US20180298463A1 - Pressure vessel steel plate resistant against hydrogen-induced cracking and manufacturing method thereof - Google Patents

Pressure vessel steel plate resistant against hydrogen-induced cracking and manufacturing method thereof Download PDF

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US20180298463A1
US20180298463A1 US15/735,146 US201615735146A US2018298463A1 US 20180298463 A1 US20180298463 A1 US 20180298463A1 US 201615735146 A US201615735146 A US 201615735146A US 2018298463 A1 US2018298463 A1 US 2018298463A1
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steel plate
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Haikuan LIU
Jingtao Li
Zhuzhong GAO
Jian Zhang
Pengcheng Yu
Jun Zhang
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Jiangyin Xingcheng Special Steel Works Co Ltd
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Jiangyin Xingcheng Special Steel Works Co Ltd
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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
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • C21D8/0221—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
    • 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
    • C22C38/04—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
    • C22C38/12—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron

Definitions

  • the invention belongs to the field of steel plate manufacturing, in particular to a thickness of 50 mm SA516Gr70 CHIC) pressure vessel steel plate which is resistant to hydrogen induced cracking (HIC), and manufacturing method thereof.
  • SA516Gr70 (HIC) steel plate is mainly used in petroleum and chemical equipment used in wet H2S corrosion environment.
  • Hydrogen induced cracking is a common failure mode in wet hydrogen sulfide environment, H2S reacts with steel surface to generate hydrogen atoms, the hydrogen atoms diffuse into steel and gather at the metallurgical defect position to generate hydrogen molecules. In this way, high internal stress is generated inside steel, resulting in interfacial crack and hydrogen blistering, and when the pressure of hydrogen continues to increase, small hydrogen bubbles tend to connect with each other, forming a ladder like hydrogen induced cracking
  • the invention patent CN104480384A adopts the normalizing and air cooling technology during production, and subsequent cooling in still air during production.
  • the invention patent CN1046411629A adopts the normalizing and air-spray cooling technology.
  • the invention patent CN102605242A adopts the quenching and tempering technology.
  • the normalizing and air cooling technology is beneficial to form uniform microstructure of steel plates, the strength of a sample can hardly meet the requirement after long-time high-temperature simulated post-welding heat treatment; By conducting air-spray cooling after normalizing, the banded structure of steel plates can be improved to a certain extent, but the effect on improving the strength of steel plate is not obvious. Since tempering treatment is not used, a martensitic structure or bainite structure might be generated on the surface of steel plate due to fast cooling, which leads to low strength and high surface hardness of steel plate, and eventually leads to edge cracking of steel plate in container manufacturing process; The quenching and tempering technology can remarkably improve the strength of steel plate. However, due to the fact that quenching temperature is high and cooling speed is too fast, it will generate non-uniform microstructure formation of steel plates, and hydrogen-induced-cracking sensitivity is increased.
  • the invention provides anti-hydrogen-induced-cracking pressure vessel steel and a manufacturing method thereof.
  • the anti-hydrogen-induced-cracking pressure vessel steel is suitable for being used in wet H2S environment, composition design and production process are simple, and it is suitable for mass production, and no patent related to the technology have been found through research.
  • the invention aims to solve current technical issues mentioned in the prior art, and provides a type of manufacturing method to produce SA516Gr70(HIC) steel plate with 50 mm thickness, which can be used to produce petrochemical devices, those are able to be applied in a wet H2S corrosive environment.
  • the steel plate has high strength, and good impact toughness at low temperature, and low hardness, and high anti-HIC performance.
  • the steel plate has fine grain size and less non-metallic inclusion content without obvious banded structure. After long-time high-temperature simulated post-welding heat treatment, the strength and low temperature impact toughness of the steel plate are not reduced obviously, and the steel plate for head end can meet the manufacturing requirements of both cold forming and hot forming processes at the same time.
  • Ti: 0.01%
  • B 0.0005%: balance of Fe and unavoidable impurities, carbon equivalent Ceq less than 0.42%, the carbon equivalent formula:
  • the performance of Resistance to Hydrogen-Induced Cracking of pressure vessel steel plate is that: Resistance to Hydrogen-Induced Cracking test is conducted on the steel plate according to NACE TM0284-2011 “Experimental method for evaluating Resistance to Hydrogen-Induced Cracking performance of pressure vessel steel plate”, use solution A to do validation: crack length ratio (CLR), crack thickness ratio (CTR) and crack sensitivity ratio (CSR) of a single inspection section are all equal to 0, and no hydrogen blister is observed, in other words, no defect is observed after corrosion. After simulated post-welding heat treatment at 635 ⁇ 14° C.
