CN115261723A - 一种抗拉强度650MPa级热轧双相高耐蚀钢板及其制造方法 - Google Patents
一种抗拉强度650MPa级热轧双相高耐蚀钢板及其制造方法 Download PDFInfo
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Abstract
本发明公开了一种抗拉强度650MPa级热轧双相高耐蚀钢板及其制造方法,属于钢铁材料制造领域。本发明的钢板,其化学成分质量百分比含量(wt%)为:C:0.010%~0.030%、Si:0.50%~0.70%、Mn:0.25%~0.55%、P:0.020%~0.030%、S:≤0.002%、Cr:3.00%~4.50%、Ni:≤0.10%、Cu:0.20%~0.35%、Als:0.020%~0.050%、Ti:0.015%~0.025%、Ca:0.0010%~0.0030%,其余为Fe和不可避免的杂质元素。本发明采用高Cr含量设计,添加适量的Si、P,通过Cr、Si、P、Cu、Ni多种元素协同作用,提高材料的耐大气腐蚀性能,实现贵重合金Ni的减量化,从而降低高耐蚀钢制造成本。
Description
技术领域
本发明属于钢铁材料制造领域,更具体地说,涉及一种抗拉强度650MPa级热轧双相高耐蚀钢板及其制造方法。
背景技术
耐候钢又称为耐大气腐蚀钢,是在普通碳钢的基础上添加Cu、P、Cr、Ni等合金元素的低合金钢。耐候钢构件在服役过程中,基体表面能形成一层以α-FeOOH为主的致密保护性锈层,阻止空气中的氧气、水等腐蚀性介质向基体扩散,具有良好的耐大气腐蚀性能,广泛应用于铁道车辆、集装箱、桥梁、建筑、塔架等户外长期暴露在大气中的钢结构及装备制造,延长服役寿命。耐候钢作为低碳绿色钢铁材料,可降低全生命周期对资源、能源等的消耗,减少碳排放,具有广阔的推广应用前景。近年来,随着铁道车辆、集装箱等向着长寿命、轻量化、重载化等方向发展,耐候钢材料也向着高耐蚀、高强度升级。
CN 102409253 A公开了一种高耐蚀高强度铁道车辆用耐候钢及其制造方法,其化学成分质量百分比含量(wt%)为:C:0.015%~0.065%、Si:0.10%~0.50%、Mn:0.20%-0.60%、P:0.015%以下、S:0.008%以下、Ti:0.01%~0.08%、Nb:0.005%~0.05%、Cr:2.15%~4.0%、Ni:0.12%~1.0%,Cu:0.20%~0.60%、Al:0.01%~0.05%,余量为Fe及不可避免的杂质。其钢的屈服强度≥550MPa,抗拉强度≥650MPa,屈强比>0.80。且添加贵重微合金元素Nb、Ni含量较高,提高了制造成本。
CN105296885A公开了一种含钛高铬耐候钢及其制备方法,其化学成分质量百分比含量(wt%)为C≤0.07%,Si≤0.50%,Mn≤1.5%,P≤0.02%,S≤0.010%,Cu:0.20-0.55%,Cr:3.0-5.5%,Ni:0.10-0.65%,Ti:0.04-0.10%,其余为Fe和不可避免的杂质。其钢的屈服强度480-530MPa,抗拉强度580-650MPa,屈强比>0.79。且贵重合金Ni的含量较高,提高了制造成本。
CN105274446 A公开了一种高铬耐候钢及其制备方法,化学成分质量百分比含量(wt%)为:C≤0.07%,Si≤0.50%,Mn≤1.5%,P≤0.02%,S≤0.010%,Cu:0.20-0.55%,Cr:4.5-5.5%,Ni:0.10-0.65%,Ti:0.01-0.03%,其余为Fe和不可避免的杂质。其钢的屈服强度450~510MPa,抗拉强度550~630MPa,屈强比>0.80。且Ni和Cr的含量较高,提高了制造成本。
