CN106282831A - 一种高强度集装箱用耐大气腐蚀钢及其制造方法 - Google Patents
一种高强度集装箱用耐大气腐蚀钢及其制造方法 Download PDFInfo
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- CN106282831A CN106282831A CN201510271882.XA CN201510271882A CN106282831A CN 106282831 A CN106282831 A CN 106282831A CN 201510271882 A CN201510271882 A CN 201510271882A CN 106282831 A CN106282831 A CN 106282831A
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- Prior art keywords
- steel
- resisting steel
- weather resisting
- strength
- strength container
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 129
- 239000010959 steel Substances 0.000 title claims abstract description 129
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 29
- 238000005096 rolling process Methods 0.000 claims abstract description 24
- 238000000034 method Methods 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 13
- 239000000126 substance Substances 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 7
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 6
- 229910000529 magnetic ferrite Inorganic materials 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 26
- 238000010438 heat treatment Methods 0.000 claims description 21
- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound 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[C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 13
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- 239000011575 calcium Substances 0.000 claims description 7
- 241001062472 Stokellia anisodon Species 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 238000010079 rubber tapping Methods 0.000 claims description 3
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Abstract
一种高强度集装箱用耐大气腐蚀钢及其制造方法，其化学成分重量百分比为：C：0.03-0.10％，Si：0.30-0.60％，Mn：0.40-0.80％，P≤0.015％，S≤0.006％，Al≤0.05％，Cu：0.20-0.4％，Cr：0.40-0.90％，Ti：0.06-0.12％，Ca：0.001-0.006％，N≤0.006％，其余为Fe和不可避免的杂质元素。本发明在较低的C－Mn钢成分的基础上，通过复合添加耐候性元素Cu、Cr和微合金强化元素Ti，采用控轧控冷工艺进行生产，使钢板具有细小的铁素体和少量贝氏体组织，屈服强度指标达到450-550MPa以上。
Description
技术领域
[0001] 本发明涉及高强度耐大气腐蚀钢及其生产方法，特别涉及一种高强度集装箱用耐 大气腐蚀钢及其制造方法。
背景技术
[0002] 集装箱用耐候钢属于耐大气腐蚀钢，如日本专利号JP04235250A、中国专利号 00121262. 1、中国专利号00133579. 0公开的耐大气腐蚀低合金结构钢。这类专利钢种都是 具有一定的耐大气腐蚀性能的低合金结构钢，成份体系为Cu - P - Cr 一 Ni或Cr 一 P - Ti 一 RE。
[0003] 为进一步延长材料的使用寿命，近年来开发了一些高耐蚀性的耐候钢，如日本专 利号JP10025550A、JP2002363704、中国专利号CN101376953A等。这类专利钢种一般含有 很高的Cr、Al或二者的复合添加，炼钢难度大、制造成本高。
[0004] 还有如中国专利号ZL200510036889. X公开的"一种应用薄板坯连铸连乳流 程生产Ti微合金化高强耐候钢板的工艺"，虽然也采用了较高的Ti提高强度，但含有 0. 075-0. 10%的P，在成分上仍属于传统的Cu-P-Cr-Ni耐候钢。
[0005] 此外，中国专利公开号CN101660099B公开的"高强度低合金热乳铁素体贝氏体耐 候钢及其生产方法"和中国专利公开号CN102168229B公开的"耐候钢板及其制造方法"。这 两个专利均采用较高的Mn，并通过Mo、Nb、V等强化元素的复合添加实现较高的强度，耐候 水平与传统的耐候钢相当。该专利涉及钢种的Mn含量较高，且含有Mo、Nb和V等元素。
[0006] 如中国专利号ZL200410061112. 4公开的"针状组织高强度耐候钢及其生产 方法"，中国专利号ZL200510111858. 6公开的"一种高强度低合金耐大气腐蚀钢及其 生产方法"。这两个发明专利均属低合金钢制造领域。前者成分设计上采用极低碳、 Cu-Cr-Ni-Mo-Nb的加入及Ti-Al-Zr-RE或Ca中的两种或两种以上复合添加，将碳含量控制 在接近或小于常温下碳在a -Fe中的最大溶解度0. 0218%，以减少或抑制渗碳体的析出， 保证主控组织为均匀的针状组织，以得到优良的耐候性能；后者通过Nb、Ti及Mo的复合添 加获得高的强度，并通过Cu、Cr及Ni的加入保证耐候性能。
[0007] 这两个专利采用的成份体系，前者采用了冶炼难度很大的极低碳含量设计，碳含 量为0. 01-0. 04%，大大增加了生产难度和制造成本，其可达到的屈服强度也低于550MPa ; 后者添加了较多的Mo和Ni，提高了生产成本。此外，这两个专利中均含有1. 0 %以上的Mn， Mn含量高对钢的焊接及低温韧性不利。
[0008] 美国专利 US6056833 公开的 "THERMOMECHANICALLY CONTROLLED PROCESSED HIGH STRENGTH WEATHERING STEEL WITH LOW YIELD/TENSILE RATIO ；H0T ROLLED, AIR COOLED ； PEARLITE-FREE"，其同样是一种采用控乳控冷方法生产的高强度耐候钢，屈服强度70 - 75ksi (约483 - 518MPa)，具有小于0. 85的低屈强比。该专利采用了 Cu-Cr-Ni耐候性成 份设计和Nb - Ti 一 Mo微合金设计，且，该发明专利特别添加了 V元素0. 06-0. 14%，这些 合金元素不但大大增加了制造成本，而且不利于钢板的焊接性能和低温冲击性能；从实际 性能对比来看，该钢种只保证达到483-518MPa。
发明内容
[0009] 本发明的目的在于设计一种高强度集装箱用耐大气腐蚀钢及其生产方法，屈服强 度为450-550MPa级别，甚至可达到600MPa以上，该钢除具备高强度、高耐大气腐蚀性能 (耐大气腐蚀性能指数I多6. 0)外，还具有良好的焊接、冷弯等加工性能，延伸率优良（冷 弯满足D = a，180° ;延伸率彡18% )，特别适用于集装箱生产过程中的各种冷成形加工。另 外，采用控乳控冷方式生产，不必进行热处理，生产周期短、生产方法简单，钢材成本较低。
