WO2017219553A1 - 一种 200mm 厚抗氢致开裂压力容器钢板及其制造方法 - Google Patents

一种 200mm 厚抗氢致开裂压力容器钢板及其制造方法 Download PDF

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WO2017219553A1
WO2017219553A1 PCT/CN2016/102636 CN2016102636W WO2017219553A1 WO 2017219553 A1 WO2017219553 A1 WO 2017219553A1 CN 2016102636 W CN2016102636 W CN 2016102636W WO 2017219553 A1 WO2017219553 A1 WO 2017219553A1
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temperature
steel plate
steel
hydrogen
ingot
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PCT/CN2016/102636
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English (en)
French (fr)
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李经涛
刘海宽
高助忠
张建
恽鹏程
张军
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江阴兴澄特种钢铁有限公司
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Publication of WO2017219553A1 publication Critical patent/WO2017219553A1/zh

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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
    • 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
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • 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
    • C22C38/02—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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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 present invention belongs to the field of steel sheet manufacturing, and particularly relates to a SA516Gr70 (HIC) anti-hydrogen induced splitting pressure vessel steel sheet having a thickness of 200 mm and a method for producing the same.
  • SA516Gr70 HIC
  • SA516Gr70 (HIC) steel plate is the main metal material used in the environment of wet hydrogen sulfide (containing acid phase or dissolved in liquid phase water, whether or not there is hydrogen in an acidic process environment).
  • Hydrogen induced splitting (HIC) is one of the main forms of equipment damage caused by the wet hydrogen sulfide environment. Once the pressure vessel fails, it will cause huge economic losses. It is also one of the most prominent corrosion problems and technical problems in current oil production, refining, chemical and gas production, which seriously plagues the safe operation of petrochemical production equipment.
  • the publication number CN102605242A relates to "a hydrogen-induced splitting pressure vessel steel and a manufacturing method thereof", and provides an anti-hydrogen
  • the crucible pressure vessel steel plate is obtained by Ni, Mo alloying and subsequent normalizing + water accelerated cooling + tempering heat treatment to obtain a bainite structure, which can improve the strength of the steel plate and replace the low-strength level anti-hydrogen induced cracking steel plate, but
  • the maximum thickness of the steel plate is only 130mm, which still cannot meet the needs of large-scale engineering equipment of petrochemical projects.
  • the water-resistant cavitation pressure vessel steel plate with a thickness of 200 mm or more is still dependent on imports.
  • the present application proposes a hydrogen-induced splitting pressure vessel steel and a manufacturing method thereof, the steel plate has a thickness of 200 mm, and has good comprehensive mechanical properties and excellent after simulated post-weld heat treatment between high temperature and long turns. It is resistant to hydrogen induced cracking and is suitable for use in wet hydrogen sulfide environment.
  • the design and production process of the steel plate is simple and suitable for mass production. technical problem
  • the technical problem to be solved by the present invention is to provide a 200 mm thick anti-hydrogen induced splitting SA516Gr70 (HIC) pressure vessel steel plate for the above-mentioned prior art, which can be applied to the production of a petrochemical plant used in a wet H 2 S corrosive environment. , with well-matched comprehensive mechanical properties and excellent resistance to hydrogen induced splitting. After simulated post-weld heat treatment between high temperature and long turns, the strength and low temperature impact toughness of the steel plate are not significantly weakened, which can meet the needs of large-scale petrochemical engineering projects at home and abroad. .
  • HIC anti-hydrogen induced splitting
  • a 200 mm thick hydrogen-induced splitting pressure vessel steel plate the chemical composition of the steel plate is C: 0.15-0.20% by weight, Si: 0.20 ⁇ 0.40 % , Mn: 1.05 ⁇ 1.20 ⁇ 3 ⁇ 4, P: ⁇ 0.006%, S: ⁇ 0.001%, Cr: 0.15 ⁇ 0.25 ⁇ 3 ⁇ 4, Ni: 0.15 to 0.35 ⁇ 3 ⁇ 4, Nb: ⁇ 0.01%, V: ⁇ 0.01%, Ti: ⁇ 0.01%, B: ⁇ 0.0005%, the balance is Fe and inevitable impurity elements.
