CN112877589B - 一种碳钢奥氏体不锈钢轧制复合板及其制造方法 - Google Patents

一种碳钢奥氏体不锈钢轧制复合板及其制造方法 Download PDF

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CN112877589B
CN112877589B CN201911196554.2A CN201911196554A CN112877589B CN 112877589 B CN112877589 B CN 112877589B CN 201911196554 A CN201911196554 A CN 201911196554A CN 112877589 B CN112877589 B CN 112877589B
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stainless steel
austenitic stainless
carbon steel
percent
composite plate
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CN112877589A (zh
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薛鹏
朱晓东
闫博
焦四海
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to CN201911196554.2A priority Critical patent/CN112877589B/zh
Priority to JP2022529742A priority patent/JP2023503912A/ja
Priority to US17/780,598 priority patent/US20230001504A1/en
Priority to PCT/CN2020/132056 priority patent/WO2021104417A1/zh
Priority to EP20894434.8A priority patent/EP4067525A4/en
Priority to KR1020227020166A priority patent/KR20220106149A/ko
Publication of CN112877589A publication Critical patent/CN112877589A/zh
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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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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    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/04—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating by means of a rolling mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
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    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
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    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
    • B23K20/227—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded with ferrous layer
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    • B32B15/00—Layered products comprising a layer of metal
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    • C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
    • 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
    • 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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    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B37/00—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding
