CN1436252A - 镀锌层扩散退火处理的金属薄板和其制备方法 - Google Patents
镀锌层扩散退火处理的金属薄板和其制备方法 Download PDFInfo
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- 239000011701 zinc Substances 0.000 title claims abstract description 79
- 229910052725 zinc Inorganic materials 0.000 title claims abstract description 72
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 title claims abstract description 71
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Abstract
本发明涉及一种制备镀锌层扩散退火处理的金属薄板的方法,其中,由含硅0.01-0.1wt.%的IF钢制备出热轧带;在不低于700℃但不高于750℃的卷取机温度下卷取热轧带;由所述卷取的热轧带轧制成冷轧带;在退火炉中,退火气氛下,对冷轧带进行再结晶退火;在锌镀液中,在已退火的冷轧带上形成锌镀层;以及,在不低于500℃但不高于540℃的镀锌层扩散退火处理温度下对所述镀覆冷轧带进行后退火。本发明也涉及一种镀层与基体材料间的结合性能得到改善的镀锌层扩散退火处理的金属薄板,而且,还提出了一种适于制备具有这种性能的金属薄板的方法。
Description
本发明涉及镀锌层扩散退火处理的金属薄板的制备方法,所述金属薄板由IF钢制成。根据通常的理解,可以认为“镀锌层扩散退火处理的金属薄板”是以卷材或半成品形式销售的热镀锌金属薄板,它们在热镀之后已进行退火处理。采用这种“镀锌层扩散退火处理”的方法在金属薄板基体材料上形成的镀层通常仅仅包含铁-锌化合物。
术语“IF(无间隙)钢”可认为是不存在间隙溶解的合金组元的钢,除了可能要求的其它合金组元之外,所述合金组元包括硅以及附加含量的用于去除C和N原子的钛和/或铌。这种钢的特征在于其屈服点低,因而具有良好的冷成形性,特别适合于深度拉拔的部件。
由IF钢制成的镀锌层扩散退火处理的金属薄板尤其可用于制造汽车车身。在这种情况下,不仅对基体材料,而且对基体材料上的镀层的成形性要求极高。实践表明:采用传统方法制备镀锌层扩散退火处理的金属薄板时,压制工具的磨损较大。这种磨损很大程度上取决于钢的组成以及钢的制备条件,而与具体成性条件的影响无关。所述钢的制备条件直接影响镀层的相结构,因此也就直接影响其表面状况、均匀性以及镀层与基体金属的结合强度。
在用于制备所述及的镀锌层扩散退火处理的金属薄板的IF钢中添加最多0.1wt.%的硅是为了改善锌镀层在基体材料上的结合性能。硅合金化能够获得更高的晶界占有率。在成型期间,所述晶界作为能够阻止镀层进一步脱落的“预置开裂点”发生剪切和成型。
然而,硅合金化会降低基体材料的机械性能,并且因此降低其成形性。例如,已证实:当硅含量增加0.01wt.%时,材料的强度下降1N/mm2。
其它研究已发现:当镀锌层扩散退火处理的金属薄板采用含硅量很低如0.012wt.%的IF钢制备且同时镀层中的铁含量为7-12wt.%时,镀层与基体材料的结合很差。当镀层中铁含量较高且镀液中铝含量较高时,能够在用于支撑镀层与基体金属的结合的钢/镀层界面处观察到齿形结构。
然而,实际上,通过提高镀液中铝含量或提高镀层中铁的分数不能改善镀层与基体材料的结合性能。这是因为镀液中铝含量高会导致在镀锌层扩散退火处理反应中合金化明显迟缓。这种迟缓只有通过提高炉温和延长炉内传输时间来弥补。这两种措施均会提高运行成本,降低经济效率和加大炉体磨损。
另外,只有通过提高镀锌层扩散退火处理温度和/或延长保温时间,才能够提高镀层中的Fe含量。这样的结果是镀层中含有清晰可辨的γ相层。该γ相层然后与强度高的基体金属结合。然而,所述γ相层与其上存在的厚得多的δ相层之间的结合强度较差。结果,在相应的加载期间,厚δ相层会发生剥落,因此,磨损增大,而且,也不能确保所要求的镀层对基体材料的保护作用。
由例如DE 198 22 156 Al可基本了解对这种方法的最初介绍。在所述已知方法中,由IF钢热轧出热轧带,再卷取并轧制成冷轧带。然后,在退火炉中对冷轧带进行再结晶退火,最后,在锌镀液中形成锌镀层。
本发明的目的是形成一种镀层与基体材料间的结合性能得到改善的镀锌层扩散退火处理的金属薄板,以及提供一种适于制备具有所述质量的金属薄板的方法。
