WO2022001904A1 - 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法 - Google Patents

一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法 Download PDF

Info

Publication number
WO2022001904A1
WO2022001904A1 PCT/CN2021/102569 CN2021102569W WO2022001904A1 WO 2022001904 A1 WO2022001904 A1 WO 2022001904A1 CN 2021102569 W CN2021102569 W CN 2021102569W WO 2022001904 A1 WO2022001904 A1 WO 2022001904A1
Authority
WO
WIPO (PCT)
Prior art keywords
thickness
pipeline steel
rolling
grade high
coil
Prior art date
Application number
PCT/CN2021/102569
Other languages
English (en)
French (fr)
Inventor
邹航
李利巍
徐进桥
岳江波
徐锋
梅荣利
张鹏武
袁金
李鹏程
周正军
Original Assignee
武汉钢铁有限公司
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 武汉钢铁有限公司 filed Critical 武汉钢铁有限公司
Publication of WO2022001904A1 publication Critical patent/WO2022001904A1/zh

Links

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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D11/00—Process control or regulation for heat treatments
    • C21D11/005—Process control or regulation for heat treatments for cooling
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/008—Martensite

Definitions

  • the invention relates to the field of hot-rolled pipeline steel, in particular to an X90 grade high-strength pipeline steel plate coil with a thickness of ⁇ 20 mm and a manufacturing method thereof.
  • the technical problem to be solved by the present invention is to provide an X90 grade high-strength pipeline steel plate coil with a thickness of ⁇ 20 mm and a manufacturing method thereof, so as to overcome the above-mentioned deficiencies in the prior art.
  • the present invention provides an X90 grade high-strength pipeline steel plate coil with a thickness of ⁇ 20 mm, and the mass percentage of each component is:
  • C 0.035%-0.045%
  • Mn 1.75%-1.85%
  • Ni 0.20%-0.30%
  • Nb 0.060%-0.070%.
  • the microstructures in the pipeline steel coil are: acicular ferrite, polygonal ferrite, granular bainite and martensite islands, and their respective proportions are:
  • a manufacturing method of X90 grade high-strength pipeline steel plate coil with thickness ⁇ 20mm the technological process is: smelting, casting billet heating, controlled rolling and controlled cooling;
  • Slab heating The heating temperature is 1150°C ⁇ 1200°C, and the holding time is 60min ⁇ 120min. The refinement of austenite grains is avoided by low temperature heating. The bulk grains grow and coarsen;
  • Controlled rolling rough rolling is carried out, with a total of 6 passes, from 230mm thick billet to 60mm, the relative reduction ratio of the two passes at the end of rough rolling is ⁇ 23%, the end temperature is 960 °C ⁇ 1000 °C, rough rolling The last two passes make the austenite grains fully recrystallized by large deformation at lower temperature, and because the temperature is relatively low, the austenite grains remain refined before finishing rolling;
  • Finish rolling a total of 6 passes, the starting rolling temperature is less than 950 ° C, the final rolling temperature is 780 ° C ⁇ 840 ° C, the cumulative reduction rate of the two passes at the end of the finishing rolling is ⁇ 18%, and the finishing rolling adopts 7-stand continuous rolling.
  • the fourth stand is empty, and the final two passes of finishing rolling are fully accumulated through large deformation at a lower temperature, which is conducive to the formation of acicular ferrite in the subsequent cooling process;