  • the yield strength of the steel plate is greater than or equal to 360 Mpa, tensile strength is greater than or equal to 540 Mpa, and transverse Charpy impact energy single value is greater than or equal to 150 J; Brinell hardness of the steel plate surface at delivery-state is less than or equal to 170 HB, the grade of granularity is greater than or equal to grade 8.0, and the grade of banded structure is less than or equal to grade 2.0.
  • the main chemical of the steel plate is the combination of C, Si and Mn, the content of S and P is reduced as much as possible, alloy elements like Cr, Ni, Cu, Mo, Nb, V, Ti and B are not added intentionally.
  • the composition design is simple. Carbon element can remarkably improve the strength and hardness of the steel plate; But with the increase of carbon content, carbide segregation is prone to occur easily, resulting in the hardness of the segregation zone different from the hardness of its surrounding microstructure, leading to HIC corrosion.
  • Mn element can improve the strength of the steel plate through solution strengthening; however, when Mn higher than 1.05%, cracking sensitivity can be increased. but the adverse effect can be eliminated through intercritical quenching and tempering.
  • Silicon is mainly used as reducing agent and deoxidizer in steelmaking, and has certain solid solution strengthening effect; meanwhile, Si element can be easily segregated in grain boundary, and promote intergranular crack generation.
  • C, Mn and Si content the contents should be controlled close to upper limits in the allowable range.
  • the control range of the application is C:0.16 ⁇ 0.20%, Si:0.15 ⁇ 0.40%, Mn:1.05 ⁇ 1.20%, and the adverse effects are eliminated by subsequent heat treatment.
  • P and S are harmful elements. With the content of S increases in the steel, the amount of hydrogen entering steel when steel is soaked in H2S increases too, resulting in the sensitivity of HIC is also increased.
  • the invention also aims to provide a manufacturing method of the anti-hydrogen-induced-cracking pressure vessel steel plate, as follows:
  • Continuous casting slab is adopted for production with using process route: KR pretreatment ⁇ converter smelting process smelting ⁇ LF refining ⁇ RH refining ⁇ continuous casting. Improving purity of molten steel and reduction of slab segregation are the essential measures for resistance to hydrogen-induced cracking of steel.
  • Smelting raw material are pretreated by KR process.
  • Slag-off treatment is conducted after converter smelting process, the content of S is strictly controlled to be less than or equal to 0.001% and P is less than or equal to 0.006%.
  • Non-metallic inclusions of Class A, class B, class C, class D and class Ds in single level is less than or equal to 1, the total sum is less than or equal to 3.5;
  • a sectional heating method is adopted, total heating time is 225-300 min, the temperature of a first heating section is 1050-1150° C., the temperature of second heating section is 1200-1260° C., the temperature of soaking section is 1170-1250° C., the total heating time of the second heating section together with soaking section is longer than or equal to 120 min, the second heating section and the soaking section are matched to promote sufficient hydrogen diffusion, segregation diffusion and formation of uniform microstructure.
  • a two-stage rolling technology is adopted, the high-temperature large-reduction rolling technology is adopted in rough rolling stage.
  • the longitudinal rolling passes there are at least two passes with single-pass rolling reduction greater than or equal to 50 mm; the accumulated reduction ratio of the finish rolling stage is larger than or equal to 60%, finish rolling temperature is controlled to be 780-820° C., ACC is applied after rolling, and steel plates are stacked and slowly cooled for over 72 h after produced from production line, so that sufficient hydrogen diffusion can be realized.
  • the subcritical quenching and tempering technology is adopted, heating temperature during subcritical quenching is Ac1-Ac3, quenching temperature is 820-850° C., soaking time factor is 1.8-2.0 min/mm, and water cooling is conducted; in order to prevent the steel plate strength from greatly decreasing after simulated post-welding heat treatment, steel plate tempering temperature is not lower than simulated post-welding heat treatment temperature, tempering temperature is 640-670° C., and soaking time factor is 3.5-4.5 min/mm.