    • B32B37/14—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers
    • B32B37/144—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers using layers with different mechanical or chemical conditions or properties, e.g. layers with different thermal shrinkage, layers under tension during bonding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B37/00—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding
    • B32B37/14—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers
    • B32B37/16—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers with all layers existing as coherent layers before laminating
    • B32B37/18—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers with all layers existing as coherent layers before laminating involving the assembly of discrete sheets or panels only
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B37/00—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding
    • B32B37/14—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers
    • B32B37/16—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers with all layers existing as coherent layers before laminating
    • B32B37/20—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the properties of the layers with all layers existing as coherent layers before laminating involving the assembly of continuous webs only
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material

Abstract

本发明公开了一种碳钢奥氏体不锈钢轧制复合板的制造方法，其包括步骤：(1)制得碳钢层坯料和不锈钢层坯料；(2)组坯；(3)复合轧制；(4)冷轧；(5)第一次退火；(6)第二次退火。该碳钢奥氏体不锈钢轧制复合板通过独特的两次退火工艺，使得该复合板兼具奥氏体不锈钢以及碳钢的各性能优点。此外，本发明还公开了一种采用该方法制造的碳钢奥氏体不锈钢轧制复合板。

Description

一种碳钢奥氏体不锈钢轧制复合板及其制造方法
技术领域
本发明涉及一种钢板及其制造方法，尤其涉及一种具有奥氏体不锈钢层的钢板及其制造方法。
背景技术
过去的十年结构用钢尤其是汽车结构用钢获得了广泛的应用，其中高强度汽车结构用钢已经成为汽车减重及结构件强度升级的主力产品。结构用钢主要通过控制不同的生产工艺以获得不同的组织和性能，品种主要包括析出强化钢、马氏体钢、双相钢、TRIP钢(QP钢)和复相钢等，强度涵盖780MPa-1700MPa的不同强度级别，其中780MPa-1180MPa级别的冷轧高强结构钢已经有了相当可观的应用实绩，但在使用过程中仍然还有部分使用性能的不足亟待解决。
超高强钢作为一种碳钢，其表面耐蚀性能低于不锈钢。需要特殊的磷化涂装工艺或者在出厂时添加镀层来增加耐蚀性能。这些增加的工序会造成成本的增加。而且随着高强钢强度的提高，合金元素的添加量不断增加，制造过程中合金元素的表面富集会影响磷化涂装性能和可镀性，不利于生产出具有耐蚀性能的高强度钢板。所以，本发明提供一种碳钢+奥氏体不锈钢轧制复合板，该复合板具有奥氏体不锈钢层，同时具有为整体钢板提供不同特定力学性能基础的高强碳钢层。
奥氏体不锈钢在耐蚀性、耐热性、低温强度和力学性能方面有非常好的表现，同时冲压弯曲等加工性好，无热处理硬化现象。但是奥氏体不锈钢是一种亚稳态不锈钢，在生产加工过程中容易产生加工硬化和析出相变，导致材料强度升高，塑性降低，成形性能降低、耐蚀性降低。要得到具有较好的耐蚀性、较强的塑性恢复能力的奥氏体不锈钢，并且消除因压力加工引起的硬化应力，目前现有技术主要通过在冷卷后进行退火处理来实现软化。常用的退火方式为：退火温度为1050-1150℃，保温时间大于30s；然后冷却至室温。
