CN107779763A - 一种抗hic压力容器用钢及其生产方法 - Google Patents
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
- C21D8/0226—Hot rolling
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- 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
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
一种抗HIC压力容器用钢,其特征在于化学成分按重量百分比为:C0.150~0.190,Si0.2~0.3,Mn1.10~1.20,P≤0.007,S≤0.002,Nb0.010~0.020,V0.030~0.050,Ti0.007~0.020,Alt0.025~0.045,Ca≤0.003,余量为铁和不可避免的杂质;Ca/S>1.2,Ceq0.35~0.40,[N]≤40ppm、[H]≤1.5ppm、[O]≤15ppm。本发明的一种抗HIC压力容器用钢,抗氢致裂纹和硫化物应力腐蚀SA‑516Gr.70N钢板,各项性能指标均达到理想要求,其力学性能为:屈服强度值≥260MPa,抗拉强度485~620MPa,延伸率≥17%,冲击功≥27J,硬度≤22,HIC性能检验合格,性能合格率100%。
Description
技术领域
本发明涉及一种钢铁产品,尤其涉及一种抗HIC压力容器用钢及其生产方法。
背景技术
随着国内容器用钢的发展,简单的容器用钢已经不能满足用户需求,特殊容器用钢成为开拓市场、赢得利润的利器。抗氢致裂纹和硫化物应力腐蚀SA-516Gr.70N钢板,具有抗HIC的特点,满足用户需求的重要产品。
SA-516Gr.70N钢板广泛应用于石油、化工、电站、锅炉等行业,用于制作反应器、换热器、分离器、球罐、煤气罐、液化气罐、核能反应堆压力壳、锅炉汽包、水电站高压水管、水轮蜗壳等设备及构件,满足高含量硫和氢的油气体需要,降低硫和氢的腐蚀、减少设备的检修、增加设备寿命。该钢板具有抗冲击性好、温度形变小、焊接性能好、抗疲劳性好、防层状撕裂性能好、抗硫氢能力强等特点。
原技术中,关于SA-516Gr.70N钢板的成分设计具有碳、硫、磷元素含量较高的特点,焊接性能较差;生产工艺中没有对钢板的二阶段累计压下率进行控制,钢板性能波动较大。
发明内容
本发明针对上述缺陷,所要解决的技术问题是提供一种抗HIC压力容器用钢及其生产方法。
为了实现上述目的,本发明的技术方案是这样实现的:
一种抗HIC压力容器用钢,其特征在于化学成分按重量百分比为:C0.150~0.190,Si0.2~0.3,Mn1.10~1.20,P≤0.007,S≤0.002,Nb0.010~0.020,V0.030~0.050,Ti0.007~0.020,Alt0.025~0.045,Ca≤0.003,余量为铁和不可避免的杂质;Ca/S>1.2,Ceq0.35~0.40,[N]≤40ppm、[H]≤1.5ppm、[O]≤15ppm。
下面主要各元素成分设计理由:
C:是钢中最基本的强化元素,通过形成间隙固溶体起固溶强化作用,能显著地提高钢的强度且成本低廉。但碳含量过高,对低温韧性和焊接性能不利,一般高性能容器用钢的C含量不超过0.30%。本发明中碳含量为0.15~0.19%。
Si:在炼钢时为脱氧元素,在钢中起固溶强化作用,能显著地提高钢的强度,但加入过多会损害钢的延伸率、韧性和焊接性能,本发明的硅含量为0.20~0.30%。
Mn:具有显著固溶强化作用,是管线钢中补偿因碳降低造成的强度损失最经济、最有效的元素。同时,锰是扩大γ相区的元素,降低γ→α转变温度,有利于获得细小的相变产物。但锰含量过多时也会在钢中产生较多的对抗HIC性能不利的MnS夹杂物,并容易因成份偏析导致硬质相带状组织出现,影响抗HIC性能。因此,本发明中的锰含量为1.10~1.20%。