  • Subcritical quenching can reduce brittle transition temperature and refine grains, so that a proper number of evenly distributed fine ferritic structures can be obtained, crack extension can be inhibited, and steel toughness can be improved remarkably. Compared to conventional quenching technologies, it requires lower tempering temperature to obtain the steel with equal harness, and with higher toughness, to restrain the stress concentration and hinder the crack initiation and propagation; the presence of non molten ferrite in the quenched structure leads to increase the content of carbon and alloy elements in austenite. After quenching, a small amount of stable retained austenite can also prevent the initiation and propagation of cracks. Subcritical quenching can also reduce the segregation of harmful impurity elements at austenite grain boundary, then it can purify the grain boundary.
  • Our invention relates to the SA516Gr70 CHIC) anti-hydrogen-induced-cracking (HIC) pressure vessel steel plate with 50 mm thickness.
  • the steel plate has high strength, and good impact toughness at low temperature, and low hardness, and high anti-HIC performance.
  • the steel plate has fine grain size and less non-metallic inclusion content without obvious banded structure. After long-time high-temperature simulated post-welding heat treatment, the strength and low temperature impact toughness of the steel plate are not reduced obviously.
  • the head is produced by using cold forming process, due to the fact that work hardening can increase the hardness of steel plate, easily lead to cracking of steel plate.
  • the delivery-state hardness of the steel plate is controlled below 170 HB, it can still meet the requirement on cold working after work hardening. Therefore, the steel plate produced by this method can meet the requirements both on cold forming and hot forming processes for head forming process.
  • the continuous casting process is adopted to reduce the hydrogen induced cracking sensitivity by reducing the segregation of the slab, improving the purity of the molten steel, and reducing the banded structure of the steel plate.
  • the composition design of the steel plate is simple, the major elements of the steel plate are C, Si and Mn alloy, alloy elements like Ni, Cr, Cu, Mo, Nb, V and Ti are not added intentionally, the design can reduce segregation with low production cost. And the hydrogen-induced cracking sensitivity of the steel plate is reduced by reducing the content of elements S, P, H, 0 and N, and by improving the purity of molten steel.
  • Casting blanks are heated with step heating mode, particularly, the total time of the second heating segment and the soaking zone is prolonged, so that segregation diffusion can be achieved sufficiently; by means of the high-temperature large-reduction rolling technology in the high-temperature rolling stage, loose defect can be sufficiently pressed, so that the internal quality of steel plate can be improved.
  • the unique subcritical quenching and tempering technology is adopted for heat treatment of the steel plate.
  • heating temperature for subcritical quenching is low
  • the cooling rate of the cooling process during subcritical quenching is between normalizing temperature and quenching
  • strength-toughness properties in steel can be optimized after further high-temperature tempering; in this way, the tensile strength and the low temperature impact toughness of the steel plate can be improved.
  • the high surface hardness of steel plate can be avoided, the structure of the steel plate is ferrite and pearlite structure, grain size is small without obvious banded structure exists.
  • FIG. 1 is a diagram of a metallurgical structure of a steel plate according to embodiment 1 of the invention.
  • FIG. 2 is a diagram of a metallurgical structure of a steel plate according to embodiment 2 of the invention.
  • FIG. 3 is a diagram of a metallurgical structure of a steel plate according to embodiment 3 of the invention.
  • the thickness of the anti-hydrogen-induced-cracking steel plate for pressure vessel is 50 mm. Its chemical composition is determined by weight percentage: 0.17% of C, 0.34% of Si, 1.18% of Mn, 0.004% of P, 0.0005% of S, 0.00006% of H, 0.0015% of 0, 0.0035% of N, and the balance being Fe and inevitable impurity elements.
  • Carbon equivalent Ceq is less than or equal to 0.41%, and the computational formula for the carbon equivalent is
  • the manufacturing process of the steel plate is as follows:
  • Continuous casting slabs which have 370 mm in thickness are adopted for production, smelting materials are subjected to KR molten steel pretreatment, converter smelting, LF refining, RH refining and plate slab continuous casting in sequence, Slag-off treatment is conducted after converter steel making, low-superheat pouring with whole-course argon protection is adopted for continuous casting, casting blank segregation is controlled by means of the dynamic soft-reduction technology, and plate slabs are covered and slowly cooled for over 48 h after exiting the line.
  • a segmented heating method is adopted, total heating time is 270 min, the temperature of a first heating segment is 1120° C., the temperature of a second heating segment is 1250° C., the temperature of a soaking zone is 1240° C., the total heating time of the second heating segment and the soaking zone is 135 min, and sufficient diffusion of casting blank segregation is ensured.