上述申请案的钢屈强比都在0.79以上,且制造成本较高。本发明旨在提供一种热轧高耐蚀钢板,具有优异的耐大气腐蚀性能和低屈强比,能满足在大气环境下服役材料的长寿命需求,且制造成本较低。
发明内容
1、要解决的问题
针对现有高强度耐候钢制造成本较高的问题,本发明拟提供一种抗拉强度650MPa级的热轧双相高耐蚀钢板及其制造方法,该高耐蚀钢板具有优异的耐大气腐蚀性能,合金成本大幅降低,且具有较低的屈强比和优异的低温韧性,易加工成形,可用于大气环境下服役的装备及构件制造。
2、技术方案
为解决上述问题,本发明采用如下的技术方案。
本发明提供一种抗拉强度超过650MPa的热轧双相高耐蚀钢板,其化学成分质量百分比含量(wt%)为:C:0.010%~0.030%、Si:0.50%~0.70%、Mn:0.25%~0.55%、P:0.020%~0.030%、S:≤0.002%、Cr:3.00%~4.50%、Ni:≤0.10%、Cu:0.20%~0.35%、Als:0.020%~0.050%、Ti:0.015%~0.025%、Ca:0.0010%~0.0030%,其余为Fe和不可避免的杂质元素。
其中各元素设计原理如下:
C(碳):C是提高钢材强度最经济的元素,本发明将C含量设计为0.015%~0.030%,避免因C含量过高而恶化钢材的焊接性能,降低塑韧性。
Si(硅):Si能增加钢中铁素体体积分数,还能通过固溶强化提高材料强度。此外,Si还有利于细化腐蚀产物,促进钢材表面形成致密的保护性锈层从而提高耐大气腐蚀性能。本发明将Si含量设计为0.50~0.70%,避免因Si含量过高恶化钢材的焊接性能和表面质量。
Mn(锰):Mn是钢中重要的固溶强化元素之一,也是炼钢过程中的重要脱氧元素。本发明中Mn有助于提高奥氏体稳定性,扩大奥氏体相区,促进贝氏体组织转变。将其含量设计为0.25~0.55%,避免提高制造成本,且防止因Mn含量过高恶化钢材的焊接性能。
Als(铝):Al是钢中加入的主要脱氧元素,本发明中还能与N结合在高温析出AlN,细化奥氏体晶粒尺寸。但过高的Al会导致钢中氧化物夹杂增加,降低钢材的低温韧性和耐大气腐蚀性能。本发明将其含量设计为0.020~0.050%。
Cr(铬):Cr是提高钢材耐大气腐蚀性能重要的合金元素,能够在钢材表面富集促进致密的与基体粘附性好的保护性锈层生成,阻止氧气、水等腐蚀性介质向集体扩散。本发明中Cr还能提高材料淬透性,促进贝氏体组织生成。但Cr含量过高会恶化钢材的焊接性能,提高制造成本,本发明将Cr含量设计为3.00~4.50%。
Cu(铜):Cu能显著提高材料的耐大气腐蚀性能,与Cr复合作用时提高耐大气腐蚀性能效果更佳。但是Cu的熔点较低,只有1083℃,含量过高容易导致连铸漏钢,热轧过程中产生边部裂纹,本发明将Cu含量设计为0.20~0.35%。
Ni(镍):Ni能提高材料的自腐蚀电位,降低腐蚀倾向,提高耐大气腐蚀性能;本发明中还能与Cu反应生成高熔点的Cu-Ni二元合金相,有效阻止Cu引起的铜脆;但Ni是贵重金属元素,含量过高显著增加钢材制造成本,因此将Ni含量控制在≤0.10%。
Ti(钛):Ti是强氮化物形成元素,有助于抑制加热过程中奥氏体晶粒粗化,降低液相Cu在奥氏体晶界的富集程度,提高边部质量;焊接过程中能够抑制粗晶区奥氏体晶粒粗化,提高焊接热影响区的低温韧性。本发明将其含量控制在0.010%~0.025%。
Ca(钙):有助于促进非金属夹杂物球化,有利于提高材料的抗大气腐蚀性能,改善材料低温韧性。本发明将其含量控制在0.0010%~0.0030%。
P(磷):P是提高钢材耐大气腐蚀性能最经济的元素,还能通过固溶强化提高强度,但是含量过高容易在晶界偏聚降低钢材的低温韧性,增加焊接裂纹敏感性。本发明将P含量设计为0.020%~0.030%。
S(硫):S是钢中的有害残余元素,易于Mn反应生成MnS非金属夹杂,降低耐大气腐蚀性能。本发明将S含量设计为≤0.002%。