P:作为钢中的有害元素,对钢的延伸率、低温冲击韧性和焊接性能均有损害。其含量应尽可能控制在较低水平。因此本发明中P的含量为≤0.007%。
S:作为钢中的有害元素,对钢的低温韧性有很大的损害。硫在钢中与锰形成硫化锰夹杂,不仅影响钢的韧性、延伸率、Z向性能、焊接性能,而且还会影响抗HIC性能,因此其含量应尽可能控制在较低水平。本发明中S的含量为≤0.002%。
Nb:是容器钢中最常用的元素之一,有显著的细化晶粒作用。热轧过程中通过固溶和应变诱导析出形式,抑制奥氏体的回复、再结晶,从而提高奥氏体的再结晶温度,使热轧在再结晶温度区间和未再结晶温度区间两个温度段进行轧制,并通过控轧后的加速冷却进一步细化钢的显微组织。本发明中Nb的含量为0.01~0.02%。
V:钒和碳、氨、氧有极强的亲和力,与之形成相应的稳定化合物。钒在钢中主要以碳化物的形式存在。其主要作用是细化钢的组织和晶粒,降低钢的强度和韧性。当在高温溶入固溶体时,增加淬透性;反之,如以碳化物形式存在时,降低淬透性。钒增加淬火钢的回火稳定性,并产生二次硬化效应。因此本发明中V的含量为0.03~0.05%。
Ti:与钢中的氮的亲和力较强,在钢中容易形成氮化钛,有固氮的作用;在板坯连铸过程中形成细小、稳定的TiN粒子,能有效地抑制再加热过程中奥氏体晶粒的长大;同时对改善焊接热影响区的韧性有明显的作用。因此本发明中Ti的含量为0.007~0.020%。
Al:铝主要用来脱氧和细化晶粒。在渗氮钢中促使形成坚硬耐蚀的渗氮层。铝能抑制低碳钢的时效,提高钢在低温下的韧性。含量高时能提高钢的抗氧化性及在氧化性酸和H2S气体中的耐蚀性,能改善钢的电、磁性能。铝在钢中固溶强化作用大,提高渗碳钢的耐磨性、疲劳强度及芯部力学性能。本发明中Al的含量为0.025~0.045%。
Ca:微量钙在钢种可以作为脱氧、去硫的净化剂,改善非金属夹杂物的形态,并且提高钢的强度和易切削性能。本发明中Ca的含量为小于等于0.003%
一种抗HIC压力容器用钢的生产方法,包括板坯加热—控轧控冷—热处理,所述的控轧工艺为出炉后应进行高压水除鳞,开轧温度不小于1000;℃厚度不大于12mm钢板,终轧温度≥800℃;厚度大于12mm小于等于20mm钢板,采用两阶段控制轧制,二阶段开轧温度920~950℃;二阶段终轧温度800~850℃;二阶段累计压下率≥50%;厚度大于20mm小于等于50mm钢板,采用两阶段控制轧制,二阶段开轧温度890~920℃;二阶段终轧温度800~850℃;二阶段累计压下率≥67%;所述的控冷工艺为钢板厚度14~50mm,开冷温度800~770℃,冷却方式为ACC,返红温度600~550℃,冷却速率4~10℃/s;对于厚度不小于35mm钢板,轧后还需采用堆垛缓冷,堆垛温度大于300℃,缓冷时间≥16小时。
所述的热处理工艺为正火温度880±10℃,升温速率1.0min/mm,净保温时间0.5min/mm钢板厚度,且不得少于10min。
由于本发明采用了低C、低Mn、低P、低S和适量的Nb、V、Ti等其它合金元素的合金设计,不仅有利于焊接性能、抗疲劳性能和抗HIC性能,还有利于控制合金成本和脱硫工艺成本。对于本发明中低C和低Mn的设计,在不增加其它合金元素含量的情况下,碳和锰含量降低引起的的固溶强化和细晶强化对强度贡献的降低,主要是通过以下措施进行了弥补:①增加精轧变形量:钢中Mn含量降低促进了Nb的析出,对热轧过程中再结晶的阻碍也增加,因此未再结晶温度Tnr升高,这样就可以相对增加精轧的轧制温度范围,有利于实施较大的精轧变形量。随着精轧变形量的增加,变形奥氏体内单位体积内的有效形核面积Sv增加,这可使相变时铁素体的形核率增加,从而进一步细化相变后的组织;②轧后加速冷却:锰含量的降低可以使Ar3温度有所增加,为避免较高的精轧终轧温度对相变后组织和性能的不利影响,轧后采取加速冷却的工艺,以提高奥氏体中温转变组织的比例和细化最终的组织。同时,碳含量的降低有利于提高钢的焊接性能。
