CN104520448B - 钢材,扁钢产品及该扁钢产品的制造方法 - Google Patents
钢材,扁钢产品及该扁钢产品的制造方法 Download PDFInfo
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- CN104520448B CN104520448B CN201380029895.5A CN201380029895A CN104520448B CN 104520448 B CN104520448 B CN 104520448B CN 201380029895 A CN201380029895 A CN 201380029895A CN 104520448 B CN104520448 B CN 104520448B
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C21D6/00—Heat treatment of ferrous alloys
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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
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/0226—Hot rolling
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- 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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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
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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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
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- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
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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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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- C25D7/00—Electroplating characterised by the article coated
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Abstract
本发明涉及一种钢材和由该钢材制成的扁钢产品,该钢材和扁钢产品具有优化了的机械特性,并且可以低成本地生产,不必使用昂贵的、采购花费波动大的合金元素。按照本发明的钢材和扁钢产品具有以下组成(重量%):C:0.11‑0.16%;Si:0.1‑0.3%;Mn:1.4‑1.9%;Al:0.02‑0.1%;Cr:0.45‑0.85%;Ti:0.025‑0.06%;B:0.0008‑0.002%;剩余Fe和生产条件决定不可避免的杂质含有磷、硫、氮或者钼,含量分别为:P<0.02%,S:<0.003%,N:<0.008%,Mo:<0.1%。本发明还涉及制造由按照本发明的钢材构成的扁钢产品的方法。