基于上述现有技术,一方面,采用一种制备镀锌层扩散退火处理的金属薄板的方法,这一问题得以解决。所述方法中包括:由含硅0.01-0.1wt.%的IF钢制备出热轧带;在不低于700℃但不高于750℃的卷取机温度下卷取热轧带;由所述卷取的热轧带轧制成冷轧带;在退火炉中,退火气氛下,对冷轧带进行再结晶退火;在锌镀液中在已退火的冷轧带上形成锌镀层;以及在不低于500℃但不高于540℃的镀锌层扩散退火处理温度下对所述镀锌冷轧带进行退火。
在根据本发明的步骤中,对各步骤的参数进行调整,以使基体材料“IF钢”的机械性能与镀覆在基体材料上的镀层性能相互之间实现最佳匹配。这样,就能够获得满足极高要求并且适于在成形期间承受极高应力的镀锌层扩散退火处理的金属薄板。
本发明基于如下认识:热轧带以及冷轧带表面的氧化状态对硅改善镀层结合性能的作用影响显著。所述氧化状态在镀锌开始阶段影响Zn/Fe相形成动力学。如果该相形成缓慢,则会在钢基体材料与镀层交界处形成一种基体材料与镀层相互之间紧密嵌入的结构。这种齿形结构的形成能显著提高镀层与基体材料间的结合性能。
另外,通过形成锯齿状的镀层可以提高结合性能。这种形式的镀层也促进镀层在基体材料上的结合。
热力学分析表明:在Zn镀液中溶解Al能够减少近表面处的氧化物。在这种情况下,部分可用铝不会促进Fe-Al阻挡层的形成。相反,该阻挡层的形成受到削弱,而Fe/Zn相反应加剧。
除了这一直接效应之外,氧化物粒子也影响钢表面结构再结晶的次序。这是因为细小的氧化物即使没有完全抑制再结晶的发生,但也具有阻碍再结晶的作用。在这一点上,钛的氧化物尤其有效。由于再结晶受到阻碍,结果出现细晶粒或者完全重复的结构。由于晶粒尺寸、晶界扩散能力和组织的作用,所述结构进而影响Fe-Al阻挡层的有效性。这样,重复或者细晶粒的结构加速所述相反应,而粗大、再结晶的结构却具有阻碍作用。
在内部氧化之后,大量细小氧化物渗透进入表面一定深度。这些细小氧化物以一种不希望的方式直接或间接地加速所述相反应,从而影响镀层的性能。已经证实:在热轧带中的鳞皮下就已发生内部氧化,而且,对热轧带酸洗也未将其去除。
除了对钢基体材料结构产生的副作用之外,内氧化对镀层的均匀性也有不利影响。其中,镀层的斑纹由内部氧化物的横向分布决定。
卷取机温度对内氧化的形成有重要影响。借助根据本发明的卷取机温度优选范围,能够有效避免内氧化的形成。因此,镀层的磨损特性以及镀锌层扩散退火处理的金属薄板的机械性能直接受卷取机温度影响。在这方面,实际实验中已发现:如果卷取机温度不低于710℃但不高于740℃,则能获得特别好的性能。
根据相应的硅含量,可以进一步限制卷取机的最佳温度范围。可允许的最低卷取机温度应不低于720℃,而该温度范围的上限仍然是740℃。已发现:在所有情况下,用于制备基体材料的IF钢的硅含量为0.03-0.08wt.%,卷取机温度为710℃或720℃,最高740℃时,能够制备出具有特别良好的磨损特性以及优异的机械性能的镀锌层扩散退火处理的金属薄板。
因为在某些情况下,内氧化仅仅在镀锌之前进行的退火期间开始,这与钢基体材料的组成或生产条件有关,所以,如果退火气体的露点处于比较高的温度范围则很不利。退火气体的露点较高会促进所不希望的内氧化发生。
同时,应该注意:钢基体材料的外氧化会导致在钢表面处形成有利于镀层结合性能的较大颗粒。为了在冷轧带退火期间形成大颗粒,必须抑制热轧带在退火期间发生内氧化。因此,本发明中设定退火气体具有低的露点。所以,根据本发明设定构成再结晶退火气氛的退火气体的露点为-20~-60℃,其中,在进一步的优化方案中,所述露点为-25~-40℃。
在氧化物形成方面,还应该注意:镀锌之前冷轧带表面的氧化状态对镀层的粗糙度、结合性能和均匀性均有明显影响。这里,必须注意氧化颗粒的直接影响与间接影响之间的差别。例如,钛的氧化物显著影响锌镀层的均匀性和粗糙度以及结构和组织,而Si的氧化物直接影响镀层与基体材料的结合性能。如果在镀锌之前的外氧化过程中,钢基体材料中存在的硅合金元素能够扩散到表面,则其仅仅对镀层的结合性能有有利作用。
在前述条件下退火的冷轧带优选在退火过程中通过铝含量为0.1-0.14wt.%的锌镀液。在Zn熔体中添加所述量的Al有利于在钢基体层与镀层件的过渡区附近形成所要求的齿形结构。这里,如必要,可以进行进一步优化,例如,锌镀液中含有0.105-0.125wt.%的铝。
在本发明的一个使制备结果同样优化的进展中,镀锌层扩散退火处理温度可以为510-530℃。
根据本发明的镀锌层扩散退火处理的金属薄板的制备步骤能够获得一种镀锌层扩散退火处理的产品,该产品中,在钢基体材料与镀层交界区形成有一种齿形结构,通过该结构可确保基体材料与镀层之间紧密结合。这种紧密结合确保镀层与钢基体材料牢固结合,结果,能够获得机械性能特别优异,同时磨损程度降至最低的金属薄板。