  • Controlled cooling Coil after cooling to 300-380°C at 30-40°C/s.
  • a large amount of coarse polygonal ferrite or low-toughness lath bainite can be avoided.
  • the formation of acicular ferrite mainly includes a small amount of refined polygonal ferrite, a small amount of granular bainite, and a small amount of martensite islands with good strength and toughness.
  • the smelting specifically includes a converter, an argon station, a ladle furnace, a vacuum furnace, and calcium treatment.
  • the main alloying element content of the present invention is based on the following principles:
  • Carbon (C) The most economical strengthening element, through interstitial solid solution strengthening to improve the strength of the steel, increasing the carbon content can greatly improve the hardenability of the steel, and obtain a high-strength and low-temperature transformation structure, such as lath bainite, but For thick gauge and high toughness X90 grade pipeline steel, high C content will aggravate the uneven microstructure of the coil thickness direction and reduce the toughness of the steel; but too low will lead to insufficient strength.
  • the appropriate amount of carbon added is 0.030% to 0.050%
  • the preferred carbon content should be 0.035% to 0.045%;
  • Silicon (Si) mainly plays the role of solid solution strengthening, which is beneficial to assist desulfurization in the smelting process, and the suitable addition amount of silicon is 0.10% to 0.30%;
  • Manganese (Mn) An economical alloying element that significantly increases the yield and tensile strength of steel. However, the higher the manganese content is, the more difficult it is to control the composition segregation, which will lead to more serious tissue segregation and uneven performance. %;
  • Copper (Cu) It mainly plays the role of solid solution strengthening in steel and improves the corrosion resistance of steel, but its solid solution strengthening effect is weak, and the addition of chromium and molybdenum in steel also makes up for the corrosion resistance to a certain extent. Therefore, copper may not be added to reduce the cost of the alloy; in addition, the removal of copper is also beneficial to the improvement of the toughness of the steel to a certain extent;
  • Nickel (Ni) It is beneficial to reduce the ductile-brittle transition temperature, but the cost of the alloy is high when added in large quantities, and it will also reduce the impact energy of the steel. 0.30%;
  • Chromium, molybdenum (Cr, Mo) elements with strong hardenability, which significantly delay the ferrite transformation, which is beneficial to the bainite (acicular ferrite) transformation, but if the content is too high, the proportion of martensite in the steel will increase. It is not conducive to toughness; if the content is too low, the hardenability will be insufficient, and large-sized polygonal ferrite will be formed, resulting in insufficient strength.
  • the crystallization area increases the cumulative strain and promotes the acicular ferrite transformation during the controlled cooling process.
  • the suitable additions of niobium and titanium are 0.060%-0.080% and 0.010%-0.025%, respectively, and the preferred addition of niobium is 0.060% ⁇ 0.070%;