  • the hydrogen-induced splitting pressure vessel steel sheet of the present invention is subjected to an anti-hydrogen induced splitting test according to the A solution in the NACE TM0284-2011 "Experimental Method for Performance Evaluation of Hydrogen-induced Splitting Steel in Pipeline Pressure Vessels", with a single inspection cross section.
  • the crack length ratio (CLR), crack width ratio (CTR) and crack sensitivity (CSR) are both zero, no hydrogen bubbling, ie no defects after corrosion.
  • 635 ⁇ 14°Cx24h simulated post-weld heat treatment test mechanical properties can meet the yield strength ⁇ 320Mp a , tensile strength ⁇ 520Mp a , heart -29°C transverse Charpy impact power value ⁇ 150J, Z-direction tensile section
  • the shrinkage rate is ⁇ 35%, and the Brinell hardness of the steel plate surface is ⁇ 200HB.
  • the main chemical composition of the steel sheet of the invention is designed by using C, Si, Mn, Ni, Cr alloying composition components, and the content of S and P is minimized, and alloying elements such as Cu, Mo, Nb, V, Ti, B are not intentionally added. .
  • c can significantly increase the strength and hardness of the steel sheet, but as the carbon content increases, carbide segregation is likely to occur, resulting in a difference in hardness between the segregation zone and the surrounding tissue, resulting in HIC corrosion.
  • Mn improves the strength of steel by solid solution strengthening. However, when Mn is added to 1.05% or more, the cleavage sensitivity can be improved. However, accelerated cooling and tempering treatment by normalizing + water can eliminate the adverse effects.
  • Si is mainly used as a reducing agent and a deoxidizer for steelmaking crucibles.
  • composition control range of the present application is C: 0.15 ⁇ 0.20%, Si: 0.20-0.40%, Mn: 1.05 ⁇ 1.20 ⁇ 3 ⁇ 4, and its adverse effect is eliminated by subsequent heat treatment.
  • Cr is a hardenability improving element, which can significantly increase the strength of steel, but excessively high content will increase the brittle transition temperature.
  • the Cr content control range of the present application is 0.15-0.25%; Ni mainly plays a solid solution strengthening effect in steel. The same can improve the toughness.
  • the Ni content control range of this application is 0.15-0.35%; P and S are harmful elements, and the amount of hydrogen in the H 2 S immersed in the steel increases as the S content in the steel increases. Thus, the sensitivity to HIC is also increased.
  • Another object of the present invention is to provide a method for manufacturing the above-mentioned hydrogen-induced splitting pressure vessel steel sheet, which is specifically as follows: 45 tons of die-cast flat ingot production, the process route: electric furnace ⁇ LF refining ⁇ VD refining ⁇ molding ⁇ Steel ingot slow cooling ⁇ steel ingot heating ⁇ steel ingot rolling ⁇ steel plate slow cooling ⁇ flaw detection ⁇ normalizing + water accelerated cooling ⁇ tempering ⁇ finishing ⁇ inspection ⁇ storage.
  • the smelting raw materials are selected from self-produced scrap steel and high-quality pig iron. After the electric furnace smelting and LF refining processes are finished, the smelting treatment is carried out, and the strict control is 8 ⁇ 0.001 ⁇ 3 ⁇ 4, P ⁇ 0.006%, Class A, Class B, Class C, Class D and Ds non-metallic inclusions are single item ⁇ 1.0, the sum of which is ⁇ 3.5; with low superheat argon protection casting, the superheat of pouring bismuth steel is controlled at 25 ⁇ 35 °C. After the steel ingot is demoulded, it is slowly cooled into the pit for more than 48 hours, ensuring the full diffusion of hydrogen in the steel.
  • the steel ingot is heated by a soaking furnace, the total heating time is ⁇ 30h, the preheating section temperature is 600 ⁇ 650°C, the heat preservation time is 2-4h; then the temperature is raised to the first heat preservation at a speed of not more than 80°C/h.