关于金属薄板,前述问题已被一种镀锌层扩散退火处理的金属薄板解决,所述镀锌层扩散退火处理的金属薄板的基体材料由IF钢制成,而且,其中,在金属薄板/锌镀层交界区形成有齿形结构,该齿形结构区至少为金属薄板总面积的50%。如根据本发明的方法所述,由于存在这种齿形结构,镀层与钢基体材料的结合性能提高,结果,与传统金属薄板相比,即使进行复杂的成形操作,根据本发明的金属薄板中发生明显可辨的磨损程度下降。另外,随着齿形结构延伸面积的增加,镀层与钢基体材料的结合强度提高。因此,齿形结构区至少相当于金属薄板总面积的80%的根据本发明的金属薄板表现出特别优异的磨损结果。
对于预期用途而言,根据本发明的金属薄板表现出优异的机械性能。例如,它的屈服点低于170 N/mm2,强度低于320N/mm2。此外,根据本发明的金属薄板的延伸率大于39%,rq值(相应的各向异性值,横向测定)大于1.8,nq值(相应的硬化指数值,横向测定)大于0.210。
根据本发明的方法尤其适于制备根据本发明的镀锌层扩散退火处理的金属薄板。
下面参照实施方案解释本发明。附图中:
图1是根据本发明的镀锌层扩散退火处理的金属薄板的截面示意图。
图2是图1中的镀锌层扩散退火处理的金属薄板截面受对应于本发明进展第一种情形的磨损影响的示意图。
图3是图1和2中的镀锌层扩散退火处理的金属薄板截面受对应于本发明进展第二种情形的磨损影响的示意图。
图4是根据本发明的镀锌层扩散退火处理的金属薄板中钢基体材料与镀层之间的过渡区的放大视图。
图5是图3所示的未根据本发明的镀锌层扩散退火处理的金属薄板中钢基体材料与镀层之间的过渡区的放大视图。
图6以图表形式示出了内氧化和外氧化对Zn/Fe相反应动力学以及对根据本发明的镀锌层扩散退火处理的金属薄板上存在的镀层性能的影响。
图1-3中所示的镀锌层扩散退火处理的金属薄板F1,F2和F3每个均包括由IF钢制成的冷轧带2。该冷轧带2构成其上镀覆主要包含锌和锌-铁化合物的镀层3的基体材料。
在图1所示的镀锌层扩散退火处理的金属薄板F1中,在金属薄板F1的制备过程中,由于在冷轧带2与镀层3之间的交界区4缓慢推进形成Zn/Fe相,结果,形成了齿形结构5,图4示出了由实际实施例获得的这种齿形结构的放大照片。这种齿形结构区至少占金属薄板总面积的50%,优选超过80%。镀层3与冷轧带2相互之间通过齿形结构5牢固结合。冷轧带2与镀层3的紧密啮合或者齿形结构5的形成是形成“生长进入”镀层的Zn/Fe相的结果。这样,镀层3被冷轧带2紧紧夹持住,确保镀层3牢固存在于冷轧带2上。由于在镀层3与冷轧带2之间存在细窄的齿形结构,结果,根据本发明的镀锌层扩散退火处理的金属薄板F1出现图2和3中所示形式的磨损的次数降至最低。
图2中所示的磨损情形典型地出现在采用传统方法制备的镀锌层扩散退火处理的金属薄板中。由图5可看出:在镀层3与冷轧带2之间没有齿形结构,因此,在冷轧带2与镀层3之间不存在有利的夹持作用。结果,由于例如在金属薄板F2成形过程中产生的应力的作用,镀层3破裂成自冷轧带2剥离的各个碎片6,7,8。这些碎片6,7,8的厚度与镀层3的厚度基本相同。结果,在碎片6,7,8剥离之后,冷轧带2表面2a未受到任何保护。这种形式的磨损称为“剥落1”。
在发展为图3所示的磨损形式的初期,曾尝试通过提高镀层3中的Fe含量来改善镀层3与冷轧带2间的结合性能。结果,在冷轧带2与镀层3之间的界面4处的镀层中形成了较厚γ相层9。δ相层10位于该相层9上。在这种情况下,相层9与相层10没有非常紧密地结合一起,尽管γ相层9与冷轧带2牢固相连。结果,例如,当其进行任何成形时,最上面的δ相层10以片状小板片12,13,14形式从下面的γ相层9上剥离。在小板片12,13,14剥离之后,只剩下与δ相层10相比薄得多的γ相层9保护该区域中的冷轧带2的表面。这种形式的磨损称为“剥落2”。
现在,结合实际实施例介绍根据本发明的步骤,所述实施例中:
IF钢含有(wt.%):
C | Si | Mn | P | S | Al | Nb | Ti |
0,004 | 0,05 | 0,12 | 0,01 | 0,008 | 0,038 | 0,023 | 0,06 |
余者为铁和通常的杂质。将所述IF钢连铸并分割成扁坯。然后,在一种多级宽带热轧机中的加热炉内加热至1150℃。
加热之后,在宽带热轧机的热轧线上将扁坯轧制成热轧带。此处的终轧温度为905℃。
在宽带热轧机的端部,在730℃的温度下,将热轧带卷取成带卷。
卷取之后,在连续运行的酸洗厂将附着在热轧带上的鳞皮去除。
酸洗之后,在例如总变形量为75%的多级冷轧带轧机中,将热轧带冷轧成带厚0.3mm的冷轧带。