进一步地,本发明中Cu、P、Cr、Ni、Si元素的含量还需同时满足如下条件:参照美国材料与试验协会标准ASTM G101-01中修正的Legault-Leckie公式计算该钢种的耐候指数I,I=26.01(%Cu)+3.88(%Ni)+1.20(%Cr)+1.49(%Si)+17.28(%P)-7.29(%Cu)×(%Ni)-9.10(%Ni)×(%P)-33.39(%Cu)2。当I值≥6.0时,具有良好的耐大气腐蚀性能,且随着I值增加,材料的耐大气腐蚀性能增加。本发明还需满足I≥10.0。
本发明采用高Cr含量设计,添加适量的Si、P,通过Cr、Si、P、Cu、Ni多种元素协同作用,提高材料的耐大气腐蚀性能,实现贵重合金Ni的减量化,从而降低高耐蚀钢制造成本。
进一步地,本发明钢板的力学性能:屈服强度ReL≥450MPa,抗拉强度Rm≥650MPa,屈强比ReL/Rm≤0.75,延伸率A≥22%,经过180°冷弯(d=0a)和双倍冷弯无裂纹。
进一步地,本发明钢板金相组织为多边形铁素体+粒状贝氏体双相组织,其中铁素体平均晶粒尺寸10μm~12μm,铁素体体积分数65~70%。
本发明还提供了上述抗拉强度650MPa级热轧双相高耐蚀钢板的制造方法,其制造工艺流程包括:铁水预处理深脱硫→转炉顶底复合吹炼→炉外精炼→连铸→加热→轧制→分段冷却→卷取→冷却至室温。以下具体说明:
1、冶炼、精炼、连铸阶段
按照上述化学成分进行钢水冶炼,采用LF+RH精炼处理,提高钢水洁净度,RH真空脱碳时间≥5min,出站温度≥1570℃。钢水浇铸中包温度控制在1530℃~1550℃,采用专用保护渣进行保护浇铸。液面波动≤±5mm,连铸坯拉速控制在1.0~1.5m/min,投用动态轻压下提高连铸坯内部质量。
铸坯切割完成后直接装炉,不具备直装条件的铸坯进入保温坑缓冷,入加热炉温度≥500℃。不具备直装、热装条件的铸坯在保温坑内缓冷至室温,避免铸坯温降速度过快产生横裂纹。
2、加热及轧制,即热轧阶段
首先对板坯进行加热,一加温度≤1070℃,二加+均热时间≤90min,在炉时间120~200min,出炉温度1170℃~1230℃,促进奥氏体均匀化和合金元素在奥氏体中充分固溶;同时避免加热时间过长,低熔点Cu元素在奥氏体晶界富集,导致热轧卷边部产生裂纹缺陷。加热炉采用还原气氛,空气过剩系数小于1.0,减少加热过程中板坯表面Fe的氧化烧损,抑制Cu富集。
轧制分粗轧和精轧两个阶段进行。粗轧阶段轧制温度控制在1050℃以上,累计压下率≥80%,在高温下进行多道次大变形,促进形变奥氏体晶粒回复再结晶,细化奥氏体细化晶粒尺寸。精轧阶段采用7机架四辊轧机连轧,精轧开轧温度≤1030℃,累计变形量≥85%。通过累计大变形,增加形变奥氏体内的形变带和位错密度,增加铁素体相变形核点,细化相变后铁素体晶粒。控制精轧终轧温度为840~900℃。
3、分段冷却和卷取阶段
精轧结束后进行层流冷却,根据该材料的过冷奥氏体连续冷却相变特点,采用分段控制冷却获得铁素体+粒状贝氏体双相组织。钢板出精轧机后首先以50~70℃/s速度快速冷却至720~770℃,然后空冷7~10s,促进过冷奥氏体向铁素体转变。本发明中若空冷时间小于7s,则铁素体体积分数减少,导致材料强度过高,延伸率不足;若空冷时间大于10s,则铁素体体积分数增加,易导致铁素体晶粒粗化,降低材料的强度。空冷过后以30~50℃/s速度冷却至550~610℃进行卷取,剩余奥氏体转变为粒状贝氏体组织。本发明中若卷取温度高于610℃,则剩余奥氏体转变为铁素体,易降低材料的强度;若卷取温度低于550℃,则生成板条贝氏体组织或马氏体组织,易降低材料的塑性和韧性。卷取后自然冷却至室温。
3、有益效果
相比于现有技术,本发明的有益效果为:
