WO2021036272A1 - 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法 - Google Patents

高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法 Download PDF

Info

Publication number
WO2021036272A1
WO2021036272A1 PCT/CN2020/084014 CN2020084014W WO2021036272A1 WO 2021036272 A1 WO2021036272 A1 WO 2021036272A1 CN 2020084014 W CN2020084014 W CN 2020084014W WO 2021036272 A1 WO2021036272 A1 WO 2021036272A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel plate
temperature
strength
rolling
steel
Prior art date
Application number
PCT/CN2020/084014
Other languages
English (en)
French (fr)
Inventor
刘朝霞
李国忠
许晓红
白云
苗丕峰
刘俊
周永浩
韩步强
武金明
Original Assignee
江阴兴澄特种钢铁有限公司
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 江阴兴澄特种钢铁有限公司 filed Critical 江阴兴澄特种钢铁有限公司
Priority to EP20856109.2A priority Critical patent/EP4015668A4/en
Priority to US17/927,881 priority patent/US20230323494A1/en
Priority to KR1020227006048A priority patent/KR20220035962A/ko
Publication of WO2021036272A1 publication Critical patent/WO2021036272A1/zh

Links

Images

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
    • C22C38/02—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
    • C22C38/18—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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/12—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention belongs to the field of iron and steel (iron-based alloy) metallurgy, and specifically relates to a 9Ni steel plate for LNG ships with high strength and low yield ratio and a manufacturing method thereof.
  • LNG is the abbreviation of liquefied natural gas, which is a clean and efficient energy source. It can be liquefied at a low temperature of -162°C, and the volume after liquefaction is reduced to 1/600 of the original volume, which greatly saves storage and transportation space. LNG also has the characteristics of large heating value and high performance. In many countries, LNG is listed as the fuel of choice. China uses LNG to optimize the domestic energy allocation structure, ensure the safety of energy supply, protect the ecological environment, and achieve sustainable economic and social development. The transportation of LNG mainly relies on large ships, and storage tanks are built on the ships. The materials of the storage tanks must have sufficient strength and toughness, and low yield ratio.
  • 9Ni steel Compared with stainless steel, 9Ni steel has the advantages of relatively small alloy content and low price. Compared with aluminum alloy for low temperature, it has the advantages of higher allowable stress and lower thermal expansion rate, so it is selected as the main material of LNG tank. As 9Ni steel has high Ni content, high surface quality requirements, and strict requirements on impurity elements, it brings a series of problems to smelting, rolling, and heat treatment. At present, there are not many companies that can successfully mass produce, plus users’ recognition of the domestic market. With a low impact, there are only a handful of domestic manufacturers that can actually supply the market.
  • high-strength, high-yield ratio is also an important factor restricting the production of 9Ni steel when used in a cryogenic environment of -196°C.
  • the yield-strength ratio is particularly restrictive to the project.
  • the important clause for the use of pipeline steel in the project is that the yield-strength ratio shall not be higher than 0.92.
  • the yield ratio shall not be higher than 0.85.
  • LR classification society rules also mandate that all ship steels, including 9Ni steel, have a yield ratio not higher than 0.94.
  • Chinese patent CN103602888 discloses a hot-rolled low-compression ratio 9Ni thick steel plate and a manufacturing method thereof. The method is to obtain 9Ni steel through a hot-rolled state without a heat treatment method, and the structure is tempered martensite as the matrix. +4-15% reverse-transformed tempered austenite, nevertheless, only Example 1 reached the lower limit of the European standard yield strength, and the yield ratio was greater than 0.93.
  • Chinese patent CN 10125668 discloses a 9Ni steel manufacturing method. Its preparation process is mainly to simulate continuous casting and rolling process, thereby shortening the production process flow. This is difficult to achieve in industrial production, and the product strength is low. To the actual supply requirements.
  • Chinese patent CN101864537 discloses a method for manufacturing Cu-containing 9Ni steel with a thickness of 20mm. After hot rolling, laminar cooling to below 200°C will have a large residual stress during this process, which is not suitable for shape control of thin and wide steel plates.
  • the yield strength of the steel plate is as high as 710MPa, but at the expense of the high toughness of 9Ni steel, the actual steel plate -196°C impact value is only 120J, and there is not much surplus for mass supply.
  • the 9Ni steel especially the thin 9Ni steel plate, is designed with low C, 9% Ni, increased Nb and Cr composition, high temperature hot rolling, and then a special QLT heat treatment process to obtain good results.
  • the present invention designs 9Ni steel, especially thin gauge 9Ni steel sheets, with low C, 9% Ni, and increased Nb and Cr components. , High temperature hot rolling, followed by a special QLT heat treatment process, to obtain 9Ni steel with good strength and toughness (strength and toughness) and low yield ratio, and easy to control the surface quality and shape of wide and thin 9Ni steel plates.
  • the present invention designs the chemical composition of the steel sheet: C: 0.02 ⁇ 0.05%, Si: 0.10 ⁇ 0.30%, Mn: 0.50 ⁇ 0.80%, Ni: 8.90 ⁇ 9.50%, P: ⁇ 0.0070%, S: ⁇ 0.0020%, Cr: 0.10 ⁇ 0.25%, Alt: 0.010 ⁇ 0.035%, Nb: 0.010 ⁇ 0.020%, Ca: 0.0005 ⁇ 0.0030%, O: ⁇ 0.0012%, N: ⁇ 0.004%, H : ⁇ 0.00015%, the balance is Fe and unavoidable impurity elements.
  • the addition of C can increase the hardenability of steel, especially for the production of medium and thick plates, which can significantly improve the strength, but too much C content is not conducive to the -196°C ultra-low temperature impact performance, ultra-low temperature strain aging performance, welding performance and corrosion resistance of steel Therefore, the carbon content in the present invention is controlled between 0.02 and 0.05%.
  • Si is mainly used for deoxidation. Although the amount of Si must be determined according to different smelting methods, it must be above 0.10% in order to obtain good steel sheet performance. In the oxide scale, if it exceeds 0.30%, it is easy to form silico-alumina spinel. It is not easy to remove. Considering that the surface quality of 9Ni steel is particularly important, the present invention implements low Si content control, and the upper limit is set at 0.30%.
  • Mn is an element that improves the hardenability of steel, and has a solid solution strengthening effect to make up for the strength loss caused by the decrease in the C content in the steel.
  • the Mn content in the steel is too low, the effect of ensuring strength cannot be fully exerted, but when the Mn content is too high, its carbon equivalent will be increased and the welding performance will be damaged.
  • Mn tends to segregate in the center of the steel sheet, reducing the impact toughness of the center of the steel sheet. Therefore, the Mn content of the present invention is controlled to 0.50 to 0.80%.
  • Ni is an element that improves the hardenability of the steel plate and can significantly improve its low-temperature toughness, and has a good effect on the impact toughness and ductile-brittle transition temperature.
  • the Ni content is too high, the surface of the slab is prone to produce high-viscosity iron oxide scale, which is difficult to remove, which affects the surface quality of the steel plate.
  • Ni is also a precious metal, too high content will increase costs. Therefore, the present invention controls its content at 8.90-9.50% on the premise of meeting the requirements of classification societies, European standards and American standards, which is conducive to achieving the best cost performance.
  • Cr is an element that improves the hardenability of steel, can inhibit the formation of polygonal ferrite and pearlite, promote the transformation of low-temperature structure martensite during the quenching process, and improve the tensile strength of steel. But too high Cr content will affect the toughness of steel and cause temper brittleness.
  • the chromium content is controlled at 0.10 to 0.25%.
  • Ca treatment is a necessary treatment link for the steel grade of the present invention.
  • the 0.0005 ⁇ 0.0030% Ca can not only reduce the performance hazards caused by sulfides, but also can be sharp Al 2 O 3 inclusions that change into spherical low melting point inclusions, thereby reducing the steel plate During the rolling process, the micro-cracks at the sharp corners of the hard inclusions are generated, which improves the impact toughness of the steel plate.
  • Al mainly plays the role of nitrogen fixation and deoxidation.
  • AlN formed by joining Al and N can effectively refine grains, but too high a content will impair the toughness of steel. Therefore, the present invention controls the content (Alt) to be 0.010 to 0.035%.
  • O, N harmful gas elements, high content, many inclusions, reduce steel plate plasticity, toughness and welding bending performance.
  • the present invention strictly controls the content of O to not more than 0.0012%; the content of N to not more than 0.004%.
  • H Harmful gas element.