[0010] 为达到上述目的，本发明的技术方案是：
[0011] 本发明在较低的C 一 Mn钢成分的基础上，通过复合添加耐候性元素Cu、Cr和微合 金强化元素Ti，采用控乳控冷工艺进行生产，使钢板具有细小的铁素体和少量贝氏体组织， 屈服强度指标达到450-550MPa，甚至可达到600MPa以上。
[0012] 具体的，本发明的一种高强度集装箱用耐大气腐蚀钢，其化学成分重量百分比 为：C :0• 03-0. 10 %，Si :0• 30-0. 60 %，Mn :0• 40-0. 80 %，P 彡 0• 015 %，S 彡 0• 006 %， A1 ^ 0. 05 %, Cu ：0. 20-0. 4 %, Cr ：0. 4〇-〇. 90 %, Ti ：0. 06-0. 12 %, Ca ：0. 001-0. 006 %, N < 0. 006%，其余为Fe和不可避免的杂质元素。
[0013] 在本发明钢的化学成分设计中：
[0014] C是钢中有效的强化元素，溶入基体具有固溶强化作用，同时在钢中以碳化物形式 存在，和合金元素结合发挥析出强化和细化晶粒的作用，因而添加量不得低于〇. 03% ;而过 多的C在钢中形成较多的碳化物起到原电池的作用，促进腐蚀的进行从而降低钢的耐腐蚀 性能，且不利于焊接，因而限定C含量不得高于0. 10%。
[0015] Si是为了对钢进行脱氧而添加的元素，同时也是耐蚀元素，并具有固溶强化作用， 所以控制含量下限为〇. 30%，Si含量多了会导致可焊性和焊接热影响区韧性恶化，因而其 上限规定为0.60%。
[0016] Mn成本低廉，是重要的强韧化元素，起固溶强化的作用，提高钢的强度和韧性，同 时Mn还是扩大奥氏体元素，能降低过冷奥氏体转变温度，促进钢中中低温强化组织的转 变，有利于钢强度的提高。但是Mn含量过多使淬透性增大，从而导致可焊性和焊接热影响 区韧性恶化，所以规定Mn含量范围限定为0. 40-0. 80%。
[0017] P属于耐蚀元素，但P对钢板的韧性影响极大，所以本发明钢种摒弃P作为提高耐 蚀性能的元素，采用低P成分设计；高的S含量不仅降低钢的低温韧性，而且促进钢板的各 向异性，对冷成形性能不利，且硫化物夹杂会使钢的耐候性能也明显降低。因而本发明钢种 设计采用极低的P、S含量，分别控制在0. 015 %和0. 006%以下。
[0018] A1是为了脱氧而加入钢中的元素，添加适量的A1有利于细化晶粒，改善钢材的强 韧性能，而较高的A1不利于连铸时的浇坯，所以控制上限为0. 05%。
[0019] Cr不仅是提高钢的淬透性的元素，而且能有效提高钢的耐大气腐蚀性能。特别是 本发明专利中未采用P提高耐候性能，所以必须保证一定的Cr加入量。但随着Cr含量的 增加，将严重恶化焊接性能及低温冲击韧性，所以Cr含量应限定为0. 40% -0. 90%。
[0020] Cu在钢中主要起固溶和沉淀强化作用，同时Cu的电化学电位高于Fe，能促进钢表 面致密性锈层的形成，也是耐蚀性元素，加入0.20%以上的Cu即可显著改善钢的耐大气腐 蚀性能，但是如果含量高时不仅会损害焊接热影响区韧性，而且热乳时易发生网裂，恶化钢 板的表面性能，所以Cu含量限定在0. 20% -0. 40%。
[0021] 通过Ca处理可以控制硫化物的形态以改善钢板的各向异性和塑性，提高低温 韧性，其含量少于0. 001时没有效果，而超过0. 006则会产生许多CaO、CaS，并形成粗 大的夹杂物，对钢的韧性造成损害，甚至影响钢的焊接性能。所以规定Ca含量范围为 0. 001% -0. 006%。
[0022] Ti是一种强烈的碳氮化物形成元素，在钢中主要以TiC或Ti(C，N)的形式存在。 TiN在高温下仍保持稳定，具有抑制加热奥氏体晶粒长大作用，同时在冷却过程中产生析出 强化。此外，Ti有阻止形变奥氏体再结晶和促进粒状贝氏体形成的作用，析出的Ti的碳氮 化物颗粒能阻止焊接热影响区的晶粒粗化，改善焊接性能。特别是Ti能够控制硫化物的形 状，使得含Ti钢具有非常好的冷成形能力，横向、纵向及厚度方向的性能均匀。研究表明， 钢中Ti含量超过0. 06时强化作用开始明显，显著提高钢的强度，Ti含量过高则易在晶界 上形成Ti的氮化物和硫化物而引起钢的脆化。所以限定Ti的含量为0. 06-0. 12%。