然后,在连续热镀锌生产线对冷轧带进行退火和镀锌。这里,首先在清洗区将冷轧带上残存的冷轧阶段的污染物清洗掉。之后,将已清洗的冷轧带通过退火炉,在退火炉中,在由保护性气体构成的气氛中,将冷轧带加热至820℃。所述保护性气体的露点为-25℃。冷却至480℃之后,将所述带材在温度为460℃的锌镀液中浸渍。该锌镀液含有0.12%的铝。在已镀覆的冷轧带从锌镀液中离开之后,借助喷射处理装置将锌镀层厚度调整至7μm。镀锌之后,在530℃的镀锌层扩散退火处理温度下,对所述带材进行后退火处理。为此,需提供一个感应加热区和一个耐热保温区。
在将该“镀锌层扩散退火处理”的金属薄带冷却至50℃以下后,在平整机上对所述冷轧带的粗糙度进行调整。
然后,在后处理区对镀锌层扩散退火处理的金属薄板进行涂油,并且,最后卷取成成品卷材。
在作为实施例的前述步骤中,已进行各种系列的实验,它们的结果分别示于表1-4中。实验1-31为模拟试验,它们的结果和操作参数示于表1-3中,而实验32-38为运行实验,其参数与结果在表4中给出。
对于每个实验,表1-4均给出了实验序列号、所用IF钢中的Si含量、卷取机温度、进行再结晶退火的退火气体的露点、镀锌层扩散退火处理温度、屈服强度、抗拉强度、断裂时的延伸率、rq值、nq值、齿形结构的面积分数和磨损值。在表2-4中的“备注”列中,也标示出是否特定的实施例属于本发明(标志“E”)。
磨损值通过带材拉拔实验确定。在这种情况下,采用drawbead测试样品。可以将所确定的磨损值分成如下三个级别:
极好: <3g/m2
良好: 3-5g/m2
差: >5g/m2
表1所示结果由Si含量为0.01wt.%的Ti/Nb IF钢获得。在相关实验1-9中,在钢/镀层界面处没有或者只看到最多20%的极少部分的齿形结构,这导致在带材拉拔实验中磨损结果为适中或差(与图5相比)。镀锌层扩散退火处理温度较高(550℃)和/或露点较高(10℃)均导致更强烈的磨损,特别是在较高镀锌层扩散退火处理温度下可观察到“剥落2”。
特别是在770℃高的卷取机温度下,机械性能极佳,即:屈服点<150N/mm2,抗拉强度<315N/mm2,延伸率>41%,rq值>1.85,nq值>0.220。但是,磨损值较差。
表2涉及采用Si含量为0.05wt.%的钢进行的实验10-22。730℃的卷取机温度,再加上-25℃的露点和515℃的镀锌层扩散退火处理温度导致形成90-100%的显著齿形结构(图4),并且,因此获得<3g/m2的优异磨损值。同时,也能获得极佳的机械性能,即:屈服点<170N/mm2,抗拉强度<320N/mm2,延伸率>39%,rq值>1.80,nq值>0.210(实施例11-14,16-18和21)。实施例15获得了良好的磨损结果,但是该样品没有发生镀锌层扩散退火处理的金属薄板所必需的完全合金化。实施例19的磨损值较高(“剥落2”),原因是该样品在较高的镀锌层扩散退火处理温度退火,而且,在钢/镀层界面处形成了厚且脆的γ层。
表3包括采用Si含量为0.08wt.%的钢进行的实验23-31的结果。这里,仅仅当卷取机温度、露点和镀锌层扩散退火处理温度根据本发明进行匹配时,能获得极佳的磨损结果(实施例27)。该样品的机械性能也很好。
表4给出了运行实验32-38的结果。这些样品的结果进一步证实了在模拟实验1-31中获得的结果(表1-3)。根据本发明的实施例33和34同时具有优异的磨损值和极佳的机械性能。
表1
*=剥落2表2
*=剥落2**=未完全合金化E=本发明表3
*=剥落2**=未完全合金化E=本发明表4
*=剥落2**=未完全合金化E=本发明
实验 | Si含量[wt.%] | 卷取机温度[℃] | 露点[℃] | 镀锌层扩散退火处理温度[℃] | 屈服点[N/mm2] | 抗拉强度[N/mm2] | 断裂时的延伸率[%] | rq值 | nq值 | 齿形结构的面积分数[%] | 磨损率 | 备注 |
1 | 0,01 | 710 | -40 | 480 | 153 | 303 | 40,1 | 1,78 | 0,214 | 0 | 4,3 | |
2 | 0,01 | 710 | -40 | 550 | 163 | 321 | 39,3 | 1,80 | 0,211 | 20 | 14,3 | * |
3 | 0,01 | 710 | -10 | 550 | 161 | 315 | 39,7 | 1,82 | 0,210 | 0 | 12,2 | * |
4 | 0,01 | 710 | -10 | 480 | 172 | 328 | 41,2 | 1,85 | 0,212 | 0 | 18,4 | |
5 | 0,01 | 730 | -25 | 515 | 158 | 317 | 41,3 | 1,87 | 0,214 | 0 | 5,5 | |
6 | 0,01 | 770 | -10 | 550 | 141 | 312 | 42,0 | 1,85 | 0,220 | 0 | 20,3 | * |