(1)本发明的抗拉强度650MPa级热轧双相高耐蚀钢板,屈服强度ReL≥450MPa,抗拉强度Rm≥650MPa,屈强比ReL/Rm≤0.75,延伸率A≥22%。经过180°冷弯(d=0a)和双倍冷弯试样外侧面没有裂纹出现,具有良好的冷弯成形性能,便于下游用户制造加工。
(2)本发明的热轧双相高耐蚀钢板,采用低Mn,高Cr和Cu、Si、P、Ni的少量多元复合成分设计,减少贵重合金Ni的含量,降低合金成本,具有优异的耐大气腐蚀性能。相对于Q450NQR1普通耐候钢耐大气腐蚀性能提高1倍。
(3)本发明的热轧双相高耐蚀钢板的制造方法,通过化学成分和控轧控冷工艺协同设计,使得钢板金相组织为多边形铁素体+粒状贝氏体双相组织,铁素体平均晶粒尺寸10μm~12μm,铁素体体积分数65~70%,-40℃冲击吸收功KV2≥110J(冲击式样尺寸:5×10×55mm),通过软硬双相的控制,获得优异的强韧性匹配和低屈强比。
(4)本发明的热轧双相高耐蚀钢板制造方法,采用直装或热装轧制工艺,避免铸坯横裂纹,降低加热炉能耗和铸坯氧化烧损,提高生产效率和成材率,降低制造成本。
附图说明
图1为实施例2的钢板金相组织图;
图2为实施例4的钢板金相组织图。
具体实施方式
下面结合具体实施例和附图对本发明进一步进行描述。
各实施例及对比例的化学成分如表1所示。对比例1主要通过Cr、Ni、Cu元素匹配提高耐大气腐蚀性能,尤其是贵重合金Ni的含量较高,制造成本高。
表1本发明各实施例及对比例的化学成分
本发明采用传统热连轧板带流程进行轧制,工艺流程包括:铁水预处理深脱硫→转炉顶底复合吹炼→炉外精炼→连铸→加热→轧制→分段冷却→卷取→冷却至室温。按照上述化学成分进行钢水冶炼,并采用LF+RH精炼处理,连铸阶段投用动态轻压下以提高连铸坯内部质量。下述实施例中所得连铸板坯的厚度为230mm。铸坯切割完成后直接装炉,不具备直装条件的铸坯进入保温坑缓冷,入加热炉温度≥500℃。不具备直装、热装条件的铸坯在保温坑内缓冷至室温,避免铸坯温降速度过快产生裂纹。
具体各实施例及对比例热轧及冷却工序主要工艺参数及力学性能分别如表2和表3所示。拉伸性能测试根据GB/T 228.1《金属材料拉伸试验第1部分:室温试验方法》进行,冷弯性能测试根据GB/T 232《金属材料弯曲试验方法》进行,冲击性能测试根据GB/T 229《金属材料夏比摆锤冲击试验方法》进行。其中对比例1采用660℃高温卷取,屈服强度和抗拉强度较低。对比例2未采用分段冷却,材料屈服强度和屈强比均较高,延伸率较低。
表2本发明各实施例及对比例的热轧及冷却工序主要工艺参数
表3本发明各实施例及对比例的力学性能及韧性
对上述实施例所得钢板按照TB/T 2375进行了72h周期浸润腐蚀试验,以Q345B低合金钢和Q450NQR1普通耐候钢作为对比试样,试验结果如表4所示。实施例中的高耐蚀钢腐蚀失重速率相对于Q450NQR1普通耐候钢降低了近1倍,具有良好的耐大气腐蚀性能。
表4各实施例及对比试样耐大气腐蚀性能
平均腐蚀失重速率,(g/(m<sup>2</sup>·h)) | 相对腐蚀率,% | |
实施例1 | / | / |
实施例2 | 1.15 | 27 |
实施例3 | 1.17 | 27 |
实施例4 | 1.20 | 28 |
Q450NQR1 | 2.33 | 54 |
Q345B | 4.32 | 100 |
综上所述,按本发明钢种化学成分及控轧控冷工艺控制技术所得高耐蚀钢板屈服强度≥450MP,抗拉强度≥650MPa,延伸率≥22%以上,屈强比≤0.75,-40℃KV2≥110J,具有优异的耐大气腐蚀性能。可应用于集装箱、铁道车辆、油气管道等制造,提高服役寿命。
本发明所述实例仅仅是对本发明的优选实施方式进行描述,并非对本发明构思和范围进行限定,在不脱离本发明设计思想的前提下,本领域工程技术人员对本发明的技术方案作出的各种变形和改进,均应落入本发明的保护范围。