Description
技术领域
本发明涉及一种能够低成本生产的、高强度钢材。本发明同样还涉及由该钢材制得的扁钢产品及其制造方法。
在这里所提到的扁钢产品是指通过轧制过程得到的钢带、钢板或由它们制得的扁坯、板材毛坯和其他同类型的产品。
除非另有明确说明,否则与合金元素罗列有关的合金元素的含量以重量表示。
背景技术
双相钢从很长时间以来就开始用于汽车制造。在此,对于这一类钢材已知大量的合金设计,这些设计可以分别组合从而满足不同的要求。许多已知的设计都基于钼合金,或者以繁琐的生产过程,特别是冷轧钢带退火时非常快的降温,为前提条件,从而产生预期的钢材组织结构。由于钼的市场价格波动很大,因此高钼含量的钢材的生产具有很高的成本风险。但与之相对地,钼对于双相钢的机械特性有积极的效用。高钼含量可以延缓冷却时珠光体的形成并且可以保证产生针对各个钢材提出的要求有利的组织结构。
发明内容
以前述现有技术为基础,本发明的目的在于,提出一种钢材以及扁钢产品,该钢材和扁钢产品具有优化了的机械特性,并且不必使用昂贵的、采购花费波动大的合金元素,可以低成本地生产。
另外,还应给出一种可靠地制造按照本发明的冷轧扁钢产品的方法。
按照本发明的、可解决上述目的的钢材具有以下的组成(重量%):
C:0.11-0.16%;
Si:0.1-0.3%;
Mn:1.4-1.9%;
Al:0.02-0.1%;
Cr:0.45-0.85%;
Ti:0.025-0.06%;
B:0.0008-0.002%;
剩余Fe和生产条件决定不可避免的杂质有磷、硫、氮或者钼,P、S、N或Mo的含量分别为:
P:≤0.02%,
S:≤0.003%,
N:≤0.008%,
Mo:≤0.1%。
在按照本发明的合金中,特别地将钼的含量减小至最小值并且由其他低成本的合金元素来替代,同时不会导致明显的强度损失或者其他机械特性的退化。
碳能够在组织结构中形成马氏体,因此按照本发明的钢材中的碳是对于调整预期的高强度的基本元素。只有当按照本发明的钢材中含有至少0.11重量%的碳元素,该作用才会充分显现。但过高的C含量对焊接性产生负面作用。在此普遍适用的是,钢材的可焊性随着碳含量的升高降低。为了避免C含量对于可加工性的负面影响,在按照本发明的钢材中最大碳含量限制在0.16重量%。
硅通过提高铁素体的硬度,同样也用于提高钢材强度。按照本发明的钢材的最小硅含量为0.1重量%。但是过高的硅含量不仅会导致不期望的晶界氧化,对由按照本发明的钢材生产的扁钢产品的表面产生负面影响,如果按照本发明的扁钢产品为了改善钢材的耐腐蚀性应镀有一个金属保护层,高硅含量还会引起热浸镀层的困难。为了避免Si在按照本发明的钢材中引起这样负面的、给后续加工造成困难的影响,按照本发明的钢材的Si含量上限为0.3重量%。
锰阻碍在冷却时珠光体的形成。以此可以促进按照本发明的钢材中马氏体的形成并且提高钢材的强度。对抑制珠光体形成足够高的锰含量为1.4重量%。但是锰元素也具有负面作用,形成偏析或者降低焊接适应性。为了避免这些负面作用,按照本发明的钢材的锰的含量范围的上限设置为1.9重量%。
铝对于按照本发明的钢材有脱氧作用。为此所需的最大铝含量为0.1重量%。实际中,已证实铝含量最大为0.05重量%为特别有利。当含量大于0.02重量%时,就一定出现铝的预期作用,因此按照本发明的钢材的Al含量为0.02-0.1重量%,特别是0.02-0.05重量%。
铬在按照本发明的钢材中与锰一样用于钢材强度的提高。铬的出现可以增加硬度和钢材中马氏体的份额。为此所要求的Cr含量至少为0.45重量%。但是过高的铬含量会促进晶界氧化。为了避免该作用,按照本发明的钢材的Cr含量限制在不超过0.85重量%。