  • Vanadium (V) Micro-alloying element, difficult to precipitate under pipeline steel production process conditions, mainly plays the role of solid solution strengthening, especially can significantly improve tensile strength and reduce yield ratio, but when the content of vanadium is too high, it will reduce steel The impact toughness is high, and the suitable addition of vanadium is 0.020% to 0.040% respectively;
  • Aluminum is the main deoxidizing element in steel, which can significantly reduce the oxygen content in the steel. At the same time, the combination of aluminum and nitrogen forms AlN, which can effectively refine the grains. However, when the aluminum content in the steel exceeds 0.06%, the It is easy to cause the oxide inclusions of aluminum to increase significantly, reduce the cleanliness of the steel, and is unfavorable to the low-temperature toughness of the steel. The appropriate addition of aluminum is 0.015% to 0.060%;
  • Calcium treatment of steel during the secondary refining process can improve the shape of inclusions in the steel and improve the impact toughness of the steel.
  • the appropriate addition of calcium is 0.0008% to 0.0025%;
  • the ultra-low C content design is adopted, and the low temperature toughness of the thick coil is adopted; at the same time, the reasonable matching design of Mn, Cr, and Mo alloys is adopted to ensure good hardenability and avoid the occurrence of more lath bainite and horses.
  • Tensite structure two low-temperature and large-reduction methods at the end of rough rolling and finishing rolling ensure the effect of austenite grain refinement and promote acicular ferrite transformation during cooling; reasonable cooling rate and Coiling temperature matching design ensures that acicular ferrite is mainly obtained (80-90%), with a small amount of refined polygonal ferrite (3-8%) and a small amount of granular bainite (3-8%) ,
  • a small amount of martensitic islands ( ⁇ 4%) can meet the construction requirements of ⁇ 40 billion m 3 /a oil and gas pipelines, and at the same time meet the requirements of -20°C CVN ⁇ 305J, -15°C DWTT ⁇ 85%, uniform elongation Agt ⁇ 5%, and tissue uniformity in the thickness direction is guaranteed.
  • C 0.035% to 0.045%
  • Mn 1.75% to 1.85%
  • Ni 0.20% to 0.30%
  • Nb 0.060% to 0.070%.
  • microstructures in the obtained pipeline steel coil are: acicular ferrite, polygonal ferrite, granular bainite and martensite islands, and their respective proportions are:
  • a manufacturing method of X90 grade high-strength pipeline steel plate coil with thickness ⁇ 20mm the technological process is: converter, argon station, ladle furnace, vacuum furnace, calcium treatment, slab heating, controlled rolling and controlled cooling;
  • the heating temperature is 1150°C ⁇ 1200°C, and the holding time is 60min ⁇ 120min;
  • Controlled rolling rough rolling is carried out, with a total of 6 passes, from 230mm thick billet to 60mm, the relative reduction rate of the two passes at the end of rough rolling is ⁇ 23%, and the end temperature is 960 °C ⁇ 1000 °C;
  • the starting rolling temperature is less than 950 °C
  • the final rolling temperature is 780 °C ⁇ 840 °C
  • the cumulative reduction rate of the two passes at the end of the finishing rolling is ⁇ 18%
  • Controlled cooling Cool to 300°C to 380°C at 30 to 40°C/s and then coil.
  • the steel of the present invention has a thickness of more than 20 mm, and the impact energy reaches more than 305 J while ensuring that the strength meets the strength performance requirements of X90 grade pipeline steel.