而结构用高强度碳钢的退火曲线多种多样，和成分配合可以实现从780MPa-1700MPa的不同强度级别，但是结构用碳钢由于合金含量的限制，奥氏体化温度低，与奥氏体不锈钢使用相同的退火均热温度会导致晶粒粗大。同时，结构用碳钢的退火曲线包含多种控制冷却要求，与奥氏体不锈钢均热后快速冷却的生产过程不同。这导致了含碳钢层和奥氏体不锈钢层的轧制复合钢板很难通过一次退火实现机械性能和耐蚀性能的同时获得。
基于此，期望获得一种碳钢奥氏体不锈钢轧制复合板的制造方法，其可以在不改变奥氏体不锈钢层组织性能的情况下，调节碳钢层组织性能，从而实现高强度碳钢+奥氏体不锈钢轧制复合板的性能。
发明内容
本发明的目的之一在于提供一种碳钢奥氏体不锈钢轧制复合板的制造方法，该碳钢奥氏体不锈钢轧制复合板具有奥氏体不锈钢层，同时具有为整体钢板提供不同特定力学性能基础的碳钢层，该碳钢奥氏体不锈钢轧制复合板可以具有不同的强度级别，并且兼具优秀的抗腐蚀能力。
为了实现上述目的，本发明提出了上述的碳钢奥氏体不锈钢轧制复合板的制造方法，其包括步骤：
(1)制得碳钢层坯料和不锈钢层坯料；
(2)组坯；
(3)复合轧制；
(4)冷轧；
(5)第一次退火：退火温度为1050-1150℃，保温时间大于30s；然后冷却至室温，在该冷却过程中，在900-500℃的温度范围内进行快速冷却，控制冷却速度为20-200℃/s；(6)第二次退火：以大于5℃/s的加热速度加热至均热温度800-950℃，保温10-100s，然后以v1＝5-20℃/s的速度冷却到快冷开始温度T，快冷开始温度T≥800-10×v1，然后再以20-1000℃/s的速度冷却到150-450℃；然后进行过时效处理，过时效温度为150-450℃，过时效处理时间为100-400s。
在本发明所述的制造方法中，在步骤(5)中，设置退火温度在1050-1150℃是因为奥氏体不锈钢在1050-1150℃之间进行固溶退火，可以使得析出的碳化物被重新固溶，然后快速冷却到室温，由于快速冷却过程中的冷却速度较快，固溶的碳来不及与其它合金元素结合析出，从而以此提高其耐晶间腐蚀性能。此外，若奥氏体不锈钢的退火温度高于1150℃时，晶粒会变得粗大，晶粒度等级降低，这样会降低带钢的耐腐蚀性能。因此，基于上述考虑，设置步骤(5)的工艺参数为：将退火温度为1050-1150℃，保温时间大于30s；然后冷却至室温，在该冷却过程中，在900-500℃的温度范围内进行快速冷却，控制冷却速度为20-200℃/s；而在步骤(6)中，第二次退火时的均热温度小于奥氏体化温度，且大于不锈钢层析出敏感温度的上限，因此，将其设置在800-950℃。且，设置缓冷速度v1为5-20℃/s，是为了防止碳化物、σ相析出，而随后设置以20-1000℃/s的速度冷却到150-450℃；然后进行过时效处理，过时效处理时间为100-400s，是为了避免已经固溶的碳化物、σ相重新析出。
进一步地，在本发明所述的制造方法中，在步骤(3)中，将坯料加热至1100-1260℃，保温0.6小时以上，控制终轧温度大于850℃，轧后以30-100℃/s的速度冷却，控制卷取温度为450-600℃。
本案发明人通过研究发现终轧温度越低，卷取温度越高，晶界有更多的析出碳化物、σ相析出。在其它轧制工艺参数相同时，较低的终轧温度以及较高的卷取温度更易析出碳化物、σ相析出，从而更容易导致晶间腐蚀的发生。因此，需要控制终轧温度较高，卷取温度较低，但是考虑到太高的终轧温度和太低的卷取温度无法稳定控制，因此，在本发明所述的制造方法中可以控制终轧温度大于850℃，轧后以30-100℃/s的速度快速冷却，控制卷取温度为450～600℃。
进一步地，在本发明所述的制造方法中，在步骤(4)中，控制冷轧压下率为40-70％。
进一步地，在本发明所述的制造方法中，还包括步骤(7)平整。
此外，本发明还提供了采用上述制造方法制得的一种碳钢奥氏体不锈钢轧制复合板。
需要说明的是，在本技术方案中，碳钢层为基层，奥氏体不锈钢为覆层，碳钢基层可以单面地或双面地复合奥氏体不锈钢覆层。
进一步地，在本发明所述的碳钢奥氏体不锈钢轧制复合板中，奥氏体不锈钢层的化学元素质量百分含量为：
C：0.02％～0.15％，Si：0.3％～1.0％，Mn：1.0％～10.5％，Cr：14.0～20.0％，Ni：0.2～14.0％，N≤0.25％，Cu≤0.6％，Mo≤3.0％，余量为Fe和其他不可避免的杂质。
在本发明所述的碳钢奥氏体不锈钢轧制复合板中，奥氏体不锈钢层的各化学元素的设计原理如下所述：
C：碳是强烈形成、稳定、扩大奥氏体相区的元素，C对室温下的奥氏体组织和强度起到关键作用，特别是当Ni含量相对较低时，C在稳定奥氏体组织方面作用重大；但是C含量过高，会影响钢的塑性和耐腐蚀性能，因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层中控制C的质量百分比在0.02～0.15％。
Si：Si是铁素体形成元素，同时Si含量过高会降低铬镍奥氏体不锈钢的耐蚀性并提高钢在固溶态的晶间腐蚀敏感性，因此为保证钢在室温下为奥氏体组织及其耐腐蚀性能，需要控制钢中的Si含量；但是在奥氏体不锈钢冶炼过程中，Si作为脱氧剂使用，钢中又必须含有一定含量的Si，因此，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层中控制Si的质量百分比控制在0.3～1.0％。