钛在按照本发明的钢材中通过细化晶粒提高钢材强度。另外Ti与钢材中的氮结合并且阻止不必要的氮化硼的形成。按照本发明的钢材中的硼可以完全发挥其提高强度的作用。为此,最小为0.025重量%Ti含量是必须的。更高的钛含量很大程度的延缓了退火时的重结晶。在极端情况下,这还可能伴随着延伸率下降。为了保证由按照本发明的钢材生产的扁钢产品具有最小14%的断裂延伸率,钛含量的上限按照本发明限制在0.06重量%,特别是0.055重量%以内,其中含量不超过0.045重量%被证明是特别符合实际生产的。
硼在按照本发明的钢材中也用于强度的提高。为此,最小为0.0008重量%的硼的含量是必要的。大于0.002重量%的B含量导致不希望的脆化现象。
磷、硫、氮和钼作为杂质微量存在于按照本发明的钢材中,因此对钢材和由该钢材制成的扁钢产品的特性没有任何影响。相应地,在按照本发明的钢材中这些杂质元素分别为:不超过0.02重量%的P,不超过0.003重量%的S,不超过0.008重量%的N,不超过0.1重量%的Mo,其中钼的含量优选小于0.05重量%。按照本发明的钢材中当然还可能存在取决于生产条件而引入的其他杂质,例如使用废料。但是这些杂质同样也是微量存在,因此并不影响钢材的特性。
生产按照本发明的扁钢产品、按照本发明的方法包括以下操作步骤:
a)按照本发明组成的钢材浇铸成为初级产品,该初级产品是扁坯或者薄扁坯;
b)初级产品热轧为厚度为2到5.5mm的热轧钢带,其中热轧初始温度为1000-1300℃,特别是1050-1200℃,并且热轧结束温度为840-950℃,特别是890-950℃;
c)在盘绕温度480-650℃下,该热轧钢带盘绕成卷材;
d)热轧钢带冷轧为厚度为0.6-2.4mm的冷轧扁钢产品,经过冷轧实现35-80%冷轧率;
e)以连续的过程完成对冷轧扁钢产品的热处理,其中
e.1)该冷轧扁钢产品首先在预热阶段,以加热速率0.2-45℃/s加热至不超过870℃的预热温度,特别是690-860℃,
e.2)该冷轧扁钢产品随后进入保持阶段,在退火温度750-870℃下保持退火持续时间8-260s,其中,可选择性地将已预热的扁钢产品在保持阶段内完成加热至退火温度,
e.3)该冷轧扁钢产品在退火持续结束之后以冷却速率0.5-110K/s冷却。
为了避免初级产品中的应力开裂,该初级产品应在浇铸之后还处在热的状态下继续保持在最小为300℃的温度下,或者以最高60℃/h的冷却速率,特别是最高50℃/h,缓慢冷却。
为了在完成热轧之前使初级产品分别达到要求的热轧初始温度,初级产品如果需要可以在温度足够高的熔炉中停留最长不超过500分钟的持续时间。
按照本发明,盘绕温度确定在480-650℃之间,因为更低的盘绕温度会导致更加坚硬的热轧扁钢产品(“热轧钢带”),该热轧钢带只能在复杂化了的条件下进一步加工。与之相对的,高于650℃的盘绕温度结合按照本发明设置的铬含量,会增加晶界氧化的危险。
盘绕成卷材的热轧钢带冷却至室温。冷却后,可选择性地进行酸洗,从而除去热轧钢带上附着的氧化皮和污垢。
在盘绕和如果有需要进行的酸洗之后,热轧钢带在一个或几个冷轧步骤中被轧制为冷轧扁钢产品(“冷轧钢带”)。在此,热轧钢带由按照本发明设置的厚度以总冷轧率为35-80%冷轧,从而实现目标冷轧钢带厚度为0.6-2.4mm。
在接下来的完成步骤中,冷轧钢带经过连续的退火过程。这有利于设置预期的机械特性。
同时,该退火过程还可以作为冷轧扁钢产品对后续金属镀层的准备,该金属涂层可保护冷轧扁钢产品在以后的使用中免受腐蚀性的破坏。这一类金属涂层可以大规模地、低成本地通过热浸镀层法涂敷在钢带表面。在此,按照本发明设置的退火可以在传统构建的、连续的热浸镀层设备中进行。电解镀锌还可以选择性紧接着该退火过程进行。
热处理的过程中,不仅要加热至各自的最大退火温度,还要在一步或多个步骤中完成随后的降温。首先在预热阶段,以0.2K/s到45K/s之间的速率加热至预热温度,最大预热温度等于最大退火温度,特别是在690-860℃或者690-840℃范围内。