7 | 0,01 | 770 | -10 | 480 | 139 | 309 | 42,0 | 1,94 | 0,222 | 0 | 25,2 | |
8 | 0,01 | 770 | -40 | 480 | 140 | 310 | 43,0 | 1,90 | 0,224 | 0 | 13,2 | |
9 | 0,01 | 770 | -40 | 550 | 142 | 313 | 41,5 | 2,02 | 0,221 | 0 | 14,7 | * |
实验 | Si含量[wt.%] | 卷取机温度[℃] | 露点[℃] | 镀锌层扩散退火处理温度[℃] | 屈服点[N/mm2] | 抗拉强度[N/mm2] | 断裂时的延伸率[%] | rq值 | nq值 | 齿形结构的面积分数[%] | 磨损率 | 备注 |
10 | 0,05 | 710 | -25 | 515 | 171 | 314 | 39,7 | 1,84 | 0,212 | 80 | 3,6 | |
11 | 0,05 | 730 | -25 | 515 | 156 | 315 | 40,3 | 1,93 | 0,216 | 90 | 2,7 | E |
12 | 0,05 | 730 | -25 | 515 | 159 | 314 | 42,0 | 1,88 | 0,219 | 90 | 2,4 | E |
13 | 0,05 | 730 | -25 | 515 | 161 | 318 | 40,7 | 1,95 | 0,218 | 100 | 1,8 | E |
14 | 0,05 | 730 | -25 | 515 | 162 | 319 | 41,4 | 1,98 | 0,217 | 100 | 1,3 | E |
15 | 0,05 | 730 | -25 | 480 | 169 | 321 | 41,9 | 1,91 | 0,214 | 80 | 2,2 | ** |
16 | 0,05 | 730 | -25 | 515 | 164 | 319 | 42,6 | 1,90 | 0,216 | 100 | 2,0 | E |
17 | 0,05 | 730 | -25 | 515 | 155 | 316 | 41,2 | 1,92 | 0,220 | 100 | 1,7 | E |
18 | 0,05 | 730 | -25 | 515 | 157 | 314 | 41,7 | 1,84 | 0,219 | 100 | 2,8 | E |
19 | 0,05 | 730 | -25 | 550 | 156 | 320 | 42,5 | 1,g0 | 0,221 | 100 | 9,3 | * |
20 | 0,05 | 730 | -10 | 515 | 154 | 316 | 42,6 | 1,89 | 0,223 | 10 | 14,2 | |
21 | 0,05 | 730 | -40 | 515 | 152 | 314 | 41,0 | 1,94 | 0,220 | 100 | 2,6 | E |
22 | 0,05 | 770 | -25 | 515 | 148 | 296 | 42,3 | 2,06 | 0,229 | 30 | 16,0 |
实验 | Si含量[wt.%] | 卷取机温度[℃] | 露点[℃] | 镀锌层扩散退火处理温度[℃] | 屈服点[N/mm2] | 抗拉强度[N/mm2] | 断裂时的延伸率[%] | rq值 | nq值 | 齿形结构的面积分数[%] | 磨损率 | 备注 |
23 | 0,08 | 710 | -10 | 550 | 165 | 328 | 40,4 | 1,83 | 0,213 | 10 | 13,3 | * |
24 | 0,08 | 710 | -40 | 480 | 159 | 321 | 39,6 | 1,78 | 0,209 | 100 | 3,5 | ** |
25 | 0,08 | 710 | -10 | 480 | 164 | 327 | 39,4 | 1,76 | 0,212 | 0 | 20,0 | |
26 | 0,08 | 710 | -40 | 550 | 162 | 322 | 40,8 | 1,85 | 0,207 | 100 | 10,8 | * |
27 | 0,08 | 730 | -25 | 515 | 161 | 315 | 40,9 | 1,89 | 0,218 | 100 | 2,1 | E |
28 | 0,08 | 770 | -10 | 480 | 156 | 311 | 42,1 | 2,03 | 0,215 | 0 | 15,8 | |
29 | 0,08 | 770 | -10 | 550 | 148 | 312 | 42,3 | 2,05 | 0,213 | 0 | 18,3 | |
