CN108570605A - 基于双辊连铸的高强度高塑性低密度钢板及其制造方法 - Google Patents
基于双辊连铸的高强度高塑性低密度钢板及其制造方法 Download PDFInfo
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- CN108570605A CN108570605A CN201810509455.4A CN201810509455A CN108570605A CN 108570605 A CN108570605 A CN 108570605A CN 201810509455 A CN201810509455 A CN 201810509455A CN 108570605 A CN108570605 A CN 108570605A
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- continuous casting
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- 238000005097 cold rolling Methods 0.000 claims abstract description 19
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- REDXJYDRNCIFBQ-UHFFFAOYSA-N aluminium(3+) Chemical compound data:image/svg+xml;base64,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 data:image/svg+xml;base64,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 [Al+3] REDXJYDRNCIFBQ-UHFFFAOYSA-N 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminum Chemical compound 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- 238000005265 energy consumption Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N manganese Chemical compound 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[Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N phosphorus Chemical compound 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[Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
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- 239000000126 substance Substances 0.000 description 1
- 230000001131 transforming Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
-
- 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
- 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
- C21D8/0221—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
-
- 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
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
Abstract
一种基于双辊连铸的高强度高塑性低密度钢板及其制造方法，成分按质量百分比为：C 0.3～0.6％，Mn 13～20％，Al 5.8～6.8％，Ni 2.5～4.5％，Si<0.1％，S<0.01％，P<0.01％，Ti 0～0.07％，Nb 0～0.1％，V 0～0.1％，余量为Fe；抗拉强度为950～1000MPa，延伸率为40～50％，密度6.5～7.5g/cm3；制造方法为：(1)冶炼钢水；(2)经中间包流入由双辊连铸机，经过辊缝凝固并导出薄带；(3)以50～100℃/s的速率冷却至室温，酸洗后冷轧；(4)加热至650～780℃并保温，以100～180℃/s的冷却至室温。本发明的方法省去了众多工序，显著降低生产成本，钢板兼具高强度和高塑性。
Description
基于双辊连铸的高强度高塑性低密度钢板及其制造方法
技术领域
[0001]本发明属于先进高强钢生产技术领域，具体涉及一种基于双辊连铸的高强度高塑 性低密度钢板及其制造方法。
背景技术
[0002]近年来，随着经济和工业的快速发展，资源匮乏和环境约束等问题日趋明显;为满 足轻量化发展的^求，开发了大量的先进高强度钢，国际钢铁协会（IISI)先进高强钢应用 指南第三版中将高强钢分为传统高强钢(Conventional HSS)和先进高强钢(AHSS);传统高 强钢主要包括碳锰(C-Mn)钢、烘烤硬化(BH)钢、高强度无间隙原子(HSS-IF)钢和高强度低 合金(HSLA)钢;先进高强钢(AHSS)主要包括双相(DP)钢、相变诱发塑性(TRIP)钢、马氏体 ⑽钢、复相(CP)钢、热成形(HF)钢和孪晶诱发塑性(TWIP)钢;传统的高强钢多是通过固溶、 析出和细化晶粒作为主要强化手段，而先进高强钢(AHSS)是指通过相变进行强化的钢种， 组织中含有马氏体、贝氏体和/或残余奥氏体，包括双相钢(DP)、孪晶诱发塑性(TRIP)钢、复 相钢(CP)和马氏体钢(Mart)等;与传统高强钢相比，先进高强钢是近年来出现的新型钢材， 具有高强度、高能量吸收性、高加工硬化率及优良的防撞凹性能、抗疲劳性能、烘烤硬化和 成形性能等一系列优点，广泛应用于汽车、桥梁工程、输电塔、海洋平台、油气输送管道和船 舶制造等行业，在理论研究和实际应用上引起了人们极大的关注。
[0003]近年来，世界各国纷纷致力于先进高强钢的研究开发;其中，Fe-Al-Mn-C系高强钢 根据化学成分的变化，其室温显微组织可能为单相奥氏体或奥氏体和铁素体双相，且纳米 级(Fe，Mn)3AlC型k-碳化物在其间弥散分布，主要是利用奥氏体的TWIP效应和多相协调变 形来达到提高强度和塑性的目的；但是含有K-碳化物的Fe-Al-Mn-C钢应变强化速率较低， 容易受到位错滑移产生的切应力的影响，不利于获得良好的塑性;迄今为止，在对Fe-Al-Mn-C系高强钢的研宄中，在合金成分设计上采用的理念一直是通过使“韧性”奥氏体晶体结 构保持稳定并抑制金属间化合物脆性相的生成，从而得到良好塑性的钢板;这是由于一旦 在钢材中形成一定量的金属间化合物脆性相，虽然会在一定程度上提高其强度，但是同时 也会大大降低其塑性;从青铜时代起，人们就一直在寻求合金材料“轻量、强度、韧性”这三 大性能指标的平衡，不过，强度和韧性却始终是相互排斥的，很难达在获得高强度的同时仍 然保证良好的塑性。
[0004] 双辊连铸技术是一种短流程、低能耗、污染小、成本低的绿色环保新工艺技术;双 辊连铸技术作为当今世界上薄带钢生产的前沿技术，可省去厚板坯连铸、加热和热连轧等 工序，由液态钢水直接生产出厚度为1〜6mm的薄带;但是，利用双辊连铸生产出来的薄带的 初始组织较粗大，强韧性较差;此外，由于初始规格薄，后续加工变形量不足，故难以大幅度 细化晶粒，钢材的力学性能不尽如人意；因此，如何在双辊连铸条件下生产一种兼具高强度 和高塑性的钢板成为所面临的一个亟待解决的关键问题。
发明内容
[0005]针对现有技术存在的上述问题，本发明提供及一种基于双辊连铸的高强度高塑性 低密度钢板及其制造方法，目的是解决先进高强钢传统生产流程工艺复杂、制造工序多、能 耗大、环境负荷大等问题，同时利用细小弥散的脆性金属间化合物NiAl相生产出一种兼具 高强度和高塑性的钢板。
[0006]本发明的基于双辊连铸的高强度高塑性低密度钢板成分按质量百分比为:c 〇. 3 〜0.6%，Mn 13〜20%，A1 5.8〜6.8%，Ni 2.5〜4.5%，Si<0.1%，S<0.01%，P<0.01%，Ti 0〜0.07%，Nb 0〜0.1%，V 0〜0.1%，余量为Fe及不可避免杂质；抗拉强度为950〜 lOOOMPa，延伸率为40〜50%，密度6 • 8〜7.5g/cm3。