Abstract

本发明公开了厚度≥20mm的X90级高强度管线钢板卷，包括C、Si、Mn、P、S、Cu、Ni、Cr、Mo、Nb、V、Ti、N、Al、Ca、B，余量为Fe及不可避免的夹杂；Pcm：0.163％～0.19％，Mn+Cr+3Mo：2.65％～2.85％。一种厚度≥20mm的X90级高强度管线钢板卷的制造方法，工艺流程为：冶炼、铸坯加热、控制轧制和控制冷却。能够满足≥400亿m3/a油气输送管道建设需求，同时满足-20℃CVN≥305J，-15℃DWTT≥85％，均匀延伸率Agt≥5％。

Description

一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法 技术领域
本发明涉及热轧管线钢领域，尤其涉及一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法。
背景技术
根据国家《中长期油气管网规划》，我国石油消费将持续稳步增长，天然气的需求潜力巨大。为保障快速增长的能源需求和国家能源安全，需要增强进口天然气输送能力，在管道输送能力方面，天然气管道输送能力同输送压力成正比，同管径的2.5次方成正比，高压、大口径输送是最基本的提升输送效率的方法。而管径越大、输送压力越高，管壁的承载就越高，相应地就需要更高钢级、更大壁厚以及良好低温韧性的管线钢。
专利申请号为201310169449.6的文献，公开了“一种X90管线用钢及其生产方法”，其成分设计为含B钢设计，而B的添加会会显著增加板条贝氏体比例，虽然能够大幅提升钢的强度，但钢的低温韧性也会较差，其公开的实施例中，低温韧性基本在300J以下。
专利申请号为201410266532.X的文献，公开了“均匀变形伸长率UEL≥5％的X90管线钢管及其制备方法”。该专利包含了X90宽厚钢板的生产方法，与本发明涉及的热连轧板卷不同，两者为不同技术路线；同时，该专利采用了相对较高的Cr+低Mo合金设计，不适于生产X90级热连轧板卷。
专利申请号为201410791739.9的文献，公开了“一种直缝焊管用X90级别多相组织管线钢”。与本发明不同，该专利包含的是X90宽厚钢板的生产方法，其C含量较高，不适于生产X90级高韧性板卷；且其使用厚度在16.3～19.6mm以下，无法满足超大输量管线钢建设需求。
专利申请号为201410791739.9和201811023904.0的文献，分别公开了“NbC纳米颗粒强化X90塑性管用钢板及其制造方法”和“VC纳米颗粒强化X90塑 性管用钢板及其制造方法”，均采用析出强化的方式制造X90级管线钢钢板，但通过添加较高的C(0.06％以上)来保证良好的析出强化效果会导致钢的韧性偏低，两项专利实施例中，钢的冲击功均在280J以下，不满足超大输量X90管线钢低温韧性需求。
发明内容
本发明所要解决的技术问题是提供一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法，以克服上述现有技术中的不足。
为了解决上述技术问题，本发明提供一种厚度≥20mm的X90级高强度管线钢板卷，各成分的质量百分比为：
C：0.030％～0.050％、Si：0.10％～0.30％、Mn：1.60％～1.90％、P≤0.012％、S≤0.0015％、Cu≤0.10％、Ni：0.15％～0.35％、Cr：0.15％～0.30％、Mo：0.20％～0.30％、Nb：0.060％～0.080％、V：0.020％～0.040％、Ti：0.010％～0.025％、N≤0.0050％、Al：0.015％～0.060％、Ca：0.0008％～0.0025％、B≤0.0004％，余量为Fe及不可避免的夹杂；Pcm：0.163％～0.19％，Mn+Cr+3Mo：2.65％～2.85％。
作为上述技术方案的改进，C：0.035％～0.045％、Mn：1.75％～1.85％、Ni：0.20％～0.30％、Nb：0.060％～0.070％。
作为上述技术方案的改进，管线钢板卷内的组织为：针状铁素体、多边形铁素体、粒状贝氏体和马氏体岛，其各自占比为：