30 | 0,08 | 770 | -40 | 550 | 146 | 311 | 42,6 | 1,97 | 0,212 | 10 | 21,3 | |
31 | 0,08 | 770 | -40 | 480 | 151 | 310 | 41,0 | 1,95 | 0,221 | 10 | 14,9 |
实验 | Si含量[wt.%] | 卷取机温度[℃] | 露点[℃] | 镀锌层扩散退火处理温度[℃] | 屈服点[N/mm2] | 抗拉强度[N/mm2] | 断裂时的延伸率[%] | rq值 | nq值 | 齿形结构的面积分数[%] | 磨损率 | 备注 |
32 | 0,006 | 715 | -28 | 526 | 171 | 322 | 39,8 | 1,78 | 0,205 | 0 | 4,7 | |
33 | 0,048 | 735 | -32 | 520 | 162 | 314 | 40,9 | 1,85 | 0.214 | 100 | 2,3 | E |
34 | 0,072 | 724 | -29 | 522 | 160 | 318 | 41,4 | 1,92 | 0,215 | 100 | 3,0 | E |
35 | 0,072 | 724 | -29 | 498 | 154 | 312 | 41,1 | 1,85 | 0,214 | 90 | 1,8 | ** |
36 | 0,072 | 724 | -29 | 562 | 153 | 316 | 41,0 | 1,89 | 0,217 | 100 | 7,8 | * |
37 | 0,055 | 770 | -33 | 524 | 145 | 314 | 42,3 | 2,01 | 0,225 | 0 | 8,5 | |
38 | 0,084 | 770 | -26 | 528 | 146 | 311 | 41,8 | 2,05 | 0,218 | 0 | 7,2 |
Claims (12)
1. 一种镀锌层扩散退火处理的金属薄板的制备方法,
- 其中,由含硅0.01-0.1wt.%的IF钢制备出热轧带,
- 其中,在不低于700℃但不高于750℃的卷取机温度下卷取热轧带,
- 其中,由所述卷取的热轧带轧制成冷轧带,
- 其中,在退火炉中,退火气氛下,对冷轧带进行再结晶退火,
- 其中,在锌镀液中,在已退火的冷轧带上形成锌镀层,
以及
- 其中,在不低于500℃但不高于540℃的镀锌层扩散退火处理温度下对所述镀覆冷轧带进行后退火。
2.根据权利要求1的方法,其特征在于:卷取机温度不低于710℃但不高于740℃。
3.根据权利要求2的方法,其特征在于:卷取机温度不低于720℃。
4.根据前述权利要求之任何一项的方法,其特征在于:在再结晶退火期间构成所述气氛的退火气体的露点为-20至-60℃。
5.根据权利要求4的方法,其特征在于:实施再结晶退火的气氛的露点为-25至-40℃。
6.根据前述权利要求之任何一项的方法,其特征在于:镀锌层扩散退火处理温度为510-530℃。
7.根据前述权利要求之任何一项的方法,其特征在于:锌镀液中含有0.1-0.14wt.%的铝。
8.根据权利要求7的方法,其特征在于:锌镀液中含有0.105-0.125wt.%的铝。
9.由IF钢制备的带有锌镀层的金属薄板,其中,在金属薄板/锌镀层交界区形成有紧密的齿形结构,该齿形结构区的面积分数至少为金属薄板总面积的50%。
10.根据权利要求9的金属薄板,其特征在于:它的屈服点低于170N/mm2,强度值低于320N/mm2,延伸率大于39%,rq值大于1.8,nq值大于0.210。
11.根据权利要求9或10的金属薄板,其特征在于:齿形结构区的面积分数至少为金属薄板总面积的80%。
12.根据权利要求8-11的金属薄板,其特征在于:它根据权利要求1-8的方法制备而成。
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DE10023312A DE10023312C1 (de) | 2000-05-15 | 2000-05-15 | Galvannealed-Feinblech und Verfahren zum Herstellen von derartigem Feinblech |
DE10023312.0 | 2000-05-15 |
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US (1) | US6887590B2 (zh) |
EP (1) | EP1285101A1 (zh) |
JP (1) | JP2003533595A (zh) |