[0007]上述的基于双辊连铸的高强度高塑性低密度钢板的组织为奥氏体和脆性金属间 化合物NiAl构成的双相组织，厚度为0.5〜1.5mm。
[000S]本发明的基于双辊连铸的高强度高塑性低密度钢板的制造方法按以下步骤进行： [0009] 1、按上述成分冶炼钢水；
[0010] 2、将钢包内的钢水经中间包流入由双辊连铸机的两个反向旋转的结晶辊和侧封 板组成的空腔内形成熔池，钢水经过两个结晶辊之间的辊缝凝固并导出薄带，导出速度为 2〇〜8〇m/min，形成2〜5mm厚的连铸薄带；
[0011] 3、将连铸薄带以50〜KKTC/s的冷却速率冷却至室温，酸洗后冷乳至〇.5〜1.5mm， 制成冷乳板；
[0012] 4、采用退火炉将冷乳板加热至650〜780°C并保温30〜90min，随后以100〜18(TC/ s的冷却速率冷却至室温，得到基于双辊连铸的高强度高塑性低密度钢板。
[0013]上述方法中，冷乳的总压下率为6〇〜75%。
[00M]与现有技术相比，本发明的特点和有益效果是:省去了先进高强钢传统生产流程 的厚板坯连铸、粗乳、热连轧、冷乳前热处理等工序，显著降低生产成本、能耗及污染物排 放，有效提高了成材率和生产效率，是一种短流程制造技术;其次，通过添加含量为2.5〜 4.5%的镍元素，利用镍元素的催化作用，促进脆性金属间化合物B2有序相（g卩NiAl相)经退 火后在钢中的奥氏体冷轧剪切带和变形带上形核，并控制NiAl相在基体中分布；同时退火 温度较低，此时奥氏体并未全部完成再结晶，剪切带和变形带等亚结构组织能够利于提高 强度;此外，利用已完成再晶界的奥氏体基体来保证良好的塑性，从而使钢板兼具高强度和 高塑性;通过严格控制(：、^111、听、八1的含量而省略了热乳步骤，避开了高41钢因热加工性能 差而热乳开裂的情况，同时还使得薄带能够直接进行冷轧，而不需要之前的固溶处理或软 化退火，显著缩短了工艺流程。
[0015]本发明中钢板成分设计依据如下：
[0016] C:能够起到稳定奥氏体基体、固溶强化提高强度等作用。但是c容易与Al、Mn形成 k-碳化物，为脆性相，不利于获得高塑性;且C含量过高，会导致钢板硬度增加，不利于直接 冷轧，因此C含量为0.3〜0.6 % ;
[0017] A1:可形成k-碳化物或脆性金属间化合物B2相(NiAl)，二者均不利于获得高塑性； 但适量NiAl可在一定程度上提高钢板强度；因此，需要对A1的含量进行严格控制，形成适量 的脆性金属间化合物B2相(NiAl);此外，A1含量过高，不利于双辊连铸时薄带的成形情况和 成功率，因此A1含量为5.8〜6.8 % ;
[0018] Mn:稳定奥氏体基体，保证良好的塑性;保证层错能处于18〜35mJ/m2,变形机制为 TWIP效应，从而保证良好的塑性，因此Mn含量为13〜20%;
[0019]附：形成脆性金属间化合物B2相(NiAl)，提高钢板强度;但是含量过高会导致NiAl 相数量过多，尺寸过于粗大，严重恶化塑性，因此Ni含量为2.5〜4.5 % ;
[0020] Ti:是一种强碳氮化物形成元素，可以形成细小弥散分布的碳氮化物，起到细化奥 氏体晶粒的作用；但是若含量过高，形成十分粗大的碳氮化物而不能起到阻止晶粒长大的 作用，显著降低钢的塑性和韧性;因此Ti含量应控制在0.07%以内；
[0021 ] Nb:形成碳氮化物能够细化晶粒，同时固溶铌可以提高未再结晶区温度，易于通过 控制乳制实现奥氏体的扁平化;高于0.10%时作用增加不明显，达到饱和；因此Nb含量应控 制在0.1%以内；
[0022] V:以细小的碳氮化物形成存在时，能够细化晶粒；以固溶形式存在时，能够提高强 度。适量加入可以改善性能，高于0.15%时易形成大颗粒碳氮化物，反而使韧塑性下降；另 外，V还具有析出强化作用，可进一步提高钢的强度;因此V含量应控制在0.1 %以内。
[0023]本发明制造方法中薄带导出结晶辊的速度为20〜80m/min是为了不影响薄带的板 形;薄带经冷却系统以50〜100 °C/s的冷却速率冷却至室温为了避免k-碳化物和NiAl有序 相形成，不利于直接冷轧;薄带厚度和冷乳最终厚度的控制是为了保证获得足够多的剪切 带和变形带，为NiAl相提供形核位点；退火是为了为脆性金属间化合物B2相(NiAl)的形核 和长大提供足够的驱动力，最终在室温获得一定量且均匀细小、弥散分布的NiAl有序相，同 时该退火温度、时间区间可使得微观组织中存在一定量的变形带等亚结构，从而提高钢板 的强度；退火后以100〜180°C/s的冷却速率冷却至室温是为了避免k-碳化物脆性相的形 成，不利于获得高塑性。