  • a two-stage rolling technology is adopted, the high-temperature large-reduction rolling technology is adopted in the rough rolling stage, and there are three longitudinal rolling passes with single-pass rolling reduction being 25 mm, 55 mm and 50 mm respectively; porous defect can be sufficiently pressed, so that the internal quality and the core performance of the steel plate can be improved.
  • the accumulated reduction ratio of the finish rolling stage is 65%, finish rolling temperature is controlled to be 810° C., ACC fast cooling is applied after rolling, and steel plates are stacked and slowly cooled for over 72 h after steel plates come out of production line.
  • Ac1 temperature of the steel plate is 720° C.
  • Ac3 temperature is 850° C.
  • quenching temperature is 835° C.
  • soaking time factor is 1.8 min/mm
  • tempering temperature is 660° C.
  • soaking time factor is 3.8 min/mm.
  • the 50 mm thick anti-hydrogen-induced cracking pressure vessel steel plate manufactured with the method has well-matched comprehensive mechanical properties and excellent anti-hydrogen-induced-cracking performance, the mechanical properties are shown in Table 1, the anti-hydrogen-induced-cracking performance is shown in Table 4, and the photo of the metallographic structure is shown in FIG. 1 .
  • the thickness of the anti-hydrogen-induced-cracking steel plate for pressure vessel is 50 mm. Its chemical composition is determined by weight percentage: 0.18% of C, 0.32% of Si, 1.17% of Mn, 0.003% of P, 0.0006% of S, 0.00005% of H, 0.0012% of 0, 0.0036% of N, and the balance being Fe and inevitable impurity elements. Carbon equivalent Ceq is less than or equal to 0.41%, and the computational formula for the carbon equivalent is
  • the manufacturing process of the steel plate is as follows:
  • a segmented heating method is adopted, total heating time is 285 min, the temperature of a first heating segment is 1125° C., the temperature of a second heating segment is 1255° C., the temperature of a soaking zone is 1242° C., the total heating time of the second heating segment and the soaking zone is 150 min, and sufficient diffusion of casting blank segregation is ensured.
  • a two-stage rolling technology is adopted, the high-temperature large-reduction rolling technology is adopted in the rough rolling stage, and there are three longitudinal rolling passes with single-pass rolling reduction being 25 mm, 55 mm and 55 mm respectively; porous defect can be sufficiently pressed, so that the internal quality and the core performance of the steel plate can be improved.
  • the subcritical quenching and tempering technology is adopted, wherein the subcritical quenching has a quenching temperature of 842° C. and soaking time factor of 1.8 min/mm; the tempering has a tempering temperature of 650° C. and soaking time factor of 4.0 min/mm.
  • the 50 mm thick anti-hydrogen-induced-cracking pressure vessel steel plate manufactured with the method has well-matched comprehensive mechanical properties and excellent anti-hydrogen-induced-cracking performance, the mechanical properties are shown in Table 2, the anti-hydrogen-induced-cracking performance is shown in Table 4, and the photo of the metallographic structure is shown in FIG. 2 .
  • the thickness of the anti-hydrogen-induced-cracking steel plate for pressure vessel is 50 mm. Its chemical composition is determined by weight percentage: 0.16% of C, 0.35% of Si, 1.16% of Mn, 0.005% of P, 0.0007% of S, 0.00006% of H, 0.0012% of 0, 0.0033% of N, and the balance being Fe and inevitable impurity elements; carbon equivalent Ceq is less than or equal to 0.40%, and the computational formula for the carbon equivalent is
  • the manufacturing process of the steel plate is as follows:
  • Continuous casting slabs are adopted for production, smelting materials are subjected to KR pretreatment, converter smelting, LF refining, RH refining and plate slab continuous casting in sequence, slag off treatment is conducted after converter steel making, low-superheat pouring with whole-course argon protection is adopted for continuous casting, casting blank segregation is controlled by means of the dynamic soft-reduction technology, and plate slabs are covered and slowly cooled for over 48 h after steel plates come out of production line.
  • total heating time is 300 min
  • the temperature of a first heating segment is 1118° C.
  • the temperature of a second heating segment is 1252° C.
  • the temperature of a soaking zone is 1241° C.
  • the total heating time of the second heating segment and the soaking zone is 150 min, and sufficient diffusion of casting blank segregation is ensured.