Mn：Mn是弱奥氏体形成元素，但在不锈钢中是强奥氏体稳定元素，并且Mn能够显著提高N在钢中的溶解度，当N含量较高Ni含量较低时，需要一定量的Mn元素，通过Mn、N、C的复合作用代替部分Ni，稳定奥氏体组织；但是Mn对不锈钢的耐腐蚀性能有负面影响，Mn含量太高会降低钢的耐点蚀、耐缝隙腐蚀性能，因此，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层控制Mn的质量百分比在1.0～10.5％。
Cr：Cr是不锈钢中最重要的合金元素，是保证不锈钢耐蚀性的最基本元素，随着钢中Cr含量增加，不锈钢的晶间腐蚀敏感性降低，强度提高，但塑性和冷成型性能会降低，同时过高的Cr将需要相应高的Ni当量与之配合，以保证获得室温奥氏体组织。因此，综合考虑，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层控制Cr的质量百分比在14.0～20.0％。
Ni：Ni是重要的奥氏体形成和稳定元素，能促进不锈钢钝化膜的稳定性，降低韧脆转变温度，提高冷成型性和焊接性，同时Ni也是昂贵的元素，对奥氏体不锈钢的成本有重要影响，因此，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层控制Ni的质量百分比在0.2～14.0％。
N：N在奥氏体不锈钢中非常强烈的形成、稳定和扩大奥氏体相区的元素，通过固溶强化作用，N可以显著提高奥氏体不锈钢的室温和高温强度，并且不显著降低钢的塑韧性，同时N能提高奥氏体不锈钢的耐酸腐蚀性和耐局部腐蚀性能；由于N在不锈钢中的溶解度有限，为避免凝固过程中产生皮下气孔，N必须与其他元素协调作用保证以固溶态存在，综合考虑本发明中的Mn、C等合金元素的质量百分比，在本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层控制N≤0.25％。
Cu：Cu能提高奥氏体不锈钢的不锈性和耐蚀性，特别是在硫酸等还原性介质中的作用更为明显，Cu能显著降低不锈钢的强度和冷加工硬化倾向；但是向以Mn、N代替Ni的铬锰奥氏体不锈钢中加入Cu，其延迟断裂敏感性要远低于铬镍奥氏体不锈钢，并且随着钢中Cu含量的增加，奥氏体不锈钢的热塑性降低，因此，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层控制Cu的质量百分比控制在≤0.6％。
Mo：添加Mo元素，可使奥氏体不锈钢其耐蚀性和高温强度有较大的提高，尤其是耐高温可达到1200-1300度，可在苛酷的条件下使用。因此，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层控制Mo的质量百分比控制在≤3.0％。
在本发明所述的碳钢奥氏体不锈钢轧制复合板中，不可避免的杂质元素应当控制得越低越好，但考虑到工艺水平以及制造成本的限制，因此，控制不可避免的元素例如P、S的质量百分比范围在P≤0.035％，S≤0.015％。P是钢中的杂质元素，对不锈钢的塑、韧性及耐蚀性都有不利影响，生产中要尽可能降低其含量，因此，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层中控制P≤0.035％，而S是钢中的杂质元素，对钢的高温塑、韧性及耐蚀性均有有害作用，生产中要尽可能降低其含量，因此，本发明所述的碳钢奥氏体不锈钢轧制复合板的奥氏体不锈钢层中控制S≤0.015％。
进一步地，在本发明所述的碳钢奥氏体不锈钢轧制复合板中，碳钢层的化学元素质量百分含量为：
C：0.05％～0.35％，Si：0.1％～2.0％，Mn：0.5％～3.0％，Al：0.01％～0.08％，余量为Fe和其他不可避免的杂质。
C：C元素的添加对提高钢的强度起关键作用，保证发生贝氏体或者马氏体相变以产生相变强化。C与合金元素析出细小弥散的金属碳化物以产生细晶强化和析出强化，但考虑到本案的碳钢奥氏体不锈钢轧制复合板的可焊接性，因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的C的质量百分比在0.05％～0.35％。
Si：Si是强化铁素体的元素，其可以有效地提高铁素体的强度。另外Si为非碳化物形成元素，在等温过程中，Si能够强烈抑制Fe3C的形成，使未转变的奥氏体富碳，从而大大提高奥氏体的稳定性，使其能够在室温下保留下来产生TRIP效应。基于此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中将Si的质量百分比控制在0.1％～2.0％。
Mn：Mn是碳化物形成元素，其会固溶拖拽碳，进而推迟珠光体转变，降低Bs点，抑制贝氏体相变，对马氏体形成窗口区间有重要作用。添力Mn降低马氏体转变温度，增加残余奥氏体的含量，同时Mn对钢板的韧性影响不大，当钢中包括质量百分比为1.5％～2.5％的Mn时，可以有效地提高残余奥氏体分解的抗力。但由于Mn对Ms点的降低较多，对焊接性有不利影响，故用量要适当，因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的Mn的质量百分比在0.5％～3.0％。
