制温度所需的。
本发明还提供了任选的冷却站25，位于处理回路13底部处在一对回向辊26的紧前面，可以用于在特定的应用中，其内使用空气/水雾，将镀锌钢带11从低于320℃冷却到低于200℃。第二感应加热站27在第二回程的开始处，用于加热镀锌带11至所需的340℃-390℃。所述处理回路13的第二回程在位于冷却塔回路顶部的第三组回向辊28之前提供了另外了的用于空冷镀锌钢带11的时间，并且引导所述钢带11穿过一组用于进一步温度降低的常规气体喷射冷却器29并在30处最终成卷。
现在参看图5所示图形，可以看出所谓TRIP辅助两相钢的制备，其中在锌罐12后需要热处理来冷却钢带S到约250℃(低于M50)然后为了配分再加热到低于380℃。在时间箭头所示的配分期间，碳从马氏体核向奥氏体扩散并钉扎(稳定化)住奥氏体，从而得到残余奥氏体。然而，应当注意到，具有点焊性的两相钢的碳当量应该低(小于0.25％)，当具有这样的C.E.量时，残余奥氏体可以为从4％到8％，这将有助于将这些钢级别定义为TRIP辅助DP800而不是TRIP钢。
因此，看出在本发明的改进下，转移处理回路13的增加(不同于传统冷却塔14的构造)使得与现有技术中当前存在的单回路传统路程相比，可以对热浸镀锌钢带11进行另外的多次处理。发现如下的增加将使得DP600级钢的已得到的成形性属性发生到理想的高抗拉强度级DP800级钢上，从而有助于满足工业中所需的成形性和焊接要求：在处理回路13的第一程的开始处22热水淬火、随后用感应再加热器24的第一次再加热、在第一程中在25处用于任选的空气/水雾冷却的时间、以及在第二程中用感应加热站27的第二次再加热。
由此，看出用于两相钢的新的、新颖的冷却塔和方法被举例说明和描述，对本领域技术人员而言显然在不脱离本发明的精神内可能做出各种对其的更改和改变。
Claims (18)
1.制备镀锌钢带的方法，包括步骤：
(1)在锌罐中浸渍钢带，然后，
(2)第一次冷却所述钢带到约250℃至约400℃的温度，然后，
(3)第二次冷却所述钢带到约150℃至约250℃的温度，然后，
(4)第一次再加热所述钢带到约340℃至约390℃的温度。
2.根据权利要求1所述的方法，其中所述第二次冷却包括热水淬火所述钢带。
3.根据权利要求1所述的方法，其中所述第二次冷却包括所述钢带穿过高于50米的冷却塔。
4.根据权利要求1所述的方法，其中所述第一次冷却将所述钢带冷却到大约低于300℃的温度，所述第二次冷却将所述钢带冷却到约150℃的温度。
5.根据权利要求1所述的方法，还包括步骤：
(5)在所述第一次再加热后的第三次冷却，其中所述第三次冷却将所述钢带冷却到约低于320℃到约低于200℃的温度，然后，
(6)第二次再加热所述钢带到约340℃到约390℃的温度，
以及，其中所述第一次再加热是加热到低于约380℃的温度。
6.制备镀锌钢带的方法，包括步骤：
(1)在锌罐中浸渍钢带，然后，
(2)冷却所述钢带到低于Mf温度的温度，然后，
(3)加热所述钢带以在最小化Fe-Zn形成的温度进行回火。
7.根据权利要求6所述的方法，其中所述回火将马氏体硬度降至低于500HV。
8.根据权利要求7所述的方法，其中所述回火将马氏体硬度降至低于350HV。
9.根据权利要求6所述的方法，其中所述回火是在约160℃至约330℃的温度。
10.根据权利要求7所述的方法，其中所述回火是在约160℃至约330℃的温度。
11.制备镀锌钢带的设备，包括
(1)适合于处理钢带的锌罐，其下游为，
(2)适合于冷却所述钢带到约300℃至约400℃的温度的第一冷却器，其下游为，
(3)适合于冷却所述钢带到约150℃至约250℃的温度的第二冷却器，其下游为，
(4)适合于再加热所述钢带到约340℃至约390℃的温度的第一再加热器。
12.根据权利要求11所述的设备，其中所述第二冷却器包括热水淬火设备。
13.根据权利要求11所述的设备，其中所述第二冷却器包括高于50米的冷却塔。
14.根据权利要求11所述的设备，其中所述第一冷却器适合于冷却所述钢带到大约低于300℃的温度，且所述第二冷却器适合于冷却所述钢带到约150℃的温度。
15.根据权利要求11所述的设备，进一步包括
(5)位于所述第一再加热器下游的第三冷却器，其中所述第三冷却器适合于冷却所述钢带到从约低于320℃至约低于200℃的温度，其下游为，
(6)适合于加热所述钢带到从约340℃至约390℃的温度的第二再加热器，
以及，
其中所述第一再加热器适合于加热所述钢带到低于约380℃的温度。
16.镀锌钢带，包含具有低于约0.25％的碳当量以及约4％至约8％的残余奥氏体的TRIP辅助钢。
17.根据权利要求16所述的镀锌钢带，其中所述钢带不含Mo。
18.镀锌钢带，包含两相钢，其中所述钢带不含奥氏体。
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| US96798407P | 2007-09-10 | 2007-09-10 | |
| US60/967,984 | 2007-09-10 | ||
| PCT/US2008/010509 WO2009035576A1 (en) | 2007-09-10 | 2008-09-09 | Method and apparatus for improved formability of galvanized steel having high tensile strength |
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| US (1) | US20090065103A1 (zh) |
| EP (1) | EP2198067A4 (zh) |
| CN (1) | CN101842509A (zh) |
| BR (1) | BRPI0816738A2 (zh) |
| CA (1) | CA2699146A1 (zh) |
| MX (1) | MX2010002581A (zh) |
| RU (1) | RU2010114212A (zh) |
| WO (1) | WO2009035576A1 (zh) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102676967A (zh) * | 2012-04-09 | 2012-09-19 | 安徽赛远薄钢科技有限公司 | 一种热镀锌系统中冷却装置 |
| CN103952653A (zh) * | 2014-04-18 | 2014-07-30 | 河北钢铁股份有限公司 | 热冲压成形钢用抗高温氧化镀层材料以及热浸渡工艺 |