紧接着,该扁钢产品进入保持阶段,在该阶段中,如果预热温度低于目标最大退火温度,可通过另一个加热过程达到最大退火温度750-870℃。扁钢产品保持在各自的最大退火温度直到保持阶段结束。退火持续时间是指扁钢产品在保持阶段保持在最大退火温度的持续时间,为8-260s。过低的温度或者过短的时间情况下,材料不会重结晶。因此,对于冷却时金相组织转变,没有足够的可用于马氏体形成的奥氏体。另外,未重结晶的钢材会导致明显的各向异性。相反地,过长的退火持续时间或者过高的温度导致粗的组织结构并且由此引起机械特性变差。
结束退火持续时间之后,冷轧扁钢产品以冷却速率0.5-110K/s进行冷却。在此,在上述区域内调节冷却速率,从而尽量避免珠光体形成。
如果在热处理之后还应该热浸镀层,该冷轧的扁钢产品应在冷却过程中冷却至455-550℃。这样调温后的冷轧扁钢产品随后通过温度为450-480℃的Zn熔池。如果冷轧扁钢产品的温度处在锌池预设的温度范围内,钢带可以在进入锌池之前保持最长不超过100s的持续时间。相反地,如果钢带的温度高于480℃,扁钢产品直到进入锌池之前以不超过10K/s的冷却速率冷却至锌池温度范围内的温度,特别是等于锌池温度。
从锌池中出来后,扁钢产品上存在的Zn基-保护涂层的厚度以已知的方式通过削去装置调节。
紧随着热浸镀层可以选择性地进行进一步的热处理(“锌镀层退火处理”/Galvannealing),其中,为了烙上锌层,经热浸镀的扁钢产品加热至最大不超过550℃。
所获得的冷轧扁钢产品从锌池中出来之后直接地或者紧随着额外的热处理冷却至室温。
按照本发明的、生产按照本发明的扁钢产品的方法包括以下变体:
变体a)
该冷轧扁钢产品(“冷轧钢带”)在预热熔炉中以加热速率10-45K/s加热至预热温度660-840℃。
随后已预热的冷轧钢带通过熔炉区域,在该区域内冷轧钢带在温度760-860℃保持经过保持时间8-24s。取决于之前操作步骤所达到的预热温度,在此可以进行加热速率为0.2-15K/s的进一步加热。
退火后的冷轧钢带随后以冷却速率2.0-30K/s冷却至进入温度455-550℃,以该温度紧接着进入锌熔池并且在锌池中保持经过不超过45s的保持时间。该锌熔池具有455-465℃的温度。取决于进入温度,锌熔池中的冷轧钢带以最大不超过10K/s的冷却速率冷却至当时锌熔池的温度,或者保持在不变的温度。在从锌熔池出来、涂敷有锌层的冷轧钢带上,以已知的方式调整涂层的厚度。随后,镀层的冷轧钢带冷却至室温。
变体b)
该冷轧扁钢产品在连续熔炉的入口加热区域以不超过25K/s的加热速率加热至目标温度760-860℃。
随后,已加热的冷轧扁钢产品在熔炉的保持区域在750-870℃,特别是780-870℃的退火温度保持35-150s。取决于冷轧扁钢产品进入保持区域的温度,在保持时间内,即在保持区域内,以不超过3K/s的加热速率加热扁钢产品至各自的退火温度。
保持在退火温度之后进行二阶冷却,其中,冷轧扁钢产品首先缓慢地以冷却速率0.5-10K/s冷却至为640-730℃的过渡温度,并且以冷却速率5-110K/s加速冷却至温度455-550℃。
已冷却至相关温度的冷轧扁钢产品然后通过锌熔池。该锌熔池具有450-480℃的温度。从锌熔池出来、涂敷有锌层的冷轧扁钢产品上,以已知的方式调整涂层的厚度。
为了促使锌层上的合金形成,可以紧随着镀锌层进行退火处理(“锌镀层退火处理”/Galvanneal ing)。为此,已镀有锌层的冷轧钢带可以加热至470-550℃并且在该温度下保持经过足够长的时间。
在镀锌层之后,或者如果进行锌镀层退火处理,则在该处理之后,为了改善冷轧钢带的机械特性和镀层的表面重量,镀锌冷轧钢带可以进行平整轧制。由此获得的平整度通常在0.1-2.0%范围内,特别是在0.1-1.0%范围内。