附图说明
[0024]图1是本发明制造方法的工艺流程示意图；
[0025] 其中：1、钢包，2、中间包，3、双辊连铸机结晶辊，4、熔池，5、连铸薄带，6、酸洗机，7、 冷乳机，8、退火炉。
[0026]图2是本发明实施例1的基于双辊连铸的高强度高塑性低密度钢板的微观组织扫 描电镜EBSD图，图中亮白色为NiAl相；
[0027]图3是本发明实施例2的基于双辊连铸的高强度高塑性低密度钢板的微观组织扫 描电镜EBSD图，图中亮白色为NiAl相；
[0028] 图4是本发明实施例3的基于双辊连铸的高强度高塑性低密度钢板的微观组织扫 描电镜EBSD图，图中亮白色为NiAl相。
具体实施方式
[0029] 本发明实施例中微观组织电镜扫描采用的设备为德国蔡司制造的场发射扫描电 子显微镜，型号为Zeiss Ultra 55。
[0030] 本发明的工艺流程如图1所示。
[0031] 本发明实施例中以50〜100。(： /s的冷却速率冷却至室温是选用水冷方式。
[0032] 实施例1
[0033]冶炼钢水，其成分按质量百分比为:C 〇_5%，Mn 15_6%，A1 6‘2%，Ni 2_8%，Si 0.06%，Ti 0.04%，S 0.002%，P 0.002%，余量为Fe及不可避免杂质；
[0034]将钢包内的钢水经中间包流入由双辊连铸机的两个反向旋转的结晶辊和侧封板 组成的空腔内形成熔池，钢水经过两个结晶辊之间的辊缝凝固并导出薄带，导出速度为 50m/min，形成2.5ram厚的连铸薄带；
[0035]将连铸薄带以7(TC/s的冷却速率冷却至室温，酸洗后冷乳至lmm，制成冷乳板;冷 乳压下率为60%;
[0036] 采用退火炉将冷乳板加热至780°C保温55min，随后以160°C/s的冷却速率冷却至 室温，得到基于双辊连铸的高强度高塑性低密度钢板，其抗拉强度为954MPa，延伸率为 48%，密度7.2g/cm3,组织为奥氏体和脆性金属间化合物NiAl构成的双相组织，EBSD图如图 2所示。
[0037] 实施例2
[0038] 方法同实施例1，不同点在于：
[0039]⑴钢水成分按质量百分比为：C 0.44%，Mn 16.8%，A1 6.3%，Ni 3.6%，Si 0.06%,Ti 0.06%,S 0.002%,P 0.002%
[0040] ⑵连铸的导出速度为60m/min，连铸薄带厚3.1mm;
[0041] (3)连铸薄带以60°C/s的冷却速率冷却至室温，酸洗后冷轧至1.2mm;冷乳压下率 为 61 %;
[0042] ⑷加热至710°C保温40min，以15(TC/s的速率冷却；
[0043] (5)基于双辊连铸的高强度高塑性低密度钢板的抗拉强度985MPa，延伸率44%，密 度7g/cm3，EBSD图如图3所示。
[0044] 实施例3
[0045] 方法同实施例1，不同点在于：
[0046] (1)钢水成分按质量百分比为：c 0.55%，Mn 16.8%，A1 6%，Ni 4.3%，Si 0.06%,Ti 0.03%,S 0.003%,P 0.005%
[0047] ⑵连铸的导出速度为60ra/min，连铸薄带厚4mm;
[0048] (3)连铸薄带以5(TC/S的冷却速率冷却至室温，酸洗后冷轧至1mm;冷轧压下率 75%；
[0049] ⑷加热至770°C保温80min，以18(TC/s的速率冷却；
[0050] ⑸基于双辊连铸的高强度高塑性低密度钢板的抗拉强度993MPa，延伸率41%，密 度7 • 3g/cm3，EBSD图如图4所示。
[0051] 实施例4
[0052] 方法同实施例1，不同点在于：
[0053] (1)钢水成分按质量百分比为：c 0.3%，Mn 13.1%，A1 6.8%，Ni 4.3%，Si 0.08%，S 0.004%，P 0.006%
[0054] ⑵连铸的导出速度为20m/min，连铸薄带厚5mm;
[0055] (3)连铸薄带以80°C/s的冷却速率冷却至室温，酸洗后冷轧至l_5mm;冷轧压下率 70%；
[0056] ⑷加热至780°C保温30min，以18(TC/s的速率冷却；
[0057] (5)基于双辊连铸的高强度高塑性低密度钢板的抗拉强度％7MPa，延伸率46%，密 度6.9g/cm3。
[0058] 实施例5
[0059] 方法同实施例1，不同点在于：
[0060]⑴钢水成分按质量百分比为：C 0.6%，Mn 19.6%，A1 5.8%，Ni 2.5%，Si 0.02%,V 0.1%,S 0.007%,P 0.006%