[0023] 本发明钢种为控制制造成本，对贵重合金元素如Ni、Nb和V等的含量加以控制。 其中Ni能提高淬透性，显著改善钢材的低温韧性并有效阻止Cu的热脆引起的网裂。而Nb、 V均能形成细微碳氮化物，有利于细化晶粒组织和发挥析出强化的作用，但这些元素的加入 将明显提高制造成本，且V的加入对焊接性能和低温韧性不利，因而对三种元素的上限加 以限定。
[0024] 本发明的主要创新点在于：通过固溶强化、细晶强化和析出强化相结合的设计思 想，在保证钢板耐候性的前提下，大幅提高钢的强度，可根据成分和工艺不同获得不同强度 级别的高强度耐候钢。
[0025] C是钢中的最有效强化元素，C固溶入基体中具有固溶强化作用；C还可与微合金 元素如Nb，Ti，V等结合，形成细小的纳米析出相，可起到析出强化的效果。本发明中C和 Ti的成分设计充分考虑TiC析出强化和C的固溶强化作用。C和Ti的含量范围是综合考 虑各种强化方式设计的。一般情况下，钢中的C含量小于0. 03%，在高温卷取工艺条件下， 钢的屈服强度达不到450-550MPa级别，同时可用于析出强化的TiC数量较少，对强度提高 有限；C的含量也不宜超过0. 10%，因为C含量过高，虽然强度可以提高，但由于与Ti形成 的碳氮化物尺寸较大，不仅起不到析出强化效果，而且降低钢的耐腐蚀性能。通常情况下， 钢中起析出强化效果的TiC粒子平均尺寸~10nm，其体积分数根据C和Ti含量的不同通常 在0. 01-0. 5%。根据公式A 0 a2p= 5. 9f 1/2/d •ln(d/b)，其中d是析出相平均尺寸，f是析 出相体积分数，b是柏氏矢量。据此，可计算出析出相尺寸~10nm、体积分数在0. 01-0. 5% 时，析出强化对强度的贡献在22-154MPa，取中值为88MPa，由此可推算出C的目标含量应 在0. 07%附近；同理，根据已知的析出强度贡献和析出相尺寸可反算出Ti的目标含量应在 0. 08%左右。
[0026] 除了析出强化外，本发明还考虑了细晶强化的影响。钢板晶粒大小除了与成分设 计有关之外，还与乳制工艺密切相关。细晶强化对强度的贡献根据公式A 〇 a2g= 19. 7d 1/2， 其中d是铁素体晶粒尺寸。实际乳制过程中钢的铁素体晶粒尺寸一般在5-lOum，由此可 得晶粒细化对强度的贡献在197-279MPa之间。这样，析出强化和固溶强化贡献之和约 为285-367MPa。要获得屈服强度达450-550MPa的高强耐候钢，固溶强化的效果至少达到 83-165MPa。根据固溶强化机理，置换元素如Mn，Cr等对强度的贡献较小，加之其含量较 低，因此对强度的贡献可忽略，而固溶强化的效果主要取决于间隙原子C和N的含量，由于 N基本被Ti全部固定，而C有一部分与Ti结合其析出强化作用，另一部分则起固溶强化作 用。根据公式A oa2s= 5000C，取固溶强化贡献的中值124MPa，可知固溶的碳含量至少达 到0. 025 %，加上与Ti结合的一部分C，故钢中的碳含量至少达到0. 03%，其含量应控制在 0. 03-0. 10% ；
[0027] Ti和C的含量应控制在合理范围内，同时采用合适的加热、乳制、冷却以及卷 取工艺制度才能获得所需要的力学性能和耐候性。其中，Ti和C应同时满足下两式： (1)1.0 彡 Ti/C 彡 4.0 ;(2)-2. 75 彡 log10[Ti% ] [C% ]彡-1.92 ;控制 Ti/C 的目的主要是 为了获得细小的纳米级TiC ;控制Ti和C乘积的对数范围主要是为了获得足够数量的细小 纳米TiC，若Ti和C的含量过高，则形成的TiC较为粗大，对强度的提高贡献不大。
[0028] 本发明所涉及的高强度耐候钢除了成分体系上的创新之外，还必须与创新性的工 艺相结合才能获得所述的高强度耐候钢。
[0029] 首先，高Ti钢的成分体系设计必须要求高的加热温度（如要求加热温度 多1260°C )以保证尽可能多的Ti固溶在基体中，这就要求控制钢中Ti和C的含量使TiC 的固溶温度控制在相对较低的温度范围；