Al：添加Al起到了脱氧作用和细化晶粒的作用，Al和Si一样，也是非碳化物形成元素，能够强烈抑制Fe3C的形成，使未转变的奥氏体富碳。虽然Al的固溶强化效果弱于Si，但是在本发明所述的技术方案中，可以添加Al元素以降低硅的副作用，因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的Al的质量百分比在0.01％～0.08％。
进一步地，在本发明所述的碳钢奥氏体不锈钢轧制复合板中，碳钢层还含有下述各化学元素的至少其中之一：B≤0.005％，Nb≤0.1％，Ti≤0.15％，V≤0.15％，Cr≤0.6％，Mo≤0.3％。
B：硼能提高钢的淬透性，提高钢的淬透性的原因是在奥氏体转化过程中，新相(指铁素体)成核最容易在晶界处发生。但高于0.005％含硼钢就要出现热脆现象。因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的B的质量百分比在B≤0.005％。
Nb：在控制轧制过程中，Nb的应变诱导析出相通过质点钉扎和亚晶界的作用而相当显著的降低变形奥氏体的再结晶温度，提供形核质点，对细化晶粒作用明显。因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的Nb的质量百分比在Nb≤0.1％。
Ti：Ti是Ti-Mo-C系纳米析出物的主要化合元素，同时Ti在高温下也显示出一种强烈的抑制奥氏体晶粒长大从而细化晶粒的效果。因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的Ti的质量百分比在Ti≤0.15％。
V：V在控制轧制相变发生后，残留在奥氏体中的进一步在铁素体中析出，产生显著的析出强化效果。因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的V的质量百分比在V≤0.15％。
Cr：Mn和Cr都是碳化物形成元素，在考虑淬透性时，可以相互替换以保证强度。但添加Cr可以更好的推迟珠光体转变，使贝氏体相变区域左移，且对Ms点的降低作用小于Mn。但在低碳钢中Nb、Ti、V等碳氮化物生成元素太多会影响后续的相变，所以合金元素含量需要控制上限。Cr、Mo等提高淬透性的元素达到一定的量后会导致可焊接性能下降，因此也需要控制上限。因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的Cr的质量百分比在Cr≤0.6％。
Mo：Mo能显著提高淬透性。Mo通过固溶拖拽碳显著地推迟珠光体转变，而对先析铁素体析出的推迟作用较小。Mo对Bs点的降低作用大于Cr，小于Mn，故对奥氏体亚稳定的作用也大于Cr。另外，Mo是影响纳米析出物产生的最重要化合元素。Mo能提高Ti(C，N)在奥氏体中的固溶度，使大量的Ti保持在固溶体中，以便在低温转变中弥散析出，从而产生较高的强化效果。
在低碳钢中Nb、Ti、V等碳氮化物生成元素太多会影响后续的相变，所以合金元素含量需要控制上限。Cr、Mo等提高淬透性的元素达到一定的量后会导致可焊接性能下降，因此也需要控制上限。因此，在本发明所述的碳钢奥氏体不锈钢轧制复合板中控制碳钢层的Mo的质量百分比在Mo≤0.3％。
进一步地，在本发明所述的碳钢奥氏体不锈钢轧制复合板中，碳钢奥氏体不锈钢轧制复合板的抗拉强度为780-1700MPa。
本发明所述的碳钢奥氏体不锈钢轧制复合板的制造方法相较于现有技术具有如下所述的优点以及有益效果：
本发明所述的碳钢奥氏体不锈钢轧制复合板具有奥氏体不锈钢层，同时具有为整体钢板提供不同特定力学性能基础的碳钢层，从而使得最终钢板具有从780MPa-1700MPa的不同强度级别，并且具有优秀的抗腐蚀能力。
具体实施方式
下面将结合具体的实施例对本发明所述的碳钢奥氏体不锈钢轧制复合板及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-6
实施例1-6的碳钢奥氏体不锈钢轧制复合板采用以下步骤制得：
(1)按照表1所示的化学成分制得碳钢层坯料和奥氏体不锈钢层坯料；
(2)组坯；
(3)复合轧制：将坯料加热至1150-1260℃，保温0.6小时以上，控制终轧温度大于850℃，轧后以30-100℃/s的速度冷却，控制卷取温度为450-600℃；
(4)冷轧：控制冷轧压下率为40-70％；
(5)第一次退火：退火温度为1050-1150℃，保温时间大于30s；然后冷却至室温，在该冷却过程中，在900-500℃的温度范围内进行快速冷却，控制冷却速度为20-200℃/s；
(6)第二次退火：以大于5℃/s的加热速度加热至均热温度800-950℃，保温10-100s，然后以v1＝5-20℃/s的速度冷却到快冷开始温度T，快冷开始温度T≥800-10×v1，然后再以20-1000℃/s的速度冷却到150-450℃；然后进行过时效处理，过时效温度为150-450℃，过时效处理时间为100-400s。
而在一些其他的实施方式中，还包括步骤(7)平整。
表1列出了1-6的碳钢奥氏体不锈钢轧制复合板的各化学元素的质量百分配比。
表1.(wt％，余量为Fe和其他不可避免的杂质)
Figure BDA0002294806280000081
Figure BDA0002294806280000091
表2-1以及表2-2列出了实施例1-6的碳钢奥氏体不锈钢轧制复合板的具体工艺参数。
表2-1.
Figure BDA0002294806280000092
表2-2.