KR (1) | KR20030014230A (zh) |
CN (1) | CN1436252A (zh) |
AU (1) | AU2001274036A1 (zh) |
DE (1) | DE10023312C1 (zh) |
WO (1) | WO2001088216A1 (zh) |
Cited By (6)
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CN101956126A (zh) * | 2010-09-30 | 2011-01-26 | 河北钢铁股份有限公司邯郸分公司 | 一种冷基高强度镀锌板及生产方法 |
CN107223166A (zh) * | 2014-12-24 | 2017-09-29 | Posco公司 | 焊接性和加工部耐蚀性优异的镀锌合金钢材及其制造方法 |
CN108138296A (zh) * | 2015-09-30 | 2018-06-08 | 蒂森克虏伯钢铁欧洲股份公司 | 具有锌扩散退火保护镀层的扁钢产品及其生产方法 |
CN108203789A (zh) * | 2016-12-16 | 2018-06-26 | 宝山钢铁股份有限公司 | 一种耐腐蚀性能优良的高强度if钢及其制造方法 |
CN108603264A (zh) * | 2016-01-29 | 2018-09-28 | 杰富意钢铁株式会社 | 高强度镀锌钢板、高强度部件及高强度镀锌钢板的制造方法 |
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EP1403388A1 (de) * | 2002-09-26 | 2004-03-31 | ThyssenKrupp Stahl AG | Verfahren zum Herstellen von Produkten durch Umformen bei erhöhten Temperaturen |
US6814815B2 (en) * | 2003-04-07 | 2004-11-09 | The Material Works, Ltd. | Method of removing scale and inhibiting oxidation in processed sheet metal |
EP1651789B1 (de) * | 2003-07-29 | 2010-08-25 | Voestalpine Stahl GmbH | Verfahren zum herstellen von geharteten bauteilen aus stahlblech |
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JPH0441658A (ja) * | 1990-06-07 | 1992-02-12 | Nippon Steel Corp | 耐パウダリング性に優れた焼付硬化性高強度合金化溶融亜鉛めっき鋼板およびその製造方法 |
JPH04346625A (ja) | 1991-05-24 | 1992-12-02 | Kobe Steel Ltd | 耐時効性、プレス成形性の優れた焼付硬化型冷延鋼板の製造方法 |
CN1039723C (zh) | 1993-11-22 | 1998-09-09 | 新日本制铁株式会社 | 钢板制造中表面缺陷少的超低碳钢连续铸造板坯和超低碳薄钢板及其制造方法 |
US5997664A (en) * | 1996-04-01 | 1999-12-07 | Nkk Corporation | Method for producing galvanized steel sheet |
US5897967A (en) | 1996-08-01 | 1999-04-27 | Sumitomo Metal Industries, Ltd. | Galvannealed steel sheet and manufacturing method thereof |
DE19822156A1 (de) * | 1998-05-16 | 1999-11-18 | Schloemann Siemag Ag | Verfahren und Vorrichtung zur Durchführung der Glühung eines Galvannealing-Prozesses |
-
2000
- 2000-05-15 DE DE10023312A patent/DE10023312C1/de not_active Expired - Fee Related
-
2001
- 2001-05-15 JP JP2001584598A patent/JP2003533595A/ja active Pending