[0030] 其次，终乳结束后以较高的冷速（彡30°C /s)冷却至合适的卷取温度。乳后高冷 速的目的：一是细化晶粒，提高强度；二是抑制在水冷过程中TiC的提前析出，使固溶在基 体中的Ti和C尽量在卷取过程中形成，这样形成的TiC尺寸细小，可达10nm以下，具有很 强的析出强化效果；同时，卷取温度也应控制在合理的温度范围。由于TiC的析出动力学规 律决定了其存在最佳的析出温度范围，在此范围内，TiC析出数量最多，平均寸最小，其析出 强化效果最佳，从而利用细晶强化和析出强化保证钢卷具有高强度和高韧性。
[0031] 本发明所述的高强度集装箱用耐大气腐蚀钢的制造方法，其包括如下步骤：
[0032] 4)冶炼、铸造
[0033] 按上述成分冶炼，采用铁水预脱硫，转炉顶底复合吹炼，RH真空循环脱气工艺，同 时进行钙处理；
[0034] 5)铸坯加热
[0035] 控制铸坯加热温度1260°C以上，并控制出炉温度在1230°C以上，控制加热炉的气 氛为还原性气氛，并保温3h以上；
[0036] 6)乳制
[0037] 采用两阶段控制乳制，控制粗乳结束温度在1020°C以上，在950°C以上开始精乳， 累计压下率彡80%，精乳终乳温度830~880°C，然后彡30°C /s的冷却速率冷却到580~ 660°C卷取，然后再空冷到室温。
[0038] 本发明钢中未添加Ni元素，采用加热工艺抑制钢坯加热过程中产生的Cu脆。控制 铸坯加热温度1260°C以上，并控制出炉温度在1230°C以上，控制加热炉的气氛为还原性气 氛并保温3h以上。加热过程一方面保证钢坯充分奥氏体化，并保证钢坯成分充分均匀化； 对于本发明钢来说，保证加热时间多3小时还有另外一个重要的作用：将钢坯中的Ti析出 粒子固溶进入到奥氏体组织中。Ti的固溶过程需要较高的温度、以及较长的时间，且这些参 数与钢中的碳含量和Nb含量有关。这也是本发明对加热过程进行控制的关键原因。
[0039] 乳制采用两阶段控制乳制，控制粗乳结束温度在1020°C以上，在950°C以上开始 精乳，累计压下率多80%，精乳终乳温度830-880°C，并且随着成品板厚的增加终乳温度应 相应降低，然后多40°C /s的冷却速率冷却到580-660°C卷取，同样也根据板厚的增加适当 降低卷取温度，然后再空冷到室温。
[0040] 本发明钢种不需要乳后热处理，缩短生产周期、降低生产成本。
[0041] 本发明具有如下优点：
[0042] 1、本发明钢具有优良的综合力学性能，屈服强度在450_550MPa以上，比普通耐候 钢强度大大提高，增加承重能力，适合集装箱的减薄设计；而且本发明钢种具有优良的塑 性，冷成形性好，特别适合集装箱板的冷弯加工。
[0043] 2、本发明钢不采用高的P含量，具有良好的焊接性能，同时通过控制Cu、Cr等抗 大气腐蚀性元素的含量，确保其耐大气腐蚀性能不低于普通耐候钢，耐候性为普通钢材的 2~8倍，钢材使用时间越长，越能发挥这一优势。
[0044] 3、本发明钢的碳当量小于等于0. 38%，通常碳当量在0. 41%以下即属于易焊接 钢种。所以本发明钢种具有良好的焊接性能，可以实现不预热焊接，也避免了焊后热处理。 通过合理的成份设计和焊接材料推荐，可以有效提高焊接效率，获得良好的焊接接头性能。 碳当量公式为：
[0045]
[0046] 4、本友明钢柙米用控乳控冷生严，乳态父货，生产工艺简单，生产周期短，同时发 明钢中不添加诸如Ni、Nb及V等贵重合金元素，钢材成本较低，在各种冶金企业均可实施。
具体实施方式
[0047] 下面结合实施例对本发明做进一步说明。
[0048] 实施例1
[0049] 按照本发明钢化学成份要求，采用转炉冶炼，然后进行炉后精炼，获得化学成份见 表1，连铸切坯送热乳生产线，钢坯加热温度为1260°C，采用两阶段控乳和乳后水冷并卷 取，终乳温度为830 °C~880 °C，卷取温度为580 °C~660 °C。
[0050] 本发明钢实施例的力学性能见表1所示。与相近钢种进行了化学成分、力学性 能等的对比，其中对比专利1为中国专利号ZL200410061112. 4,对比专利2为中国专利号 ZL200510111858. 6。对比专利 3 为美国专利 US6056833。
[0051] 表1本发明钢与对比钢种的化学成份、力学性能对比
[0052]
[0054] 注：Pcn= C+V/10+Mo/15+(Mn+Cu+Cr)/20+Si/30+Ni/60+5 • B