按照本发明组成并制得的冷轧扁钢产品为了调整其机械特性可以替换上述热浸镀层在传统退火炉中进行热处理,其中,加热(操作步骤e.1))和在各自退火温度上的退火(操作步骤e.2))以上述的方式完成,但是操作步骤e.3)至少分为两个阶段进行,对此首先冷却冷轧扁钢产品至250-500℃,然后在该温度范围下保持最长不超过760s,从而进行过时效处理,并且最后冷却至室温。通过这种方式,使按照本发明的扁钢产品的组织结构中的奥氏体稳定。
在一个符合上述处理方式的按照本发明方法的变体中,随后在连续熔炉中进行如下的热处理步骤:
该冷轧扁钢产品首先在加热区域以加热速率1-8K/s加热至750-870℃,特别是750-850℃。
随后,已加热的冷轧扁钢产品通过熔炉区域,在该区域冷轧扁钢产品在退火温度750-870℃,特别是750-850℃,保持经过保持时间70-260s。取决于在以上过程中所达到的预热温度,进一步以不超过5K/s的加热速率加热。
这样退火的冷轧扁钢产品随后进行二阶冷却,其中,首先以冷却速率3-30K/s加速冷却至过渡温度450-570℃。该冷却通过风冷和/或喷气冷却完成。随后的减慢冷却中,冷轧扁钢产品以冷却速率1-15K/s冷却至400-500℃。
紧随着各个冷却步骤可以进行过时效处理,其中,冷轧扁钢产品在温度250-500℃,特别是250-330℃,保持经过保持时间150-760s。取决于各自的进入温度,冷轧扁钢产品以不超过1.5K/s的冷却速率冷却。
为了进一步改善扁钢产品的机械特性,以上述方式热处理过的冷轧扁钢产品随后还可以进行平整轧制。在此调整后的平整度在0.1-2.0%范围内,特别是0.1-1%范围内。
这样热处理并且必要时平整轧制后的冷轧扁钢产品可以随后通过镀层设备电解镀层,在该电镀设备中,金属镀层,例如锌合金镀层,以已知的电化学(“电解”)方式在冷轧扁钢产品上沉积。
按照本发明的扁钢产品具有上述方式组成的、按照本发明的合金,并且通过结构表明了特征,该结构的60-90体积%由包括贝氏体中铁素体的铁素体组成,10-40体积%由马氏体组成,不超过5体积%由残余奥氏体组成以及不超过5体积%由生产条件限制的、不可避免的其他结构部分而组成。
在此,按照DIN EN ISO 6892(样品形状2,长样品)的拉伸试验中得出的数值在以下的范围内:
Rp0.2最小为440Mpa,特别是不超过550Mpa,
Rm最小为780Mpa,特别是不超过900Mpa,
A80最小为14%,
n10-20/Ag最小为0.10,
BH2最小为25Mpa,特别是最小为30Mpa。
在实践中可以采用根据本发明的方法可靠地生产根据本发明的扁钢产品。
具体实施方式
在图1和图2中示出的曲线图分别示出了当冷轧扁钢产品经过按照本发明的方式实施的退火过程和紧接着立即进行热浸镀层时不同的温度变化曲线:
-以加热速率RV预热至预热温度TV;
-保持在最大退火温度TG经过退火持续时间tG,其中,当预热温度TV小于退火温度TG时(虚线TV=TG;实线TV<TG),该保持时间还包括完成加热到退火温度TG的时间;
-冷却分为一阶(图1)或者二阶(图2),如下说明:
-扁钢产品冷却至温度TE(图1)或者第一温度TE’(图2),
-当温度TE在为熔池温度TB设置的温度范围内,特别是等于温度TB时,可选择地在温度TE上保持通过持续时间tH(图1),或者
-当第一温度TE’大于熔池预设温度范围的上限值时,温度由第一温度TE’继续降温至第二温度TE”,其中在第二降温步骤,第二温度TE”落在熔池预设温度TB范围内,特别是等于温度TB(图2);
-扁钢产品在通过时间tB内经过熔池;
-冷却至室温RT。
与此相对,图3中的曲线图示例性地示出了扁钢产品不进行热浸镀层、连续地退火时的温度变化曲线:
-以加热速率RV在预热持续时间tV内预热至预热温度TV;
-保持在最大退火温度TG经过退火持续时间tG,其中,当预热温度TV小于退火温度TG时(虚线TV=TG;实线TV<TG),该保持时间还包括完成加热到退火温度TG的时间;