- 2001-05-15 US US10/276,151 patent/US6887590B2/en not_active Expired - Fee Related
- 2001-05-15 WO PCT/EP2001/005472 patent/WO2001088216A1/de not_active Application Discontinuation
- 2001-05-15 KR KR1020027015457A patent/KR20030014230A/ko not_active Application Discontinuation
- 2001-05-15 EP EP01940473A patent/EP1285101A1/de not_active Withdrawn
- 2001-05-15 CN CN01810960A patent/CN1436252A/zh active Pending
- 2001-05-15 AU AU2001274036A patent/AU2001274036A1/en not_active Abandoned
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CN101956126A (zh) * | 2010-09-30 | 2011-01-26 | 河北钢铁股份有限公司邯郸分公司 | 一种冷基高强度镀锌板及生产方法 |
CN107223166A (zh) * | 2014-12-24 | 2017-09-29 | Posco公司 | 焊接性和加工部耐蚀性优异的镀锌合金钢材及其制造方法 |
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CN108603264A (zh) * | 2016-01-29 | 2018-09-28 | 杰富意钢铁株式会社 | 高强度镀锌钢板、高强度部件及高强度镀锌钢板的制造方法 |
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US11447852B2 (en) | 2016-01-29 | 2022-09-20 | Jfe Steel Corporation | High-strength galvanized steel sheet, high-strength member, and method for producing high-strength galvanized steel sheet |
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CN108203789B (zh) * | 2016-12-16 | 2019-11-22 | 宝钢湛江钢铁有限公司 | 一种耐腐蚀性能优良的高强度if钢及其制造方法 |
CN114761603A (zh) * | 2019-12-20 | 2022-07-15 | Posco公司 | 加工性和耐蚀性优异的铝基合金镀覆钢板及其制造方法 |
US11898252B2 (en) | 2019-12-20 | 2024-02-13 | Posco | Aluminum-based alloy-plated steel sheet having excellent workability and corrosion resistance, and manufacturing method therefor |
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Also Published As
Publication number | Publication date |
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DE10023312C1 (de) | 2001-08-23 |
EP1285101A1 (de) | 2003-02-26 |
US20030155048A1 (en) | 2003-08-21 |
AU2001274036A1 (en) | 2001-11-26 |
JP2003533595A (ja) | 2003-11-11 |
WO2001088216A1 (de) | 2001-11-22 |
US6887590B2 (en) | 2005-05-03 |
KR20030014230A (ko) | 2003-02-15 |
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