  • a two-stage rolling technology is adopted, the high-temperature large reduction rolling technology is adopted in the rough rolling stage, and there are three longitudinal rolling passes with single-pass rolling reduction being 30 mm, 55 mm and 55 mm respectively; porous defect can be sufficiently pressed, so that the internal quality and the core performance of the steel plate can be improved.
  • the accumulated reduction ratio of the finish rolling stage is 68%, finish rolling temperature is controlled to be 802° C., ACC fast cooling is applied after rolling, and steel plates are stacked and slowly cooled for over 72 h after exiting the line.
  • the subcritical quenching and tempering technology is adopted, and the subcritical quenching has a quenching temperature of 840° C. and soaking time factor of 1.8 min/mm; the tempering has a tempering temperature of 645° C. and soaking time factor of 4.2 min/mm.
  • the 50 mm thick anti-hydrogen-induced-cracking pressure vessel steel plate manufactured with the method has well-matched comprehensive mechanical properties and excellent anti-hydrogen-induced-cracking performance, the mechanical properties are shown in Table 3, the anti-hydrogen-induced-cracking performance is shown in Table 4, and the photo of the metallographic structure is shown in FIG. 3 .
  • the simulated subcritical quenching and simulated tempering technology have the same parameters with the steel plate thermal treatment technology.
  • the simulated subcritical quenching and simulated tempering technology have the same parameters with the steel plate thermal treatment technology.
  • the simulated subcritical quenching and simulated tempering technology have the same parameters with the steel plate thermal treatment technology.
  • the granularity of the steel plates in all embodiments is grade 8.5, the banded structure is grade 0.5, as shown in FIG. 1 - FIG. 3 .

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CN201610241719.3A CN105886909B (zh) 2016-04-19 2016-04-19 一种抗氢致开裂压力容器钢板及其制造方法
PCT/CN2016/102379 WO2017181630A1 (zh) 2016-04-19 2016-10-18 一种抗氢致开裂压力容器钢板及其制造方法

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Cited By (13)

* Cited by examiner, † Cited by third party
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CN109825661A (zh) * 2019-01-17 2019-05-31 河北敬业中厚板有限公司 一种大压下量轧制生产压力容器钢板的工艺
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CN109825661A (zh) * 2019-01-17 2019-05-31 河北敬业中厚板有限公司 一种大压下量轧制生产压力容器钢板的工艺
CN112481546A (zh) * 2020-11-26 2021-03-12 南阳汉冶特钢有限公司 一种特厚塑料模具用钢板p20的生产方法
CN113088633A (zh) * 2021-02-26 2021-07-09 舞阳钢铁有限责任公司 一种Cr-Mo钢钢板的生产方法
CN113088632A (zh) * 2021-02-26 2021-07-09 舞阳钢铁有限责任公司 一种SA387Gr11CL2钢板的生产方法
CN113699443A (zh) * 2021-08-02 2021-11-26 山东钢铁集团日照有限公司 一种调质型x70级别管桩用管线钢及其制备方法
CN113862446A (zh) * 2021-09-16 2021-12-31 湖南华菱湘潭钢铁有限公司 一种高加热温度的x70管线钢的生产方法
CN115852242A (zh) * 2021-09-24 2023-03-28 宝山钢铁股份有限公司 一种高温高压耐氢腐蚀厚钢板及其制造方法
CN113957350A (zh) * 2021-10-26 2022-01-21 江苏沙钢集团有限公司 一种2000MPa级热成形钢及其生产方法
CN114318159A (zh) * 2021-12-02 2022-04-12 首钢集团有限公司 一种抗氢致开裂性能的345MPa级容器钢板及其制备方法
CN114410894A (zh) * 2021-12-28 2022-04-29 舞阳钢铁有限责任公司 一种减少12Cr2Mo1VR钢淬火裂纹的方法
CN115354219A (zh) * 2022-07-06 2022-11-18 江阴兴澄特种钢铁有限公司 一种200～400℃高温强度优异的SA516Gr70钢板及其制造方法
CN115094331A (zh) * 2022-07-18 2022-09-23 柳州钢铁股份有限公司 一种低成本的q690钢板及其生产方法
CN115198074A (zh) * 2022-07-30 2022-10-18 日钢营口中板有限公司 一种提升低合金钢板探伤挽救合格率的热处理方法

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