针状铁素体：80％～90％、多边形铁素体：3％～8％、粒状贝氏体：3％～8％、马氏体岛≤4％。
一种厚度≥20mm的X90级高强度管线钢板卷的制造方法，工艺流程为：：冶炼、铸坯加热、控制轧制和控制冷却；
铸坯加热：加热温度为1150℃～1200℃，保温时间为60min～120min，通过低温加热避免奥氏体晶粒的细化，通过控制保温时间以保证板坯温度的均匀性，以及避免奥氏体晶粒长大粗化；
控制轧制：进行粗轧，轧制共计6道次，由230mm厚钢坯轧制到60mm，粗轧末两道次相对压下率均≥23％，结束温度为960℃～1000℃，粗轧末两道次 在较低温度通过大变形使得奥氏体晶粒充分再结晶，且由于温度相对较低，在入精轧前奥氏体晶粒保持细化；
进行精轧，轧制共计6道次，开轧温度小于950℃，终轧温度为780℃～840℃，精轧末两道次累积压下率≥18％，精轧采用7机架连轧，第4机架空过，精轧末两道次在较低温度通过大变形充分累积形变，在随后的冷却过程中利于针状铁素体的形成；
控制冷却：以30～40℃/s冷却至300℃～380℃后卷取，通过适宜的冷速和合理的卷取温度控制，避免了大量粗大多边形铁素体或低韧性的板条贝氏体的形成，获得以针状铁素体为主，含少量细化的多边形铁素体、少量粒状贝氏体、少量马氏体岛的具有良好强韧性的板卷。
作为上述技术方案的改进，冶炼具体依次包括转炉、氩站、钢包炉、真空炉、钙处理。
本发明的主要合金元素含量基于以下原理：
碳(C)：最经济的强化元素，通过间隙固溶强化提升钢的强度，增加碳含量，可大幅提升钢的淬透性，获得高强度低温相变组织，如板条贝氏体，但对于厚规格高韧性X90级管线钢，C含量偏高会加剧板卷厚度方向组织不均以及降钢的韧性；但过低则会导致强度不足，碳的适宜添加量为0.030％～0.050％，优选的碳含量应为0.035％～0.045％；
硅(Si)：主要起固溶强化作用，有益于辅助冶炼过程中脱硫，较适宜的硅的添加量为0.10％～0.30％；
锰(Mn)：较为经济的合金化元素，可显著提升钢的屈服和抗拉强度。但锰含量越高，其成分偏析控制难度越大，进而导致较严重的组织偏析和性能不均，较适宜的锰的添加量为1.60％～1.90％，优选的锰含量应为1.75％～1.85％；
磷、硫、氮(P、S、N)：磷、硫、氮在管线钢中均为有害元素，增加钢的各类脆性倾向，尤其氮含量过高易导致钢种TiN夹杂尺寸过大、含量过高，对韧性不利，因此应尽量降低钢中的磷、硫、氮的含量；
铜(Cu)：在钢中主要起固溶强化作用，以及提升钢的耐蚀性能，但其固溶 强化效果较弱，且钢中铬、钼的添加也一定程度上弥补了耐蚀性的不足，因而，可不添加铜以降低合金成本；此外，铜的去除也一定程度上有利于钢的韧性提升；
镍(Ni)：有利于降低韧脆转变温度，但大量添加时合金成本较高，同时也会降低钢的冲击功，适宜的添加量为0.15％～0.35％，优选镍含量应为0.20％～0.30％；
铬、钼(Cr、Mo)：强淬透性元素，显著推迟铁素体相变，利于贝氏体(针状铁素体)相变，但含量过高则钢种马氏体比例增加，不利于韧性；含量过低则淬透性不足，会形成大尺寸的多边形铁素体，导致强度不足，适宜的铬添加量为0.15％～0.35％、铬添加量为0.20％～0.30％；
铌、钛(Nb、Ti)：微合金化元素，可显著细化晶粒并起到析出强化作用，同时可显著提高钢的奥氏体再结晶温度，扩大未再结晶区范围，利于未再结晶区增加累积应变，促进控冷过程中的针状铁素体相变，较适宜的铌、钛的添加量分别为0.060％～0.080％，0.010％～0.025％，其中优选的铌的添加量为0.060％～0.070％；
钒(V)：微合金化元素，在管线钢生产工艺条件下难以析出，主要起固溶强化作用，尤其能显著提升抗拉强度，降低屈强比，但钒的含量过高时会降低钢的冲击韧性，较适宜的钒的添加量分别为0.020％～0.040％；
铝(Al)：铝是钢中主要的脱氧元素，能够显著降低钢中的氧含量，同时铝与氮的结合形成AlN，能够有效地细化晶粒，但是钢中铝含量超过0.06％时，易导致铝的氧化物夹杂明显增加，降低钢的洁净度，对钢的低温韧性不利，较适宜的铝的添加量分别为0.015％～0.060％；