[0061] (2)连铸的导出速度为3〇m/min，连铸薄带厚4.5mm;
[0062] (3)连铸薄带以100°C/s的冷却速率冷却至室温，酸洗后冷乳至1.4mm;冷轧压下率 69%；
[0063] ⑷加热至650°C保温90min，以100°C/s的速率冷却；
[0064] (¾基于双辊连铸的高强度高塑性低密度钢板的抗拉强度979MPa，延伸率奶％，密 度7.5g/cm3。
[0065] 实施例6
[0066] 方法同实施例1，不同点在于：
[0067] (1)钢水成分按质量百分比为：C 0.32%，Mn 14.4%，A1 6.1%，Ni 4.5%，Si 0.05%,Ti 0.07%,V 0.02%,S 0.005%,P 0.003%
[0068] ⑵连铸的导出速度为80m/min，连铸薄带厚3.8mm;
[0069] (3)连铸薄带以9(TC/s的冷却速率冷却至室温，酸洗后冷轧至1.2圓;冷乳压下率 68%；
[0070] ⑷加热至750°C保温50min，以16(TC/s的速率冷却；
[0071] (5)基于双辊连铸的高强度高塑性低密度钢板的抗拉强度988MPa，延伸率42%，密 度7.2g/cm3。
[0072] 实施例7
[0073]方法同实施例1，不同点在于：
[0074] (1)钢水成分按质量百分比为：c 0_43%，Mn 17.3%，A1 6.4%，Ni 3.1%，Si 0.07%,Nb 0.1%,S 0.004%,P 0.002%
[0075] ⑵连铸的导出速度为45m/min，连铸薄带厚3 • 6mm;
[0076] (3)连铸薄带以80°C/s的冷却速率冷却至室温，酸洗后冷轧至1.2mm;冷轧压下率 67%；
[0077] ⑷加热至700°C保温70min，以14(TC/s的速率冷却；
[0078] (5)基于双辊连铸的高强度高塑性低密度钢板的抗拉强度9%MPa，延伸率47%，密 度7g/cm3。
[0079] 实施例8
[0080] 方法同实施例1，不同点在于：
[0081] (1)钢水成分按质量百分比为：C 0.51%，Mn 15.5%，A1 6.7%，Ni 3.2%，Si 0.01%,Ti 0.03%,Nb 0.02%,V 0.02%,S 0.002%,P 0.005%
[0082] ⑵连铸的导出速度为70m/min，连铸薄带厚2mm;
[0083] (3)连铸薄带以70°C/s的冷却速率冷却至室温，酸洗后冷轧至0_5mm;冷轧压下率 75%；
[0084] ⑷加热至68〇°C保温75min，以12(TC/s的速率冷却；
[0085] (5)基于双辊连铸的高强度高塑性低密度钢板的抗拉强度991MPa，延伸率49。/ + 度 6.9g/cm3。 °’$
[0086] 对比例1
[0087] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0088] 钢水按质量百分比含C 0.26% (即降低含碳量）；
[0089] 制成的钢板抗拉强度为902MPa，延伸率为43%。
[0090] 对比例2
[0091] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0092] 钢水按质量百分比含C 0.65% (即提高含碳量）；
[0093] 制成的钢板抗拉强度为1020MPa，延伸率为35%。
[0094] 对比例3
[0095] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0096] 钢水按质量百分比含Ni 2.2% (即降低镍含量）；
[0097] 制成的钢板抗拉强度为921MPa，延伸率为42%。
[0098] 对比例4
[0099] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0100] 钢水按质量百分比含Ni 4.7% (即提高镲含量）；
[0101]制成的钢板抗拉强度为988MPa，延伸率为28%。
[0102] 对比例5
[0103] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0104] 钢水按质量百分比含Mn 24% (即提高锰含量）；
[0105] 制成的钢板抗拉强度为903MPa，延伸率为52%。
[0106] 对比例6