-冷却分为两个阶段,其中,在第一阶段以更高的冷却速度冷却至第一过渡温度TZ’并且随后以减小的冷却速度冷却至第二过渡温度TZ”;
-进行过时效处理,处理过程中,扁钢产品由第二过渡温度TZ”以冷却速率RU经过处理持续时间tU冷却至过时效处理温度TU;
-冷却至室温RT。
为了检测通过本发明实现的效果,表格1给出了九个熔炼的钢水A-I以及X,Y的组成。钢材A-I涉及按照本发明的钢材,而钢材X,Y不属于本发明。
钢水A-I,X,Y浇铸成扁坯。冷却扁坯时,最大冷却速度不能超过60K/h。为了完成下一步的热轧,扁坯随后在熔炉中加热至各自的热轧起始温度WAT。
在热轧步骤中,温度为热轧初始温度WAT的扁钢热轧为结束温度为WET并具有厚度WBD的热轧钢带。热轧之后所得到的钢带冷却至盘绕温度HT,随后在该盘绕温度下盘绕成卷材。
这样热轧制得的、具有各自不同的总变形程度KWG的钢带被冷轧成为具有厚度KBD的冷轧钢带。
生产热轧和冷轧钢带需要考虑到的工艺参数“热轧初始温度WAT”,“热轧结束温度WET”,“热轧钢带厚度WBD”,“盘绕温度HT”,“总变形程度KWG”和“冷轧钢带厚度KBD”分别在表2和3中给出。
这样冷轧制得的钢带可以进行不同的退火实验。
遵循图1中曲线的这些实验的第一个变体中,钢带在传统的热浸镀层设备中首先在预热区域以加热速率RV加热至预热温度TV。
紧随着预热,钢带在保持区域首先以加热速率RF完成加热至最大退火温度TG,随后保持在该温度。经过整个保持区域,即包括经过完成加热和保持,需要退火持续时间tG。
随后冷轧钢带不间断地以冷却速率RE在一个阶段内冷却至温度TE。从熔池出来的钢带具有可以防止腐蚀的Zn合金镀层。
生产热轧和冷轧钢带需要考虑到的工艺参数“加热速率RV”,“预热温度TV”,“加热速率RF”,“退火温度TG”,“退火持续时间tG”,“冷却速率rE”,“温度TE”,“保持时间tE”,“冷却速率RB”和“熔池温度TB”分别在表4中给出。另外,对实际操作适用的、以按照本发明的方式热浸镀层的参数以普通形式在表4中示出。
遵循图2中曲线进行的试验的第二个变体中,钢带再次在传统的热浸镀层设备中首先在熔炉的第一区域以加热速率RV加热至预热温度TV。紧接在预热之后钢带立即进入熔炉的第二区域。如果预热温度TV小于上述的最大退火温度TG,钢带以加热速率RF完成加热至要求的最大退火温度TG。随后冷轧钢带连续的分为两个阶段冷却。在冷却的第一阶段,钢带以相对较低的第一冷却速率RE’冷却至第一过渡温度TE’。随着第一过渡温度TE’的达到,以提高的冷却速率RE将钢带快速冷却至温度TE。从熔池中出来的钢带具有Zn合金镀层,可以保护钢带不被腐蚀。
生产热轧和冷轧钢带需要考虑到的工艺参数“加热速率RV”,“预热温度TV”,“加热速率RF”“退火温度TG”,“退火持续时间tG”,“第一冷却速率RE’”,“第一过渡温度TE’”,“冷却速率RE”,“温度TE”,“保持时间tE”,“冷却速率RB”和“温度TB”在表5中给出。
遵循图3中曲线进行的试验的第三个变体中,钢带在传统的热处理设备中首先在熔炉的预热区域以加热速率RV加热至预热温度TV。紧接在预热之后钢带立即进入熔炉的第二区域。如果预热温度TV小于上述的最大退火温度TG,钢带在该保持区域以加热速率RG完成加热至要求的最大退火温度TG。已加热至各自退火温度TG的钢带随后保持在该温度下。完成加热和保持时间同样都在退火持续时间tG内进行。
随后冷轧钢带被连续的分为两个阶段冷却。在冷却的第一阶段,通过喷气冷却,以相对较高的第一冷却速率RZ’将钢带冷却至第一过渡温度TZ’。随着第一过渡温度TZ’的达到,结束喷气冷却,通过滚动冷却以降低的第二冷却速率RZ”快速冷却至第二过渡温度TZ”。通过在二阶冷却随后进行的过时效处理,钢带由第二过渡温度TZ”以冷却速率RU冷却至过时效温度TU。