  • the high content of H is easy to produce white spots, reduce the plastic toughness of the steel plate, and seriously harm the performance of the steel plate.
  • H-induced delayed cracking is one of the main reasons for the failure of high-strength steel cutting, cold bending and other applications.
  • the present invention In order to improve the comprehensive performance of the steel plate, the present invention strictly controls the H content within 0.00015%.
  • the present invention also provides a method for preparing the above-mentioned 9Ni steel plate for LNG ship with high strength and low yield ratio with good low temperature toughness.
  • the specific process is as follows:
  • Smelting and continuous casting process smelting raw materials are smelted in a converter, RH refining, LF refining, RH refining, in order to control the internal looseness and segregation of the steel plate, low superheat pouring, full argon protection pouring, and dynamic light reduction control.
  • the casting superheat is controlled at 5 ⁇ 25°C; the soft reduction interval is controlled at 0.40 ⁇ fs ⁇ 0.90, where fs is the fraction of solid phase in the slab to ensure that the center segregation of the slab is not higher than the C1.0 level.
  • Slow cooling and cleaning and grinding process of the slab After the casting slab is off the production line, it must be slowly cooled. The cast billets are required to be stacked into pits or covered. The starting temperature of slow cooling should not be less than 600°C, and the time should not be less than 48 hours. The surface of the cast slab is polished and cleaned by the machine, and the upper and lower surfaces of the cast slab are ground to a thickness of 1.5mm.
  • Heating process The casting slab is sent to a walking-type heating furnace with an average heating rate of 10-14cm/min. In order to ensure high-temperature rolling, it is heated to 1180-1250°C. When the temperature of the core reaches the surface temperature, heat preservation will start. Not less than 1 hour. The alloying elements in the steel are fully dissolved to ensure the uniformity of the composition and performance of the final product. And control the heating time in the temperature range of 600 ⁇ 900°C ⁇ 0.32min/mm.
  • Rolling process After the billet is released from the furnace, it is subjected to two-stage controlled rolling of rough rolling + finishing rolling after descaling with high pressure water.
  • the opening temperature of rough rolling is between 1080-1150°C, and the three-pass single-pass reduction rate after rough rolling ⁇ 15%.
  • the thickness to be heated is ⁇ 1.8H, where H is the thickness of the finished product.
  • the finishing rolling adopts high temperature rolling, and the start rolling temperature is between 900 and 980°C.
  • Quenching heat treatment process After rolling, the steel plate is subjected to offline quenching treatment. After testing the steel of the present invention, the ferritic austenite equilibrium transformation start temperature AC 1 is 608°C, the ferritic austenite equilibrium transformation end temperature AC 3 is 725°C, and the first quenching (one-quenching) temperature is 840°C. ⁇ 10°C, the holding time after furnace temperature reaches 30 ⁇ 60min. The secondary quenching (secondary quenching) temperature is 625 ⁇ 10°C, and the holding time after the furnace temperature reaches the temperature is 30-60min. In order to ensure the uniformity of the steel plate, the temperature control accuracy is ⁇ 10°C.
  • Tempering heat treatment process After the steel plate is quenched, it is tempered at 560 ⁇ 10°C. After reaching the temperature at 1/2 of the thickness of the steel plate, the tempering holding time is 120-180min, and enough time is given to fully diffuse the carbon in the quenched martensite to obtain ferrite. In the subsequent long-term holding process, iron The growth of the element body layer ensures the best match of the strength and toughness of the steel plate, reduces the yield ratio of the steel plate, and improves the engineering application of the steel plate.
  • the invention adopts low C, high Ni, and added Cr to ensure the hardenability of the steel plate, improve the tensile strength of the steel plate, reduce the yield ratio, increase the Nb content, ensure the high temperature rolling of the steel plate, and obtain relatively uniform and large grain initial deformation. Tensile grains. Using the heritability of the steel plate structure, a larger size parent phase austenite can be obtained during the quenching and holding process.
  • the invention adopts a series of measures such as cleaning the upper and lower surfaces of the casting slab with a thickness of 1.5 mm, controlled heating during heating, high-pressure water descaling, and high-temperature rolling to ensure that the steel plate has a good surface quality.
  • the invention guarantees the good shape of the 9Ni steel plate by adding Nb, section heating control, high temperature rolling, and no watering after rolling, and also prevents the steel plate from being scratched due to straightening and affecting the surface quality of the steel plate.
  • the invention guarantees the low C content control stability of the steel plate through double RH treatment.
  • the first quenching temperature is increased through heat treatment to ensure the large size of the initial austenite crystal grains, and the second quenching forms a structure in which large size and small size austenite crystal grains coexist, ensuring the low yield ratio of the final steel plate.
  • the invention ensures the ferrite content in the tempered sorbite structure of the steel plate through the tempering treatment at a temperature higher than and close to AC1 and closes to the temperature of AC1, so that the ferrite is coarsened and the ferrite lamella is maximized. Up to 2um. Improve the toughness of the steel plate and reduce the yield ratio. For thin gauge steel plates with a thickness of 12-50mm, the yield strength is greater than or equal to 590MPa, the tensile strength is between 680 and 820MPa, the yield ratio is less than or equal to 0.90, the elongation is greater than or equal to 20%, and the impact toughness at -196°C is greater than or equal to 200J.
  • Figure 1 is a metallographic diagram of a typical structure of the test steel in Example 2 of the present invention.
  • Figure 2 is the structure of the test steel of Example 2 of the present invention after secondary quenching, and the initial austenite grain morphology under corrosion by a picric acid alcohol solution.
  • the production process of the high-strength and low-yield ratio LNG ship 9Ni steel plate of the present invention is: converter or electric furnace steelmaking->RH vacuum degassing->LF refining->RH high vacuum degassing->Ca treatment->continuous casting- >Slow cooling treatment of cast slab->Slab surface cleaning->heating->rolling->quenching->tempering.
  • the production method of the high-strength low-yield ratio LNG ship 9Ni steel plate of the embodiments 1-4 of the present invention includes the following steps:
  • step (3) Put the continuous casting billet obtained in step (3) into a walking heating furnace at an average heating rate of 10-14cm/min, and heat to 1180-1250°C. When the temperature of the core reaches the surface temperature, heat preservation is started. The time is not less than 1 hour. The alloying elements in the steel are fully dissolved to ensure the uniformity of the composition and performance of the final product. And control the heating time of 600 ⁇ 900°C ⁇ 0.32min/mm.
  • the quenching temperature of steel plate is 840 ⁇ 10°C, the holding time after furnace temperature reaches temperature is 30-60min; the secondary quenching temperature is 625 ⁇ 10°C, the holding time after furnace temperature reaches temperature is 30-60min; quenching medium For water.
  • Tempering The tempering temperature of the steel plate is 560 ⁇ 10°C, and the holding time is 120 ⁇ 180min.
  • Figures 1 and 2 show the microstructure photos of the test steels of Examples 1 and 2.
  • the microstructure of the finished steel plate is tempered sorbite structure. After secondary quenching, the original austenite grain size is larger than 40um, and the smaller size is less than 10um. It can be seen that through two-stage controlled rolling and controlled cooling and selection of appropriate quenching process parameters, multiple sizes of original austenite grains can be obtained, the yield ratio of the steel plate can be reduced, and the elongation of the steel plate can be increased. In the tempering process, close to AC 1 point for a long time heat preservation treatment to coarsen the ferrite layer. Further reduce the yield ratio and increase the elongation.
  • the invention adopts high temperature controlled rolling and off-line quenching + tempering process to control from the perspectives of chemical composition design, base material structure, inclusions, center segregation, quenching and tempering temperature and time, etc., to ensure that while achieving ultra-high strength,
  • the elongation of the steel and the low-temperature impact toughness of -196°C are good, which achieves the purpose of reducing the low yield ratio of the thin gauge 9Ni steel plate.
  • Table 1 The chemical composition of the super-strength steel sheet in the embodiment (wt%)
  • Example Billet thickness mm Overheating degree °C Dynamic soft depression interval fs Slow cooling start temperature°C Hydrogen expansion time hour 1 150 25 0.35-0.95 690 48 2 150 18 0.35-0.95 650 48 3 150 15 0.35-0.95 680 48 4 150 15 0.35-0.95 700 48