钙(Ca)：在二次精炼过程中对钢进行钙处理，可以改善钢中的夹杂物形态，提高钢冲击韧性，但加入过量，易降低钢的洁净度，对钢的低温韧性不利，较适宜的钙的添加量分别为0.0008％～0.0025％；
硼(B)：同其他元素共同作用下，显著提升钢的淬透性，获得板条贝氏体组织；但在高钢级管线钢中板条贝氏体的比例提升会大幅降低钢的韧性，应严 格限制钢中硼的含量。
与现有技术相比，本发明的技术方案具有如下有益效果：
采用超低C含量设计，以厚规格板卷的低温韧性；同时采用合理的Mn、Cr、Mo合金匹配设计，保证良好淬透性的同时，以及避免出现较多的板条贝氏体及马氏体组织；粗轧及精轧末两道此低温大压下的方式，保证了奥氏体晶粒细化效果及促进了冷却过程中的针状铁素体相变；合理的冷速和卷取温度匹配设计，确保获得以针状铁素体为主(80～90％)，含少量细化的多边形铁素体(3～8％)、少量粒状贝氏体(3～8％)、少量马氏体岛(≤4％)的组织，能够满足≥400亿m 3/a油气输送管道建设需求，同时满足-20℃ CVN≥305J，-15℃ DWTT≥85％，均匀延伸率Agt≥5％，以及保证了厚度方向上的组织均匀性。
具体实施方式
下面详细说明本发明的具体实施方式，其作为本说明书的一部分，通过实施例来说明本发明的原理，本发明的其他方面、特征及其优点通过该详细说明将会变得一目了然。
一种厚度≥20mm的X90级高强度管线钢板卷，各成分的质量百分比为：
C：0.030％～0.050％、Si：0.10％～0.30％、Mn：1.60％～1.90％、P≤0.012％、S≤0.0015％、Cu≤0.10％、Ni：0.15％～0.35％、Cr：0.15％～0.30％、Mo：0.20％～0.30％、Nb：0.060％～0.080％、V：0.020％～0.040％、Ti：0.010％～0.025％、N≤0.0050％、Al：0.015％～0.060％、Ca：0.0008％～0.0025％、B≤0.0004％，余量为Fe及不可避免的夹杂；Pcm：0.163％～0.19％，Mn+Cr+3Mo：2.65％～2.85％。
更进一步，C：0.035％～0.045％、Mn：1.75％～1.85％、Ni：0.20％～0.30％、Nb：0.060％～0.070％。
所获得的管线钢板卷内的组织为：针状铁素体、多边形铁素体、粒状贝氏体和马氏体岛，其各自占比为：
针状铁素体：80％～90％、多边形铁素体：3％～8％、粒状贝氏体：3％～8％、马氏体岛≤4％。
一种厚度≥20mm的X90级高强度管线钢板卷的制造方法，工艺流程为： 转炉、氩站、钢包炉、真空炉、钙处理、铸坯加热、控制轧制和控制冷却；
铸坯加热：加热温度为1150℃～1200℃，保温时间为60min～120min；
控制轧制：进行粗轧，轧制共计6道次，由230mm厚钢坯轧制到60mm，粗轧末两道次相对压下率均≥23％，结束温度为960℃～1000℃；
进行精轧，轧制共计6道次，开轧温度小于950℃，终轧温度为780℃～840℃，精轧末两道次累积压下率≥18％；
控制冷却：以30～40℃/s冷却至300℃～380℃后卷取。
本发明实施例及对比例成分、工艺、性能分别如表1～表3所示：
表1本发明各实施例和对比例的成分取值列表(wt，％)
Figure PCTCN2021102569-appb-000001
Figure PCTCN2021102569-appb-000002
表2本发明各实施例及对比例的主要工艺参数列表
Figure PCTCN2021102569-appb-000003
Figure PCTCN2021102569-appb-000004
表3本发明各实施例和对比例主要性能
Figure PCTCN2021102569-appb-000005
从表1～3可已看出，本发明钢与对比例比较，实施例厚度达到20mm以上，在保证强度满足X90级管线钢强度性能要求的同时，冲击功达到305J以上。
以上所述是本发明的优选实施方式而已，当然不能以此来限定本发明之权利范围，应当指出，对于本技术领域的普通技术人员来说，在不脱离本发明原理的前提下，还可以做出若干改进和变动，这些改进和变动也视为本发明的保护范围。