本发明的一种抗HIC压力容器用钢,抗氢致裂纹和硫化物应力腐蚀SA-516Gr.70N钢板,各项性能指标均达到理想要求,其力学性能为:屈服强度值≥260MPa,抗拉强度485~620MPa,延伸率≥17%,冲击功≥27J,硬度≤22,HIC性能检验合格,性能合格率100%。
具体实施方式
下面结合具体实施例对本发明做进一步说明:
表1实施例化学成分质量百分比(%)含量
表2实施例的主要工艺参数
表3实施例的力学性能(取样方向为纵向)
抗HIC性能:按照NACE TM0284-2003标准,采用A溶液浸泡96小时,进行抗HIC性能检验,检验结果合格。
Claims (3)
1.一种抗HIC压力容器用钢,其特征在于化学成分按重量百分比为:C0.150~0.190,Si0.2~0.3,Mn1.10~1.20,P≤0.007,S≤0.002,Nb0.010~0.020,V0.030~0.050,Ti0.007~0.020,Alt0.025~0.045,Ca≤0.003,余量为铁和不可避免的杂质;Ca/S>1.2,Ceq0.35~0.40,[N]≤40ppm、[H]≤1.5ppm、[O]≤15ppm。
2.一种根据权利要求1所述的抗HIC压力容器用钢的生产方法,包括板坯加热—控轧控冷—热处理,其特征在于:所述的控轧工艺为出炉后应进行高压水除鳞,开轧温度不小于1000℃;厚度不大于12mm钢板,终轧温度≥800℃;厚度大于12mm小于等于20mm钢板,采用两阶段控制轧制,二阶段开轧温度920~950℃;二阶段终轧温度800~850℃;二阶段累计压下率≥50%;厚度大于20mm小于等于50mm钢板,采用两阶段控制轧制,二阶段开轧温度890~920℃;二阶段终轧温度800~850℃;二阶段累计压下率≥67%;所述的控冷工艺为钢板厚度14~50mm,开冷温度800~770℃,冷却方式为ACC,返红温度600~550℃,冷却速率4~10℃/s;对于厚度不小于35mm钢板,轧后还需采用堆垛缓冷,堆垛温度大于300℃,缓冷时间≥16小时。
3.根据权利要求2所述的抗HIC压力容器用钢的生产方法,其特征在于:所述的热处理工艺为正火温度880±10℃,升温速率1.0min/mm,净保温时间0.5min/mm钢板厚度,且不得少于10min。
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CN109930062A (zh) * | 2018-11-09 | 2019-06-25 | 鞍钢股份有限公司 | 一种改善特厚正火船板钢拉伸性能的方法 |
CN111004978A (zh) * | 2020-01-02 | 2020-04-14 | 鞍钢股份有限公司 | 一种低合金耐高温压力容器钢板及其生产方法 |
CN116590610A (zh) * | 2023-04-17 | 2023-08-15 | 包头钢铁(集团)有限责任公司 | 一种正火型屈服强度370MPa级压力容器钢板及其制备方法 |
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CN109930062A (zh) * | 2018-11-09 | 2019-06-25 | 鞍钢股份有限公司 | 一种改善特厚正火船板钢拉伸性能的方法 |
CN111004978A (zh) * | 2020-01-02 | 2020-04-14 | 鞍钢股份有限公司 | 一种低合金耐高温压力容器钢板及其生产方法 |
CN111004978B (zh) * | 2020-01-02 | 2021-04-27 | 鞍钢股份有限公司 | 一种低合金耐高温压力容器钢板及其生产方法 |
CN116590610A (zh) * | 2023-04-17 | 2023-08-15 | 包头钢铁(集团)有限责任公司 | 一种正火型屈服强度370MPa级压力容器钢板及其制备方法 |
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