Abstract

一种高强度低屈强比船舶LNG储罐用9Ni钢板，化学成分按质量百分比计为C：0.02～0.05％，Si：0.10～0.30％，Mn：0.50～0.80％，Ni：8.90～9.50％，P：≤0.0070％，S：≤0.0020％，Cr：0.10～0.25％，Alt：0.010～0.035％，Nb：0.010～0.020％，Ca：0.0005～0.0030％，O：≤0.0012％，N：≤0.004％，H：≤0.00015％，余量为Fe及不可避免的杂质元素。生产工艺流程为：转炉或电炉炼钢->RH真空脱气->LF精炼->RH高真空脱气->Ca处理->连铸->铸坯缓冷处理->铸坯表面清理->加热->轧制->淬火->回火。该9Ni钢板，采用低C，9％Ni，增加Nb、Cr的成分设计，进行高温热轧，随后进行特殊的QLT热处理工艺，获得良好的强韧性以及低屈强比的9Ni钢。

Description

高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法 技术领域
本发明属于钢铁(铁基合金)冶金领域，具体涉及、高强度低屈强比LNG船用9Ni钢板及其制造方法。
背景技术
LNG是liquefied natural gas即液态天然气的简称，是一种清洁、高效的能源，可在-162℃低温下液化，液化后的体积缩小至原体积的1/600，大大节约储运空间。LNG还具有热值大、性能高等特点。在很多国家，LNG被列为首选燃料。中国利用LNG进行优化国内的能源配置结构，保障能源供应安全、保护生态环境，实现经济和社会的可持续发展。LNG的运输主要还是依靠大型船舶，船舶上再建造储罐，储罐的材料必须具有足够的强度和韧性、低的屈强比等。
9Ni钢因其与不锈钢相比，合金含量相对少、价格便宜的优点，与低温用铝合金相比具有许用应力大、热膨胀率小的优点，所以被选用为LNG罐主体材料。由于9Ni钢Ni含量高、表面质量要求高、杂质元素要求严苛，给冶炼、轧制、热处理带来一系列难题，目前能够成功批量生产的企业不多，再加上用户对国内市场认可度不高的影响，实际能够对市场供货的国内厂家更是屈指可数。
此外，高强高、-196℃深冷环境下使用，屈强比高也是制约9Ni钢生产的重要因素。特别是屈强比，它对工程的限制因素特别大，比如管线钢应用过程中，考虑到包辛格效应，工程使用管线钢重要条款是屈强比不得高于0.92，对于高层建筑用钢，屈强比不得高于0.85。LR船级社规范中也强制要求所有船舶用钢，连同9Ni钢在内，其屈强比不得高于0.94.
为了安全起见，船东通常要求在满足船级社规范的基础上，要求LNG船用9Ni钢还需满足欧洲标准En10028-4对应牌号X7Ni9或者美国标准对应牌号SA553type-I的要求。在欧洲标准与美国标准中，9Ni钢屈服强度分别要求680MPa和690MPa。通过实际9Ni钢供货来看， 同种成分体系下的9Ni钢屈服强度越高，屈强比越难控制，钢板 越薄屈强比越高。这是因为9Ni钢的交货态组织是细小的回火索氏体。晶粒越细，屈服 强度越高，导致的屈强比也越高。
现有技术中，中国专利CN103602888公开了一种热轧低压缩比9Ni厚钢板及其制造方法，该方法是通过热轧状态不经过热处理方法获得了9Ni钢，组织为回火马氏体为基体+4-15％逆转变回火奥氏体，尽管如此，仅有实施例1达到了欧洲标准的屈服强度的下限值，屈强比大于0.93。中国专利CN 10125668公开了一种9Ni钢制造方法，其制备工艺流程为主要是模拟连铸连轧工艺，从而缩短生产工艺流程，这在工业化生产中较难实现，且产品强度较低，达不到实际供货要求。中国专利CN101864537公开了一种含Cu的9Ni钢制造方法，其制造的厚度为20mm。热轧后层流冷却至200℃以下，这个过程中会有较大的残余应力，不适合薄宽钢板的板形控制。此外，钢板的屈服强度虽然高达710MPa，但是牺牲了9Ni钢的高韧性，实际钢板-196℃冲击值仅有120J，批量供货得富余量不大。
为了解决现有技术的不足，对9Ni钢特别是薄规格的9Ni钢板，进行低C，9％Ni，增加Nb、Cr的成分设计，进行高温热轧，随后进行特殊的QLT热处理工艺，获得良好的强韧性(强度和韧性)以及低屈强比的9Ni钢，并易于宽薄规格9Ni钢板表面质量、板形的控制。
发明内容
针对现有技术中薄规格的9Ni钢板存在屈强比高或低温韧性不足的缺陷，本发明对9Ni钢特别是薄规格的9Ni钢板，进行低C，9％Ni，增加Nb、Cr的成分设计，进行高温热轧，随后进行特殊的QLT热处理工艺，获得良好的强韧性(强度和韧性)以及低屈强比的9Ni钢，并易于宽薄规格9Ni钢板表面质量、板形的控制。
为实现上述目的，本发明对钢板化学成分的设计：按质量百分比计为C：0.02～0.05％，Si：0.10～0.30％，Mn：0.50～0.80％，Ni：8.90～9.50％，P：≤0.0070％，S：≤0.0020％，Cr：0.10～0.25％，Alt：0.010～0.035％，Nb：0.010～0.020％，Ca:0.0005～0.0030％，O：≤0.0012％，N：≤0.004％，H：≤0.00015％，余量为Fe及不可避免的杂质元素。