[0055] 本发明钢种与对比专利1的化学成份有明显不同，本发明钢种C含量为0.03~ 0. 10%，而对比专利1钢的C含量为0.01~0.04%;本发明钢不添加Nb、V和Ni，而对比钢 中除了这些合金元素外，Mn含量也明显高于本发明（0.4-0. 8% )，且添加了贵重合金元素 Mo,同时Ti的含量与本发明钢种也明显不同。而对比专利2要求V含量为0.01~0. 15%， 对比专利3要求V含量为0. 06~0. 14%。
[0056] 本发明钢的力学性能要求与对比钢不同，本发明钢种屈服强度可满足450_550MPa 以上，而三个对比专利钢种中除了对比专利2外其他的屈服强度要求均低于550MPa。
[0057] 实施例2
[0058] 按照本发明成分要求，在试验室500kg真空感应炉上冶炼本发明钢。化学成分见 表2,制造工艺参见表3。
[0059] 钢坯加热温度为1260°C，终乳温度830~880°C，乳后加速冷却至580°C~660°C 卷取，随后空冷至室温。
[0060] 本发明钢力学性能见表4。
[0061] 表2本发明钢实施例一化学成分（wt% )
[0062]
[0063] 表 3
[0064]
[0065] 表 4
[0066]
[0067] 从与现有专利的对比可发现，本发明钢种采用更为经济的成分设计和连铸连乳生 产制造工艺，乳态交货无需热处理，钢卷具有良好的焊接性能、耐候性，同时屈服强度满足 450-550MPa以上的高强度要求，特别是采用高Ti设计改善了冷成形性能，这是目前已发现 的所有耐候钢发明专利所不具备的。
[0068] 按本发明钢种成分设计范围及乳制工艺控制技术所得实施例钢的屈服强度达 450-550MPa级别，甚至可达到600MPa以上，延伸率在18%以上。该钢除具备高强度、高耐 大气腐蚀性能外，还具有良好的焊接、冷弯等加工性能，延伸率优良，特别适用于集装箱生 产过程中的各种冷成形加工。
Claims (8)
1. 一种高强度集装箱用耐大气腐蚀钢，其化学成分重量百分比为：c :0. 03-0. 10%， Si ：0. 30-0. 60 %, Μη ：0. 4〇-〇. 80 %, Ρ ^ 0. 015 %, S ^ 0. 006 %, Α1 ^ 0. 05 %, Cu ： 0· 20-0. 4%，Cr :0· 40-0. 90%，Ti :0· 06-0. 12%，Ca :0· 001-0. 006%，Ν 彡 0· 006%，其余为 Fe和不可避免的杂质元素；其中， 其中，11和（：应同时满足下两式：（1)1.0彡11/(：彡4.0 42)-2.75彡1(^1。[11%] [C% ] ^ -1. 92〇
2. 如权利要求1所述的高强度集装箱用耐大气腐蚀钢，其特征是，所述耐大气腐蚀钢 的碳当量彡〇. 38%。
3. 如权利要求1所述的高强度集装箱用耐大气腐蚀钢，其特征是，所述耐大气腐蚀钢 的显微组织为细小的铁素体和少量贝氏体组织。
4. 如权利要求1所述的高强度集装箱用耐大气腐蚀钢，其特征是，所述耐大气腐蚀钢 的屈服强度在450-550MPa。
5. 如权利要求1~4中任何一项所述的高强度集装箱用耐大气腐蚀钢的制造方法，其 特征是：包括如下步骤： 1) 冶炼、铸造 按上述成分冶炼，采用铁水预脱硫，转炉顶底复合吹炼，RH真空循环脱气工艺，同时进 行钙处理； 2) 铸还加热 控制铸坯加热温度1260°C以上，并控制出炉温度在1230°C以上，控制加热炉的气氛为 还原性气氛，并保温3h以上； 3) 乳制 采用两阶段控制乳制，控制粗乳结束温度在1020°C以上，在950°C以上开始精乳，累计 压下率彡80%，精乳终乳温度830~880°C，然后彡30°C /s的冷却速率冷却到580~660°C 卷取，然后再空冷到室温。
6. 如权利要求5所述的高强度集装箱用耐大气腐蚀钢的制造方法，其特征是，所述耐 大气腐蚀钢的碳当量< 〇. 38%。
7. 如权利要求5所述的高强度集装箱用耐大气腐蚀钢的制造方法，其特征是，所述耐 大气腐蚀钢的显微组织为细小的铁素体和少量贝氏体组织。
8. 如权利要求5所述的高强度集装箱用耐大气腐蚀钢的制造方法，其特征是，所述耐 大气腐蚀钢的屈服强度在450-550MPa。
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