生产热轧和冷轧钢带需要考虑到的工艺参数“加热速率RV”,“预热温度TV”,“加热速率RG”,“退火温度TG”,“退火持续时间tG”,“第一冷却速率RZ’”,“第一过渡温度TZ’”,“第二冷却速率RZ””,“第二过渡温度TZ””,“冷却速率RU”和“过时效温度TU”在表6中给出。
在冷轧钢带样品上,在样品上沿着轧制方向测定屈服强度Rp0.2、抗拉强度Rm、伸长率A80,n值(10-20/Ag)和金相组织结构的组成。
另外,V型弯曲的特性可以按照DIN EN ISO 7438确定。最小弯曲半径,也就是指在没有可见裂缝出现的情况下半径,与钢板厚度的比例关系在此最大为2.0并且理想情况下不超过1.7。
按照DIN EN ISO 7438的弯曲试验中(样品尺寸为钢板厚度×20mm×120mm)测定最小弯曲直径,在该弯曲直径下样品没有出现可见的损坏。弯曲直径应该为4×钢板厚度,理想为3×钢板厚度。根据上述发明,这意味着,最大弯曲直径不应超过9.6mm。
最后,由上述方式生产的冷轧钢带冲制成的样品的扩孔率按照ISO 16630,以孔径10mm和拉延速度0.8mm/s进行测定。扩孔率最小为15%,理想至少为18%。
在表7中,共有32个按照上述方式进行的试验,每个试验中,加工一种表1中给出的钢材,该钢材使用表2给出的热轧变体,使用表3给出的冷轧变体,进行表4、5和6分别给出的各个冷轧钢带的退火过程变体。另外,表7还给出了组织结构的机械特性和组成以及按照DIN EN ISO 7438(“V型弯曲”,“U型弯曲”)和按照DIN ISO16630(“扩孔率”)确定的特性。
Claims (14)
1.一种冷轧扁钢产品,所述冷轧扁钢产品具有以下组成部分(重量%):
C:0.11-0.16%;
Si:0.1-0.3%;
Mn:1.4-1.9%;
Al:0.02-0.1%;
Cr:0.45-0.85%;
Ti:0.025-0.06%;
B:0.0008-0.002%;
剩余Fe和生产条件决定不可避免的杂质有磷、硫、氮或者钼,含量分别为:
P:≤0.02%,
S:≤0.003%,
N:≤0.008%,
Mo:≤0.1%
其特征在于,所述冷轧扁钢产品具有60-90体积%由包括贝氏体中铁素体的铁素体,10-40体积%由马氏体,不超过5体积%由剩余奥氏体和不超过5体积%由生产条件限制的、不可避免的其他组成部分构成的组织结构。
2.根据权利要求1所述的冷轧扁钢产品,其特征在于,所述冷轧扁钢产品的Al含量最高为0.05重量%。
3.根据权利要求1所述的冷轧扁钢产品,其特征在于,所述冷轧扁钢产品的Ti含量最高≤0.055重量%。
4.根据权利要求3所述的冷轧扁钢产品,其特征在于,所述冷轧扁钢产品的Ti含量最高为0.045重量%。
5.根据前述权利要求的任意一项所述的冷轧扁钢产品,其特征在于,所述冷轧扁钢产品的Mo含量最高为0.05重量%。
6.根据权利要求1所述的冷轧扁钢产品,其特征在于,所述扁钢产品的屈服强度Rp0.2最小为440Mpa,抗拉强度最小为780Mpa,断裂延伸率A80最小为14%,n10-20/Ag值最小为0.11,BH2值最小为25Mpa。
7.一种生产具有权利要求1至6中任一项所述的冷轧扁钢的方法,所述方法包括以下操作步骤:
a)将钢材浇铸成为初级产品;其中钢材具有以下组成部分(重量%):
C:0.11-0.16%;
Si:0.1-0.3%;
Mn:1.4-1.9%;
Al:0.02-0.1%;
Cr:0.45-0.85%;
Ti:0.025-0.06%;
B:0.0008-0.002%;
剩余Fe和生产条件决定不可避免的杂质有磷、硫、氮或者钼,含量分别为:
P:≤0.02%,
S:≤0.003%,
N:≤0.008%,
Mo:≤0.1%
b)所述初级产品热轧为具有2到5.5mm厚度的热轧钢带,其中热轧初始温度为1000-1300℃并且热轧结束温度为840-950℃;
c)在盘绕温度480-650℃下,所述热轧钢带盘绕成卷材;
d)所述热轧钢带冷轧为厚度为0.6-2.4mm的冷轧扁钢产品,其中经过冷轧实现冷轧率为35-80%;