本发明中钢成分的限定理由阐述如下：
C的加入可以增加钢的淬透性，特别是中厚板生产，可以显著提高强度，但是C含量过多不利于钢的-196℃超低温冲击性能、超低温应变时效性能、焊接性能以及耐蚀性能，所以本发明中碳含量控制介于0.02～0.05％。
Si主要用于脱氧，虽要依据不同的冶炼方式来确定其加入量，但要获得良好的钢板 性能，必须在0.10％以上，氧化铁皮中但若超过0.30％以上易形成硅铝尖晶石，不易去除，考虑到9Ni钢表面质量尤其重要，所以本发明进行低Si含量控制，并规定其上限为0.30％。
Mn是提高钢淬透性的元素，并起固溶强化作用以弥补钢中因C含量降低而引起的强度损失。当钢中Mn含量过低时，无法充分发挥强度确保的作用，但当Mn含量过高时则会增加其碳当量从而损坏焊接性能。另外，Mn易在钢板中心产生偏析，降低钢板中心部位的冲击韧性。因此，本发明Mn含量控制为0.50～0.80％。
Ni是提高钢板的淬透性并可以显著改善其低温韧性的元素，对冲击韧性和韧脆转变温度具有良好的影响。但Ni含量太高时，板坯表面易生成黏性较高的氧化铁皮，难以去除，影响钢板的表面质量。另外，Ni也是贵重金属，含量过高会增加成本。因此，本发明在满足按照船级社规范与欧洲标准与美国标准的前提下，将其含量控制在8.90～9.50％，有利于达到最优的性价比。
Cr是提高钢淬透性的元素，能够抑制多边形铁素体和珠光体的形成，在淬火过程中促进低温组织马氏体的转变，提高钢的抗拉强度。但Cr含量过高将影响钢的韧性，并引起回火脆性。本发明中铬含量控制在0.10～0.25％。
Nb的溶质拖曳作用和Nb(C,N)对奥氏体晶界的钉扎作用，均抑制形变奥氏体的再结晶，扩大奥氏体非再结晶区间，可以提高精轧开轧温度，保证钢板板型，易于实现高温轧制，降低钢板的屈强比，避开二次氧化铁皮形成的温度区间。但过多的Nb也会导致钢板的细晶形成，提高屈强比，故本发明控制其含量在窄区间内0.010～0.020％。
Ca处理是本发明钢种的必要处理环节，0.0005～0.0030％的Ca不仅可以降低硫化物带来的性能危害，还可以是尖锐的Al 2O 3夹杂变性为球性低熔点夹杂，从而减少钢板轧制过程中硬质夹杂物尖角处微裂纹的产生，提高钢板冲击韧性。
P虽能提高耐蚀性，但会降低低温韧性和影响钢板的可焊性，对结构钢是不适当的，本发明规定其控制在0.0070％以下。
S形成MnS夹杂物，也会导致中心偏析，对耐蚀性也有不良影响，发明规定在其控制在0.0020％以下。
Al主要是起固氮和脱氧作用。Al与N接合形成的AlN可以有效地细化晶粒，但含量过高会损害钢的韧性。因此，本发明控制其含量(Alt)在0.010～0.035％。
O、N：有害气体元素，含量高，夹杂物多，降低钢板塑性、韧性和焊接弯曲性能。本发明严格控制O含量不高于0.0012％；N含量不高于0.004％。
H：有害气体元素。H含量高，易产生白点，降低钢板塑韧性，严重危害钢板使用性能。H致延迟裂纹是高强钢切割、冷弯等应用过程产生失效的主要原因之一。本发明为提高钢板综合性能，严格控制H含量在0.00015％以内。
本发明另提供上述一种具有良好低温韧性的高强度低屈强比LNG船用9Ni钢板的 制备方法，具体工艺如下，
冶炼连铸工艺：冶炼原料依次经转炉冶炼、RH精炼、LF精炼、RH精炼、为了控制钢板内部疏松、偏析，进行低过热度浇注，全程氩气保护浇注，以及动态轻压下控制。浇铸过热度控制在5～25℃；轻压下区间控制在0.40≤fs≤0.90，其中fs为铸坯中固相份数，以保证铸坯中心偏析不高于C1.0级。
板坯缓冷及清理修磨工艺：铸坯下线后，必须进行缓冷处理。铸坯要求堆垛入坑或加罩。缓冷开始温度要求不低于600℃，时间不得低于48小时。表面机器打磨清理铸坯，铸坯上下表各磨去1.5mm厚。
加热工艺：将铸坯送入步进式加热炉，平均加热速率10～14cm/min，为保证高温度轧制，加热至1180-1250℃，待心部温度到达表面温度时开始保温，保温时间不低于1小时。使钢中的合金元素充分固溶以保证最终产品的成份及性能的均匀性。并控制600～900℃温度区间内加热时间≥0.32min/mm。
轧制工艺：钢坯出炉后经高压水除鳞后进行粗轧+精轧两阶段控制轧制，其中粗轧的开轧温度介于1080-1150℃，粗轧后三道单道次压下率≥15％。待温厚度≥1.8H，其中H为成品厚度。精轧采取高温轧制，开轧温度介于900～980℃。轧制完成之后钢板不经ACC机组进行加速冷却，耳进行空气冷却。
淬火热处理工艺：轧制后钢板进行离线淬火处理。经测定本发明钢，铁素体奥氏体平衡相变开始温度AC 1为608℃，铁素体奥氏体平衡相变结束温度AC 3为725℃，第一次淬火(一淬)温度840±10℃，炉温到温后保温时间为30～60min。二次淬火(二淬)温度为625±10℃，炉温到温后保温时间为30～60min。为保证钢板的均匀性，温度控制精度为±10℃。
回火热处理工艺：钢板淬火后，在560±10℃回火。钢板厚度1/2处到温后，回火保温时间120～180min，给予足够的时间，使淬火马氏体中的碳充分扩散，获得铁素体，并在随后长时间的保温过程中，铁素体片层长大，保证钢板强韧性最佳匹配，并降低钢板屈服比，提升钢板工程应用性。