Claims (10)
1.一种抗拉强度650MPa级的热轧双相高耐蚀钢板,其特征在于:其化学成分质量百分比含量(wt%)为:C:0.010%~0.030%、Si:0.50%~0.70%、Mn:0.25%~0.55%、P:0.020%~0.030%、S:≤0.002%、Cr:3.00%~4.50%、Ni:≤0.10%、Cu:0.20%~0.35%、Als:0.020%~0.050%、Ti:0.015%~0.025%、Ca:0.0010%~0.0030%,其余为Fe和不可避免的杂质元素。
2.根据权利要求1所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板,其特征在于:该钢板的耐候指数I≥10.0。
3.根据权利要求1所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板,其特征在于:该钢板的屈服强度ReL≥450MPa,抗拉强度Rm≥650MPa,屈强比ReL/Rm≤0.75,延伸率A≥22%,经过180°冷弯(d=0a)和双倍冷弯无裂纹。
4.根据权利要求1所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板,其特征在于:该钢板金相组织为多边形铁素体+粒状贝氏体双相组织,其中铁素体平均晶粒尺寸10μm~12μm,铁素体体积分数65~70%。
5.如权利要求1-4任一项所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板的制造方法,其特征在于:制造工艺流程包括:铁水预处理深脱硫→转炉顶底复合吹炼→炉外精炼→连铸→加热→轧制→分段冷却→卷取→冷却至室温,分段冷却阶段中钢板出精轧机后首先以50~70℃/s速度冷却至720~770℃,然后空冷7~10s,空冷过后以30~50℃/s速度冷却至550~610℃进行卷取。
6.根据权利要求5所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板的制造方法,其特征在于:轧制前的加热阶段中,一加温度≤1070℃,二加+均热时间≤90min,在炉时间120~200min,出炉温度1170℃~1230℃。
7.根据权利要求5所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板的制造方法,其特征在于:加热阶段中加热炉采用还原气氛,空气过剩系数小于1.0。
8.根据权利要求5所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板的制造方法,其特征在于:钢水精炼采用LF+RH精炼处理,RH真空脱碳时间≥5min,出站温度≥1570℃;钢水浇铸中包温度控制在1530℃~1550℃,采用专用保护渣进行保护浇铸,液面波动≤±5mm,连铸坯拉速控制在1.0~1.5m/min,投用动态轻压下。
9.根据权利要求8所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板的制造方法,其特征在于:铸坯切割完成后直接装炉,不具备直装条件的铸坯进入保温坑缓冷,入加热炉温度≥500℃;不具备直装、热装条件的铸坯在保温坑内缓冷至室温。
10.根据权利要求5所述的一种抗拉强度650MPa级的热轧双相高耐蚀钢板的制造方法,其特征在于:轧制分粗轧和精轧两个阶段进行,粗轧阶段轧制温度控制在1050℃以上,累计压下率≥80%;精轧阶段开轧温度≤1030℃,累计变形量≥85%,精轧终轧温度为840~900℃。
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