  • the temperature of the first holding section is 800 ⁇ 850 °C, and after 4-6 hours of heat preservation, the temperature is raised to the second holding section (soaking section) at a speed of not more than 80 °C/h; 1260 ⁇ 1280°C, the insulation time is 14-16h.
  • the rolling temperature is 1150-1200 ° C
  • the single pass reduction of at least 2 passes in the vertical pass is ⁇ 501 ⁇
  • the single pass reduction rate is ⁇ 6%
  • the finish rolling temperature is controlled at 900 ⁇ 950 °C.
  • the normalizing heating temperature is 890 ⁇ 910 ° C
  • the thermal insulation interturn coefficient 2.0 ⁇ 2.5min/mm
  • water cooling cooling the surface of the steel plate to 500-600 ° C
  • the tempering temperature of the steel plate of the present invention is not lower than the temperature after the simulated post-weld heat treatment, tempering: tempering temperature 640 to 660 ° C, the inter-turn coefficient of the thermal insulation: 3.5 to 4.5 min /mm.
  • the present invention relates to a SA516Gr70 (HIC) anti-hydrogen induced splitting pressure vessel steel plate having a thickness of 200 mm, the steel plate has well-matched comprehensive mechanical properties and excellent hydrogen-induced splitting performance, and is simulated between high temperature and long turns. After the post-weld heat treatment, the strength and low-temperature impact toughness of the steel sheet did not significantly decrease.
  • the steel plate is subjected to the hydrogen-induced cleaving test according to the solution A of NACE TM0284-2011 "Experimental method for evaluating the performance of anti-hydrogen induced cracking steel in pipeline pressure vessels", the crack length ratio (CLR) and the crack width ratio (CTR) of a single inspection section.
  • CLR crack length ratio
  • CTR crack width ratio
  • CSR crack sensitivity rate
  • the present invention uses steel ingot production to reduce the hydrogen induced splitting sensitivity by means of improving the purity of the molten steel and the internal quality of the steel sheet.
  • the steel plate is designed by combining alloy composition of Si, Mn, Ni and Cr, and the content of 8 and P is reduced as much as possible. It is intended to add alloying elements such as Cu, Mo, Nb, V, Ti and B. By reducing the content of 8, P, H, 0 and N elements, the purity of molten steel is improved, and the sensitivity of the steel plate to hydrogen splitting is reduced.
  • the steel ingot is heated by the soaking furnace, and the segregation can be fully diffused by prolonging the soaking section of the soaking section.
  • the loose defects can be effectively pressed and the inner part of the steel plate can be effectively improved. quality.
  • the heat treatment process of the steel plate of the invention adopts normalizing + water accelerated cooling + tempering process, can reduce the phase transition temperature, refine the crystal grains, reduce the band structure, and inhibit the growth and coarsening of the alloying element carbonitride, so that It is dispersed at a low temperature to increase the strength and keep the toughness of the steel sheet from decreasing significantly.
  • the hydrogen-induced splitting pressure vessel steel sheet of the present embodiment has a thickness of 200 mm, and its chemical composition is in terms of weight percent: C: 0.18%, Si: 0.30%, Mn: 1.17%, P: 0.003%, S : 0.0005% , H: 0.00006% , 0: 0.0012% , N: 0.0040% , Cr: 0.20% , Ni : 0.25% , Nb : 0.00 5% , V: 0.003% , Ti : ⁇ 0.002% , B : ⁇ 0.0001 %, the balance is Fe and inevitable impurity elements.
  • the smelting raw materials are selected from self-produced scrap steel and high-quality pig iron, and are subjected to smelting treatment after electric furnace smelting and LF smelting, strictly controlling S ⁇ 0.001 ⁇ 3 ⁇ 4, P ⁇ 0.006%, Class A, Class B, Class C, Class D and Ds non-metallic inclusions single item ⁇ 1.0, the sum of which is ⁇ 3.5; with low superheat argon protection casting, molten steel pouring ⁇ superheat is 32 ° C
  • the steel ingot is heated by a soaking furnace, the temperature of the preheating section is 620 ° C, and the heat preservation time is 3 h; the temperature of the first heat preservation section is 8 20 ° C, the heat preservation time is 5 h, and the heating rate is 60 ° C / h; The hot section temperature is 1270 ° C, the insulation time is 16 h, the heating rate is 60 ° C / h; the total heating time is 35 h.