与现有技术相比，本发明的特点在于：
本发明采用低C、高Ni、添加Cr，保证钢板淬透性，提高钢板的抗拉强度，降低屈强比，增加Nb含量，保证钢板高温轧制，获得相对均匀大晶粒的初始变形奥氏体晶粒。利用钢板组织遗传性，在淬火保温过程中获得较大尺寸的母相奥氏体。
本发明采用对铸坯上下表面各清理1.5mm厚、加热过程中控制加热、高压水除鳞、 高温轧制等系列手段保证钢板具有良好的钢板表面质量。
本发明通过加入Nb，分段加热控制，高温轧制，轧后不浇水，保证了9Ni钢板的良好板形，也防止因矫直导致的钢板划伤，影响钢板表面质量。
本发明通过双RH处理，保证了钢板的低C含量控制稳定性。
本发明通过热处理，提高一淬温度，保证初始奥氏体晶粒的大尺寸，二淬形成大尺寸、小尺寸奥氏体晶粒并存的组织，保证最终钢板的低屈强比。
本发明通过在高于并趋近于AC1的温度下进行回火处理，并长时间保温，保证钢板回火索氏体组织中铁素体含量，粗化铁素体，使铁素体片层最大可达2um。提升钢板的韧性，降低屈强比。对于12～50mm厚的薄规格钢板，屈服强度≥590MPa，抗拉强度介于680～820MPa，屈强比≤0.90，延伸率≥20％，-196℃下冲击韧性≥200J。
附图说明
图1是本发明实施例2的试验钢典型组织金相图；
图2是本发明实施例2的试验钢经过二淬后的组织，通过苦味酸酒精溶液腐蚀下的初始奥氏体晶粒形貌。
具体实施方式
以下结合附图实施例对本发明作进一步详细描述。
本发明的高强度低屈强比LNG船用9Ni钢板的生产工艺流程为：转炉或电炉炼钢->RH真空脱气->LF精炼->RH高真空脱气->Ca处理->连铸->铸坯缓冷处理->铸坯表面清理->加热->轧制->淬火->回火。
本发明实施例1-4的高强度低屈强比LNG船用9Ni钢板的生产方法，包括如下步骤：
(1)冶炼：选用优质原料，采用150吨转炉冶炼，RH高真空脱气处理后送入LF炉精炼并破空进行Ca处理，再经过RH真空脱气，成分控制见表1。
(2)连铸：将冶炼的钢水浇铸成150mm厚的连铸坯。浇铸温度控制在液相线以上5-25℃。浇铸过程中实施动态轻压下。连铸工艺参数见表2。
(3)铸坯缓冷处理：连铸板坯入坑进行缓冷扩氢，入坑温度及缓冷时间见表2。缓冷后对铸坯表面用机器打磨清理，上下表各清理掉1.5mm厚。
(4)加热：将步骤(3)所得连铸坯放入步进式加热炉，平均加热速率10～ 14cm/min，加热至1180-1250℃,待心部温度到达表面温度时开始保温，保温时间不低于1小时。使钢中的合金元素充分固溶以保证最终产品的成份及性能的均匀性。并控制600～900℃加热时间≥0.32min/mm。
(5)轧制：钢坯出炉后经高压水除鳞处理后，进行粗轧+精轧两阶段控制轧制。粗轧的开轧温度介于1080-1150℃，粗轧后三道道次压下率≥12％。待温厚度≥1.8H，其中H为成品厚度。精轧采取高温轧制，精轧开轧温度介于900～980℃，粗轧结束温度≥820℃。轧制完成之后钢板不经ACC机组进行加速冷却，进行空气冷却。相关工艺参数见表3。
(6)淬火：钢板淬火温度为840±10℃,炉温到温后保温时间为30～60min；二次淬火温度为625±10℃，炉温到温后保温时间为30～60min；淬火介质为水。
(7)回火：钢板回火温度为560±10℃，保温时间为120～180min。
(8)回火后钢板进行横向拉伸、横向冲击试验。
具体成分、工艺参数见表1-3。各实例样板对应的性能见表4。
图1、2给出了实施例1、2试验钢的微观组织照片。成品钢板的微观组织为回火索氏体组织，二淬后原始奥氏体晶粒尺寸大的≥40um，小尺寸不足10um。可见，通过两阶段控轧控冷和合适的淬火工艺参数选择，可以得到多尺寸的原始奥氏体晶粒，降低钢板屈强比，提高钢板的延伸率。在回火过程中接近AC 1点长时间保温处理，粗化铁素体片层。进一步降低屈强比，提高延伸率。
本发明采用高温控轧和离线淬火+回火工艺，从化学成分设计、母材组织、夹杂物、中心偏析、淬回火温度及时间等角度进行控制，保证在实现超高强度的同时，钢的延伸率、-196℃低温冲击韧性良好，达到了降低薄规格9Ni钢板低屈强比的目的。
表1实施例超强钢板的化学成分(wt％)
Figure PCTCN2020084014-appb-000001
表2连铸工艺控制
实施例 铸坯厚度mm 过热度℃ 动态轻压下区间fs 缓冷起始温度℃ 扩氢时间hour
1 150 25 0.35-0.95 690 48
2 150 18 0.35-0.95 650 48
3 150 15 0.35-0.95 680 48
4 150 15 0.35-0.95 700 48
表3轧制工艺控制
Figure PCTCN2020084014-appb-000002
表4本发明实施例横向拉伸、横向冲击性能
Figure PCTCN2020084014-appb-000003
尽管以上详细地描述了本发明的优选实施例，但是应该清楚地理解，对于本领域的技术人员来说，本发明可以有各种更改和变化。凡在本发明的精神和原则之内所作的任何修改、等同替换、改进等，均应包含在本发明的保护范围之内。