Figure BDA0002294806280000101
为了验证本案的实施效果，同时证明本案较之现有技术的优异效果，本案将实施例1-6的碳钢奥氏体不锈钢轧制复合板进行测试，测试结果列于表3。
表3.
Figure BDA0002294806280000102
由表3可以看出，本案各实施例的碳钢奥氏体不锈钢轧制复合板的抗拉强度在802-1710MPa，屈服强度在514-1390MPa，延伸率在7.3-15.4％。点腐蚀测试按照GB/T17899-1999不锈钢点蚀电位测量方法进行，晶间腐蚀性能测试按照ASTM G108-94进行，由表3可以看出，本案各实施例的点腐蚀电位在0.29～0.42V，晶间腐蚀在0.26～0.4Ra，由此说明本案各实施例的耐蚀性能优异。
综上所述，采用本发明所述的方法制得的碳钢奥氏体不锈钢轧制复合板具有保证抗腐蚀能量的奥氏体不锈钢层，同时具有为整体钢板提供不同特定力学性能基础的碳钢层，从而使得最终钢板具有从780MPa-1700MPa的不同强度级别，并且具有优秀的抗腐蚀能力。
需要说明的是，本发明的保护范围中现有技术部分并不局限于本申请文件所给出的实施例，所有不与本发明的方案相矛盾的现有技术，包括但不局限于在先专利文献、在先公开出版物，在先公开使用等等，都可纳入本发明的保护范围。
此外，本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，以上所列举的实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的，均应属于本发明的保护范围。

Claims (9)

1.一种碳钢奥氏体不锈钢轧制复合板的制造方法，其特征在于，其包括步骤：
(1)制得碳钢层坯料和奥氏体不锈钢层坯料；
(2)组坯；
(3)复合轧制；
(4)冷轧；
(5)第一次退火：退火温度为1050-1150℃，保温时间大于30s；然后冷却至室温，在该冷却过程中，在900-500℃的温度范围内进行快速冷却，控制冷却速度为20-200℃/s；
(6)第二次退火：以大于5℃/s的加热速度加热至均热温度800-950℃，保温10-100s，然后以v1＝5-20℃/s的速度冷却到快冷开始温度T，所述快冷开始温度T≥800-10×v1，然后再以20-1000℃/s的速度冷却到150-450℃；然后进行过时效处理，过时效温度为150-450℃，过时效处理时间为100-400s。
2.如权利要求1所述的制造方法，其特征在于，在步骤(3)中，将坯料加热至1150-1260℃，保温0.6小时以上，控制终轧温度大于850℃，轧后以30-100℃/s的速度冷却，控制卷取温度为450-600℃。
3.如权利要求1所述的制造方法，其特征在于，在步骤(4)中，控制冷轧压下率为40-70％。
4.如权利要求1所述的制造方法，其特征在于，还包括步骤(7)平整。
5.一种碳钢奥氏体不锈钢轧制复合板，其采用如权利要求1-4中任意一项所述的制造方法制得。
6.如权利要求5所述的碳钢奥氏体不锈钢轧制复合板，其特征在于，其中奥氏体不锈钢层的化学元素质量百分含量为：C：0.02％～0.15％，Si：0.3％～1.0％，Mn：1.0％～10.5％，Cr：14.0～20.0％，Ni：0.2～14.0％，N≤0.25％，Cu≤0.6％，Mo≤3.0％，余量为Fe和其他不可避免的杂质。
7.如权利要求6所述的碳钢奥氏体不锈钢轧制复合板，其特征在于，所述碳钢层的化学元素质量百分含量为：
C：0.05％～0.35％，Si：0.1％～2.0％，Mn：0.5％～3.0％，Al：0.01％～0.08％，余量为Fe和其他不可避免的杂质。
8.如权利要求7所述的碳钢奥氏体不锈钢轧制复合板，其特征在于，所述碳钢层还含有下述各化学元素的至少其中之一：B≤0.005％，Nb≤0.1％，Ti≤0.15％，V≤0.15％，Cr≤0.6％，Mo≤0.3％。
9.如权利要求5-8中任意一项所述的碳钢奥氏体不锈钢轧制复合板，其特征在于，所述碳钢奥氏体不锈钢轧制复合板的抗拉强度为780-1700MPa。
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