| TWI560279B (en) * | 2013-05-17 | 2016-12-01 | Ak Steel Properties Inc | High strength steel exhibiting good ductility and method of production via in-line heat treatment downstream of molten zinc bath |
| KR20220032632A (ko) * | 2019-07-22 | 2022-03-15 | 난징고광반도체재료유한회사 | 전자 수송 물질 및 이를 이용한 유기 전계 발광 소자 |
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| DE102012100509B4 (de) * | 2012-01-23 | 2015-10-08 | Thyssenkrupp Rasselstein Gmbh | Verfahren zum Veredeln einer metallischen Beschichtung auf einem Stahlband |
| WO2016001702A1 (en) | 2014-07-03 | 2016-01-07 | Arcelormittal | Method for producing a high strength coated steel sheet having improved strength, ductility and formability |
| WO2016001700A1 (en) | 2014-07-03 | 2016-01-07 | Arcelormittal | Method for producing a high strength steel sheet having improved strength, ductility and formability |
| WO2016001706A1 (en) | 2014-07-03 | 2016-01-07 | Arcelormittal | Method for producing a high strength steel sheet having improved strength and formability and obtained sheet |
| WO2016001710A1 (en) * | 2014-07-03 | 2016-01-07 | Arcelormittal | Method for producing a high strength coated steel having improved strength and ductility and obtained sheet |
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- 2008-09-09 RU RU2010114212/02A patent/RU2010114212A/ru not_active Application Discontinuation
- 2008-09-09 BR BRPI0816738 patent/BRPI0816738A2/pt not_active IP Right Cessation
- 2008-09-09 MX MX2010002581A patent/MX2010002581A/es unknown
- 2008-09-09 WO PCT/US2008/010509 patent/WO2009035576A1/en active Application Filing
- 2008-09-09 CA CA2699146A patent/CA2699146A1/en not_active Abandoned
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102676967A (zh) * | 2012-04-09 | 2012-09-19 | 安徽赛远薄钢科技有限公司 | 一种热镀锌系统中冷却装置 |
| TWI560279B (en) * | 2013-05-17 | 2016-12-01 | Ak Steel Properties Inc | High strength steel exhibiting good ductility and method of production via in-line heat treatment downstream of molten zinc bath |
| TWI627288B (zh) * | 2013-05-17 | 2018-06-21 | Ａｋ鋼鐵資產公司 | 展現良好延展性之高強度鋼及藉由熔融鋅浴槽的下游在線熱處理之製造方法 |
| CN103952653A (zh) * | 2014-04-18 | 2014-07-30 | 河北钢铁股份有限公司 | 热冲压成形钢用抗高温氧化镀层材料以及热浸渡工艺 |
| KR20220032632A (ko) * | 2019-07-22 | 2022-03-15 | 난징고광반도체재료유한회사 | 전자 수송 물질 및 이를 이용한 유기 전계 발광 소자 |
| KR102489676B1 (ko) | 2019-07-22 | 2023-01-18 | 난징고광반도체재료유한회사 | 전자 수송 물질 및 이를 이용한 유기 전계 발광 소자 |
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| Publication number | Publication date |
|---|---|
| BRPI0816738A2 (pt) | 2015-03-17 |
| EP2198067A1 (en) | 2010-06-23 |
| MX2010002581A (es) | 2010-04-30 |
| WO2009035576A1 (en) | 2009-03-19 |
| US20090065103A1 (en) | 2009-03-12 |
| RU2010114212A (ru) | 2011-10-20 |
| CA2699146A1 (en) | 2009-03-19 |
| EP2198067A4 (en) | 2011-10-05 |
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