Claims (7)

  1. 一种高强度低屈强比船舶LNG储罐用9Ni钢板，其特征在于：钢板化学成分按质量百分比计为C：0.02～0.05％，Si：0.10～0.30％，Mn：0.50～0.80％，Ni：8.90～9.50％，P：≤0.0070％，S：≤0.0020％，Cr：0.10～0.25％，Alt：0.010～0.035％，Nb：0.010～0.020％，Ca:0.0005～0.0030％，O：≤0.0012％，N：≤0.004％，H：≤0.00015％，余量为Fe及不可避免的杂质元素。
  2. 根据权利要求1所述的高强度低屈强比船舶LNG储罐用9Ni钢板，其特征在于：钢板厚度12～50mm。
  3. 根据权利要求1或2所述的高强度低屈强比船舶LNG储罐用9Ni钢板，其特征在于：钢板屈服强度≥590MPa，抗拉强度介于680～820MPa，屈强比≤0.90，延伸率≥20％，-196℃下冲击韧性≥200J；钢板组织为回火索氏体，且铁素体片层可达2um。
  4. 一种高强度低屈强比船舶LNG储罐用9Ni钢板的制造方法，其特征在于：包括如下步骤
    (1)钢水冶炼：冶炼原料依次经转炉冶炼、RH精炼、LF精炼、RH精炼；
    (2)浇注成坯：浇铸过热度控制在5-25℃，轻压下区间满足0.35≤fs≤0.95，其中fs为铸坯中固相份数；铸坯中心偏析不高于C1.0级；
    (3)铸坯缓冷和表面清理：铸坯入坑或加罩缓冷处理，缓冷起始温度不低于600℃，缓冷48小时以上，缓冷后铸坯表面清理打磨；
    (4)加热
    采用步进式加热炉，控制平均加热速率10～14cm/min，加热至1180-1250℃，控制600～900℃区间内加热时间不低于0.32min/mm，待心部温度和表面温度一致时开始保温，保温时间不低于1小时。使钢中的合金元素充分固溶以保证最终产品的成份及性能的均匀性；
    (5)轧制
    钢坯出炉后经高压水除鳞处理后进行粗轧+精轧两阶段控制轧制，细化晶粒：粗轧的开轧温度介于1080-1150℃，粗轧后三道道次压下率≥15％，待温厚度≥1.8H，其中H为成品厚度；精轧采取高温轧制，开轧温度介于900-980℃，轧制完成之后不可水冷而空气冷却；
    (6)淬火
    轧制后钢板离线淬火处理，一淬温度为840±10℃，炉温到温后保温30-60min；二淬温度为625±10℃，炉温到温后保温时间为30-60min；淬火介质为水；
    (7)回火
    淬火后的钢板进行回火，回火温度为560±10℃，保温时间为120-180min。
  5. 根据权利要求4所述的高强度低屈强比船舶LNG储罐用9Ni钢板的制造方法，其特征在于：步骤(1)钢水冶炼按照化学成分为C：0.02～0.05％，Si：0.10～0.30％，Mn：0.50～0.80％，Ni：8.90～9.50％，P：≤0.0070％，S：≤0.0020％，Cr：0.10～0.25％，Alt：0.010～0.035％，Nb：0.010～0.020％，Ca:0.0005～0.0030％，O：≤0.0012％，N：≤0.004％，H：≤0.00015％，余量为Fe及不可避免的杂质元素的进行。
  6. 根据权利要求4所述的高强度低屈强比船舶LNG储罐用9Ni钢板的制造方法，其特征在于：步骤(3)中对铸坯上下表面分别进行打磨处理，上下表各清理掉1.5mm厚。
  7. 根据权利要求4所述的高强度低屈强比船舶LNG储罐用9Ni钢板的制造方法，其特征在于：步骤(6)，在二淬后初始奥氏体晶粒大、小尺寸并存，晶粒尺寸大的≥40um，小尺寸不足10um，最终显微组织为回火索氏体，铁素体片层最大可达2um。
PCT/CN2020/084014 2019-08-24 2020-04-09 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法 WO2021036272A1 (zh)