Claims (5)

  1. 一种厚度≥20mm的X90级高强度管线钢板卷，其特征在于，各成分的质量百分比为：
    C：0.030％～0.050％、Si：0.10％～0.30％、Mn：1.60％～1.90％、P≤0.012％、S≤0.0015％、Cu≤0.10％、Ni：0.15％～0.35％、Cr：0.15％～0.30％、Mo：0.20％～0.30％、Nb：0.060％～0.080％、V：0.020％～0.040％、Ti：0.010％～0.025％、N≤0.0050％、Al：0.015％～0.060％、Ca：0.0008％～0.0025％、B≤0.0004％，余量为Fe及不可避免的夹杂；Pcm：0.163％～0.19％，Mn+Cr+3Mo：2.65％～2.85％。
  2. 如权利要求1所述的一种厚度≥20mm的X90级高强度管线钢板卷，其特征在于，C：0.035％～0.045％、Mn：1.75％～1.85％、Ni：0.20％～0.30％、Nb：0.060％～0.070％。
  3. 如权利要求1或2所述的一种厚度≥20mm的X90级高强度管线钢板卷，其特征在于，管线钢板卷内的组织为：针状铁素体、多边形铁素体、粒状贝氏体和马氏体岛，其各自占比为：
    针状铁素体：80％～90％、多边形铁素体：3％～8％、粒状贝氏体：3％～8％、马氏体岛≤4％。
  4. 一种厚度≥20mm的X90级高强度管线钢板卷的制造方法，其特征在于，工艺流程为：冶炼、铸坯加热、控制轧制和控制冷却；
    铸坯加热：加热温度为1150℃～1200℃，保温时间为60min～120min；
    控制轧制：进行粗轧，轧制共计6道次，由230mm厚钢坯轧制到60mm，粗轧末两道次相对压下率均≥23％，结束温度为960℃～1000℃；
    进行精轧，轧制共计6道次，开轧温度小于950℃，终轧温度为780℃～840℃，精轧末两道次累积压下率≥18％；
    控制冷却：以30～40℃/s冷却至300℃～380℃后卷取。
  5. 如权利要求4所述的一种厚度≥20mm的X90级高强度管线钢板卷的制 造方法，其特征在于，冶炼具体依次包括转炉、氩站、钢包炉、真空炉、钙处理。
PCT/CN2021/102569 2020-06-30 2021-06-26 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法 WO2022001904A1 (zh)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN202010617441.1 2020-06-30
CN202010617441.1A CN111607750A (zh) 2020-06-30 2020-06-30 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法

Publications (1)

Publication Number Publication Date
WO2022001904A1 true WO2022001904A1 (zh) 2022-01-06

Family

ID=72202375

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2021/102569 WO2022001904A1 (zh) 2020-06-30 2021-06-26 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法

Country Status (2)

Country Link
CN (1) CN111607750A (zh)
WO (1) WO2022001904A1 (zh)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115449698A (zh) * 2022-09-30 2022-12-09 马鞍山钢铁股份有限公司 一种屈服强度480MPa级耐微生物腐蚀管线钢及其制备方法
CN115652191A (zh) * 2022-09-26 2023-01-31 武汉钢铁有限公司 一种经济型含钛管线钢及生产方法

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111607750A (zh) * 2020-06-30 2020-09-01 武汉钢铁有限公司 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法
CN112575253A (zh) * 2020-11-24 2021-03-30 中国石油天然气集团有限公司 一种用于直缝埋弧焊的x80m钢材料、x80m钢管及其制备方法
CN113564464A (zh) * 2021-06-29 2021-10-29 武汉钢铁有限公司 一种25.4mm热连轧极限规格管线钢板卷及其制造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103243278A (zh) * 2013-05-10 2013-08-14 武汉钢铁(集团)公司 一种x90管线用钢及其生产方法
CN104357749A (zh) * 2014-11-14 2015-02-18 武汉钢铁(集团)公司 一种螺旋埋弧焊管用高强韧性x90热轧钢带及生产方法
CN105803327A (zh) * 2016-05-13 2016-07-27 江阴兴澄特种钢铁有限公司 一种经济型抗hic的x90管线钢板及其制造方法
CN110387551A (zh) * 2019-08-06 2019-10-29 北京首钢冷轧薄板有限公司 一种酸轧生产600MPa级TRIP钢的工艺
CN111607750A (zh) * 2020-06-30 2020-09-01 武汉钢铁有限公司 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101505279B1 (ko) * 2013-04-30 2015-03-24 현대제철 주식회사 열연강판 및 그 제조 방법
CN104532155B (zh) * 2014-12-19 2017-02-22 山东钢铁股份有限公司 一种直缝焊管用x90级别多相组织管线钢