e)在连续的过程中完成对所述冷轧扁钢产品的热处理,其中
e.1)所述冷轧扁钢产品首先在预热阶段以加热速率0.2-45℃/s加热至不超过870℃的预热温度,
e.2)所述冷轧扁钢产品随后进入保持阶段,在退火温度750-870℃下保持经过退火持续时间8-260s,其中,将已预热的扁钢产品在保持阶段内完成加热至退火温度,
e.3)所述冷轧扁钢产品在退火持续结束之后以冷却速率0.5-110K/s冷却。
8.根据权利要求7所述的方法,其特征在于,所述初级产品在操作步骤a)和b)之间温度保持在≥300℃。
9.根据权利要求7所述的方法,其特征在于,在操作步骤a)和b)之间所述初级产品以冷却速率≤60℃/h冷却至室温。
10.根据权利要求8或9所述的方法,其特征在于,在操作步骤b)之前,所述初级产品经过不超过500分钟的加热持续时间加热至各自的热轧初始温度。
11.根据权利要求7所述的方法,其特征在于,所述冷轧扁钢产品紧随着操作步骤e.3)连续地进行热浸镀层,并且在操作步骤e.3)中冷轧扁钢产品冷却至455-550℃。
12.根据权利要求7所述的方法,其特征在于,所述冷轧扁钢产品在操作步骤e.3)中冷却至室温。
13.根据权利要求12所述的方法,其特征在于,所述冷轧扁钢产品在操作步骤e.3)中以至少两个冷却步骤冷却至室温,冷轧扁钢产品在第一冷却步骤冷却至250-500℃并且在所述温度范围保持不超过760s,并且紧接着冷却至室温。
14.根据权利要求12或13所述的方法,其特征在于,所述冷轧扁钢产品在冷却至室温后电镀金属保护涂层。
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JP5088023B2 (ja) * | 2006-09-29 | 2012-12-05 | 新日本製鐵株式会社 | 加工性に優れた高強度冷延鋼板及びその製造方法 |
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CN101229565A (zh) * | 2008-02-26 | 2008-07-30 | 重庆钢铁(集团)有限责任公司 | 高强度球扁钢的生产工艺 |
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EP2855717A1 (de) | 2015-04-08 |
US9976205B2 (en) | 2018-05-22 |
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EP2855718A1 (de) | 2015-04-08 |
CN104583424A (zh) | 2015-04-29 |
EP2855717B1 (de) | 2020-01-22 |
JP6374864B2 (ja) | 2018-08-15 |
KR20150023566A (ko) | 2015-03-05 |
JP2015525293A (ja) | 2015-09-03 |
CN104520448A (zh) | 2015-04-15 |
US20150152533A1 (en) | 2015-06-04 |
KR102073442B1 (ko) | 2020-02-04 |
WO2013182622A1 (de) | 2013-12-12 |
US20150122377A1 (en) | 2015-05-07 |
KR102073441B1 (ko) | 2020-02-04 |
JP2015525292A (ja) | 2015-09-03 |
JP6310452B2 (ja) | 2018-04-11 |
WO2013182621A1 (de) | 2013-12-12 |
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