Priority Applications (3)

Application Number Priority Date Filing Date Title
EP20856109.2A EP4015668A4 (en) 2019-08-24 2020-04-09 HIGH STRENGTH 9NI LOW YIELD STRENGTH STEEL PLATE FOR SHIP'S LNG STORAGE VESSELS AND PROCESS FOR THEIR MANUFACTURE
US17/927,881 US20230323494A1 (en) 2019-08-24 2020-04-09 A 9ni steel plate for ship lng storage tank with high strength and low yield ratio and its production method
KR1020227006048A KR20220035962A (ko) 2019-08-24 2020-04-09 고강도 저항복비 선박 LNG 저장탱크용 9Ni 강판과 그 제조방법

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201910786113.1A CN110541110B (zh) 2019-08-24 2019-08-24 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法
CN201910786113.1 2019-08-24

Publications (1)

Publication Number Publication Date
WO2021036272A1 true WO2021036272A1 (zh) 2021-03-04

Family

ID=68711943

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2020/084014 WO2021036272A1 (zh) 2019-08-24 2020-04-09 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法

Country Status (5)

Country Link
US (1) US20230323494A1 (zh)
EP (1) EP4015668A4 (zh)
KR (1) KR20220035962A (zh)
CN (1) CN110541110B (zh)
WO (1) WO2021036272A1 (zh)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113481434A (zh) * 2021-06-21 2021-10-08 邯郸新兴特种管材有限公司 屈服强度125钢级的厚壁超级13Cr无缝钢管及生产方法
CN114134293A (zh) * 2021-09-23 2022-03-04 江阴兴澄特种钢铁有限公司 一种低偏析度LNG船用9Ni钢的制备方法
CN114214496A (zh) * 2021-11-26 2022-03-22 首钢集团有限公司 一种30MnSi盘条钢及其制备方法
CN115323285A (zh) * 2022-07-13 2022-11-11 首钢京唐钢铁联合有限责任公司 一种车厢钢板及其制备方法
CN115786812A (zh) * 2023-02-10 2023-03-14 江苏省沙钢钢铁研究院有限公司 大厚度低屈强比LNG储罐用9Ni钢板及其生产方法

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110541110B (zh) * 2019-08-24 2021-02-26 江阴兴澄特种钢铁有限公司 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法
CN111440990B (zh) * 2020-03-30 2022-07-15 江阴兴澄特种钢铁有限公司 一种低剩磁、表面质量优异的船用5Ni钢板的制造方法
CN112647021B (zh) * 2020-12-09 2021-10-15 上海电气上重铸锻有限公司 超低温工程紧固件用高强度9%Ni钢及其制备方法
CN113584384A (zh) * 2021-07-22 2021-11-02 江苏省沙钢钢铁研究院有限公司 一种易焊接的低屈强比调质石油储罐钢板及其制造方法
CN114427024B (zh) * 2021-12-17 2024-01-23 山西平阳重工机械有限责任公司 一种消除液压支架外缸回火脆性的工艺
CN114438393B (zh) * 2022-01-14 2023-03-21 南京钢铁股份有限公司 一种防止高镍钢板表面沿晶氧化裂纹的方法
CN114737114A (zh) * 2022-03-24 2022-07-12 南京钢铁股份有限公司 一种9Ni用钢及其生产方法
CN114836692A (zh) * 2022-05-06 2022-08-02 鞍钢股份有限公司 大压缩比、低屈强比船用高镍钢板及其制造方法
CN115786634A (zh) * 2022-12-06 2023-03-14 舞阳钢铁有限责任公司 一种提高含镍低温钢焊接性能的方法
CN116790989A (zh) * 2023-06-30 2023-09-22 湖南华菱湘潭钢铁有限公司 一种超低温调质钢薄板及其制备方法与应用

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007080646A1 (ja) * 2006-01-13 2007-07-19 Sumitomo Metal Industries, Ltd. 極低温用鋼
CN101256680A (zh) 2008-03-18 2008-09-03 耿杰 一种刷卡装置
CN101864537A (zh) 2010-05-24 2010-10-20 江苏省沙钢钢铁研究院有限公司 应用于深冷环境的超高强度9Ni钢及其制备工艺
CN103602888A (zh) 2013-12-02 2014-02-26 南京钢铁股份有限公司 一种低压缩比热轧9Ni钢厚板及其制造方法
WO2019087318A1 (ja) * 2017-10-31 2019-05-09 新日鐵住金株式会社 低温用ニッケル含有鋼板およびそれを用いた低温用タンク
WO2019124671A1 (ko) * 2017-12-24 2019-06-27 주식회사 포스코 용접부 인성이 우수한 저온용 강재 및 그 제조방법
CN110129676A (zh) * 2019-05-27 2019-08-16 南京钢铁股份有限公司 一种LNG储罐用7Ni钢板及生产工艺
CN110541110A (zh) * 2019-08-24 2019-12-06 江阴兴澄特种钢铁有限公司 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3972553B2 (ja) * 1999-02-15 2007-09-05 住友金属工業株式会社 テーパー鋼板及びその製造方法
CN102172775B (zh) * 2005-10-12 2013-08-28 日立粉末冶金株式会社 烧结阀座的制造方法
JP5126780B2 (ja) * 2006-01-13 2013-01-23 新日鐵住金株式会社 溶接熱影響部のｃｔｏｄ特性に優れた極低温用鋼
EP2743363B1 (en) * 2011-09-28 2017-11-01 Nippon Steel & Sumitomo Metal Corporation Nickel steel plate and manufacturing process therefor
CN107604255B (zh) * 2017-08-02 2019-06-07 江阴兴澄特种钢铁有限公司 一种高探伤质量的9Ni船用低温容器钢板及其制造方法