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103243278A (zh) * 2013-05-10 2013-08-14 武汉钢铁(集团)公司 一种x90管线用钢及其生产方法
CN104357749A (zh) * 2014-11-14 2015-02-18 武汉钢铁(集团)公司 一种螺旋埋弧焊管用高强韧性x90热轧钢带及生产方法
CN105803327A (zh) * 2016-05-13 2016-07-27 江阴兴澄特种钢铁有限公司 一种经济型抗hic的x90管线钢板及其制造方法
CN110387551A (zh) * 2019-08-06 2019-10-29 北京首钢冷轧薄板有限公司 一种酸轧生产600MPa级TRIP钢的工艺
CN111607750A (zh) * 2020-06-30 2020-09-01 武汉钢铁有限公司 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115652191A (zh) * 2022-09-26 2023-01-31 武汉钢铁有限公司 一种经济型含钛管线钢及生产方法
CN115449698A (zh) * 2022-09-30 2022-12-09 马鞍山钢铁股份有限公司 一种屈服强度480MPa级耐微生物腐蚀管线钢及其制备方法
CN115449698B (zh) * 2022-09-30 2024-01-23 马鞍山钢铁股份有限公司 一种屈服强度480MPa级耐微生物腐蚀管线钢及其制备方法

Also Published As

Publication number Publication date
CN111607750A (zh) 2020-09-01

Similar Documents

Publication Publication Date Title
CN109055864B (zh) 高强韧性低屈强比热煨弯管用宽厚钢板及其生产方法
WO2022001904A1 (zh) 一种厚度≥20mm的X90级高强度管线钢板卷及其制造方法
CN109957713B (zh) 超宽厚壁x80级管线用热轧钢板及其生产方法
CN108467993A (zh) 一种低温管线用超宽高韧性热轧厚板及其生产方法
CN101649425B (zh) 低裂纹敏感性高韧性x120管线钢及其制造方法
CN109402500A (zh) 低温韧性良好的热煨弯管用x80宽厚钢板及其生产方法
CN109957712A (zh) 一种低硬度x70m管线钢热轧板卷及其制造方法
CN109023069B (zh) NbC纳米颗粒强化X80塑性管用钢板及其制造方法
CN103468905B (zh) 一种485MPa级管线钢热轧卷板及其制造方法
CN103469098B (zh) 一种具有良好抗hic性能的x80管线钢及其生产方法
CN107779740B (zh) 屈服强度700MPa级耐大气腐蚀热轧钢带及制造方法
CN109385576A (zh) 一种基于镁处理的低成本x65管线钢及其制造方法
CN103866204A (zh) 一种低温大压下工艺生产的大应变x80双相钢板
CN109023068B (zh) Vc纳米颗粒强化x90塑性管用钢板及其制造方法
WO2022022040A1 (zh) 一种355MPa级别海洋工程用耐低温热轧H型钢及其制备方法
CN109136756B (zh) NbC纳米颗粒强化X90塑性管用钢板及其制造方法
CN103160746A (zh) 一种高强度厚壁输水管用钢及其制造方法
CN102400062B (zh) 低屈强比超高强度x130管线钢
CN109957709B (zh) 一种含v大变形x70m管线钢板及其制造方法
CN109957710B (zh) 一种含v大变形x80m管线钢板及其制造方法
CN109536847A (zh) 屈服强度390MPa级焊管用热轧钢板及其制造方法
CN104878291B (zh) 一种屈服强度350 MPa无缝管线管及其制备方法
CN101165203B (zh) 超高强度高韧性x120管线钢及其制造方法
CN110468332A (zh) 一种薄规格直缝低屈强比高韧性管线卷板及其制造方法
CN104451446B (zh) 一种厚规格高强韧性贝氏体工程用钢及其生产方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 21833193

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 21833193

Country of ref document: EP

Kind code of ref document: A1