[0107] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0108] 钢水按质量百分比含Mn 11.5% (即降低锰含量）；
[0109] 制成的钢板抗拉强度为961MPa，延伸率为38%。
[0110] 对比例7
[0111] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0112] 连铸薄带的厚度6mm (即提高连铸薄带的厚度，相当于增大冷乳的总压下率）；
[0113] 制成的钢板抗拉强度为10321?&，延伸率为36%。 ’
[0114] 对比例8
[0115] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0116] 冷轧至1.8ram (冷乳压下率减少至42%);
[0117] 制成的钢板抗拉强度为936MPa，延伸率为44%。
[0118] 对比例9
[0119] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0120] 钢水按质量百分比含A1 5.3% (即降低铝含量）；
[0121] 制成的钢板抗拉强度为910MPa，延伸率为46%。
[0122] 对比例10
[0123] 以实施例2为对比进行对比试验，与实施例2的不同点在于： 一--i-
[0124] 钢水按质量百分比含A1 7% (即提高铝含量）；
[0125] 制成的钢板抗拉强度为1033MPa，延伸率为29%。
[0126] 对比例11
[0127] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0128] 冷乳板在620°C保温40min(即降低冷乳退火温度）；
[0129] 制成的钢板抗拉强度为880MPa，延伸率为15%。
[0130] 对比例12
[0131] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0132] 冷轧板在850°C保温40min (即提高冷乳退火温度）；
[0133]制成的钢板抗拉强度为922MPa，延伸率为43%。
[0134] 对比例13
[0135]以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0136] 冷轧板在71(TC保温110min(即延长冷乳退火时间）；
[0137] 制成的钢板抗拉强度为1026MPa，延伸率为32%。
[0138] 对比例14
[0139] 以实施例2为对比进行对比试验，与实施例2的不同点在于：
[0M0] 冷轧板在71(TC保温20min(即缩短冷轧退火时间）；
[0141] 制成的钢板抗拉强度为895MPa，延伸率为44%。
[0142]从以上对比可以看出，对比例中钢板的抗拉强度或延伸率显著低于本发明的实施 效果。
Claims (4)
1.一种基于双辊连铸的高强度高塑性低密度钢板，其特征在于成分按质量百分比为:c 0.3〜0.6%，Mnl3〜20%，A15.8〜6.8%，Ni2.5〜4.5%，Si〈0.1%，S<0.01%，P< 0.01%，Ti 0〜0.07%，Nb 0〜0.1%，V 0〜0.1%，余量为Fe及不可避免杂质；抗拉强度为 950〜lOOOMPa，延伸率为40〜50%，密度6.5〜7.5g/cm3。
2. 根据权利要求1所述的一种基于双辊连铸的高强度高塑性低密度钢板，其特征在于 组织为奥氏体和脆性金属间化合物NiAl构成的双相组织，厚度为0.5〜1.5mm。
3. —种权利要求1所述的基于双辊连铸的高强度高塑性低密度钢板的制造方法，其特 征在于按以下步骤进行： (1) 按上述成分冶炼钢水； (2) 将钢包内的钢水经中间包流入由双辊连铸机的两个反向旋转的结晶辊和侧封板组 成的空腔内形成熔池，钢水经过两个结晶辊之间的辊缝凝固并导出薄带，导出速度为20〜 80m/min，形成2〜5mm厚的连铸薄带； (3) 将连铸薄带以50〜100°C/s的冷却速率冷却至室温，酸洗后冷轧至0.5〜1.5圆，制 成冷乳板； ⑷采用退火炉将冷乳板加热至650〜78(TC并保温30〜90min，随后以100〜180°C/s的 冷却速率冷却至室温，得到基于双辊连铸的高强度高塑性低密度钢板。
4. 根据权利要求1所述的基于双辊连铸的高强度高塑性低密度钢板的制造方法，其特 征在于步骤(3)中冷轧的总压下率为60〜75%。
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