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007080646A1 (ja) * 2006-01-13 2007-07-19 Sumitomo Metal Industries, Ltd. 極低温用鋼
CN101256680A (zh) 2008-03-18 2008-09-03 耿杰 一种刷卡装置
CN101864537A (zh) 2010-05-24 2010-10-20 江苏省沙钢钢铁研究院有限公司 应用于深冷环境的超高强度9Ni钢及其制备工艺
CN103602888A (zh) 2013-12-02 2014-02-26 南京钢铁股份有限公司 一种低压缩比热轧9Ni钢厚板及其制造方法
WO2019087318A1 (ja) * 2017-10-31 2019-05-09 新日鐵住金株式会社 低温用ニッケル含有鋼板およびそれを用いた低温用タンク
WO2019124671A1 (ko) * 2017-12-24 2019-06-27 주식회사 포스코 용접부 인성이 우수한 저온용 강재 및 그 제조방법
CN110129676A (zh) * 2019-05-27 2019-08-16 南京钢铁股份有限公司 一种LNG储罐用7Ni钢板及生产工艺
CN110541110A (zh) * 2019-08-24 2019-12-06 江阴兴澄特种钢铁有限公司 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113481434A (zh) * 2021-06-21 2021-10-08 邯郸新兴特种管材有限公司 屈服强度125钢级的厚壁超级13Cr无缝钢管及生产方法
CN113481434B (zh) * 2021-06-21 2022-05-31 邯郸新兴特种管材有限公司 屈服强度125钢级的厚壁超级13Cr无缝钢管及生产方法
CN114134293A (zh) * 2021-09-23 2022-03-04 江阴兴澄特种钢铁有限公司 一种低偏析度LNG船用9Ni钢的制备方法
CN114134293B (zh) * 2021-09-23 2024-02-09 江阴兴澄特种钢铁有限公司 一种低偏析度LNG船用9Ni钢的制备方法
CN114214496A (zh) * 2021-11-26 2022-03-22 首钢集团有限公司 一种30MnSi盘条钢及其制备方法
CN114214496B (zh) * 2021-11-26 2024-04-09 首钢集团有限公司 一种30MnSi盘条钢及其制备方法
CN115323285A (zh) * 2022-07-13 2022-11-11 首钢京唐钢铁联合有限责任公司 一种车厢钢板及其制备方法
CN115786812A (zh) * 2023-02-10 2023-03-14 江苏省沙钢钢铁研究院有限公司 大厚度低屈强比LNG储罐用9Ni钢板及其生产方法

Also Published As

Publication number Publication date
KR20220035962A (ko) 2022-03-22
US20230323494A1 (en) 2023-10-12
CN110541110B (zh) 2021-02-26
CN110541110A (zh) 2019-12-06
EP4015668A1 (en) 2022-06-22
EP4015668A4 (en) 2023-01-11

Similar Documents

Publication Publication Date Title
WO2021036272A1 (zh) 高强度低屈强比船舶LNG储罐用9Ni钢板及其制造方法
WO2021196820A1 (zh) 一种低剩磁、表面质量优异的船用5Ni钢板的制造方法
WO2022011936A1 (zh) 一种具有优良低温韧性的高强度容器板及制造方法
WO2022022047A1 (zh) 一种低温环境下使用的低屈强比粒状贝氏体高强钢板及其制造方法
CN109576585B (zh) 一种大型集装箱船用eh47止裂钢及其制造方法
WO2020237975A1 (zh) 一种LNG储罐用7Ni钢板及生产工艺
CN110129685B (zh) 一种超低温容器用7Ni钢厚板的制造方法
WO2022067962A1 (zh) 低成本高性能Q370qE-HPS桥梁钢及生产方法
CN106811700B (zh) 一种厚规格抗酸性x60ms热轧卷板及其制造方法
KR20230037040A (ko) 우량한 코어부 인성을 구비한 고강도 용기용 후판(厚板) 및 제조방법
CN105925896B (zh) 一种1000MPa级高强度高塑性热轧钢板及其制造方法
WO2021027188A1 (zh) 一种铸坯生产超低温高强度抗酸容器钢的方法
CN110184528A (zh) 一种高温模拟焊后热处理条件下具有优异性能的q345r钢板及其制造方法
CN109280848A (zh) 一种低镍型液化天然气储罐用钢板及其制备方法
CN105441798A (zh) 一种低温容器用Ni钢中厚板的制造方法
CN105331890B (zh) 一种在线淬火生产高韧性5Ni钢中厚板的方法
WO2023173803A1 (zh) 一种客货混运铁路用耐滚动接触疲劳钢轨及其生产方法
WO2024001078A1 (zh) 一种80mm厚690MPa级超高强韧海工钢板及其制备方法
CN112680652A (zh) 一种Cr-Mo低合金压力容器用钢板及其制备方法
CN114875331B (zh) 一种具有优良心部疲劳性能的610MPa级厚钢板及其生产方法
CN110273106A (zh) 一种260MPa级冷轧连退搪瓷钢及其生产方法
CN101255528A (zh) 超低温韧性优异的含铌钢板及其轧制方法
CN111424221B (zh) 一种层压用不锈钢板及其制造方法
CN115369323B (zh) 一种800MPa级抗氢致裂纹容器钢板及其生产方法
WO2023138595A1 (zh) 一种耐氢氧化钠腐蚀的高强度管道及其制造方法

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: 20856109

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 20227006048

Country of ref document: KR

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 2020856109

Country of ref document: EP

Effective date: 20220315