  • the rolling temperature is 1180 ° C, and the single pass of the rolling pass 2 passes
  • the reduction is ⁇ 50mm, the reduction is 55mm, 55mm respectively; the single pass reduction is 6.2%, the finish rolling temperature is 920°C, and the steel plate is slowly cooled more than 72 ⁇ after the steel wire is off the line, fully expanding hydrogen .
  • the normalizing heating temperature is 900 ° C, the thermal insulation interturn coefficient: 2.2 min / mm, water cooling, cooling the surface of the steel plate to 500-600 ° C; After the post-weld heat treatment, the strength of the steel plate is greatly reduced.
  • the tempering temperature of the steel plate of the present invention is not lower than the temperature after the simulated post-weld heat treatment, tempering: tempering temperature 650 ° C, thermal insulation day coefficient: 4.0 min / mm.
  • the 200 mm thick anti-hydrogen induced splitting pressure vessel steel plate produced by the above manufacturing process has well-matched comprehensive mechanical properties and excellent hydrogen-induced splitting performance, and its mechanical properties are shown in Table 1, which is resistant to hydrogen.
  • the cracking performance is shown in Table 4.
  • the hydrogen-induced splitting pressure vessel steel sheet of the present embodiment has a thickness of 200 mm, and its chemical composition is in terms of weight percent: C: 0.18%, Si: 0.28%, Mn: 1.18%, P: 0.004%, S : 0.0006%, H: 0.00006%, 0: 0.0013%, N: 0.0042%, Cr: 0.21%, Ni: 0.28%, Nb: ⁇ 0.0 06%, V: ⁇ 0.004%, Ti: ⁇ 0.003%, B: ⁇ 0.0001%, the balance is Fe and inevitable impurity elements.
  • the manufacturing process of the steel sheet is:
  • the smelting raw materials are selected from self-produced scrap steel and high-quality pig iron, and are subjected to smelting treatment after electric furnace smelting and LF smelting, strictly controlling S ⁇ 0.001 ⁇ 3 ⁇ 4, P ⁇ 0.006%, Class A, Class B, Class C, Class D and Ds non-metallic inclusions are single item ⁇ 1.0, the sum of which is ⁇ 3.5; with low superheat argon protection casting, molten steel pouring ⁇ superheat is 30 °C. After the steel ingot is demolded, it is slowly cooled into the pit for more than 48 hours to ensure that the hydrogen in the steel is fully diffused.
  • the steel ingot is heated by a soaking furnace, the temperature of the preheating section is 630 ° C, and the heat preservation time is 4 h; the temperature of the first heat preservation section is 8 30 ° C, the heat preservation time is 6 h, and the heating rate is 70 ° C / h; The hot section temperature is 1260 ° C, the heat preservation time is 15 h, the heating rate is 80 ° C / h; the total heating time is 33 h.
  • the rolling temperature is 1170 °C
  • the single pass reduction of the two passes of the vertical rolling pass is ⁇ 50mm
  • the reduction is 52mm, 55mm respectively
  • single pass pressure The minimum rate is 6.1%
  • the finishing temperature is 910 °C.
  • the normalizing heating temperature is 900 ° C, the thermal insulation interturn coefficient: 2.3 min / mm, water cooling, the steel plate surface is cooled to 500-600 ° C; After the post-weld heat treatment, the strength of the steel plate is greatly reduced.
  • the tempering temperature of the steel plate of the present invention is not lower than the temperature after the simulated post-weld heat treatment, tempering: tempering temperature is 645 ° C, and the coefficient of thermal insulation is 4.2 min/mm.
  • the 200 mm thick anti-hydrogen induced splitting pressure vessel steel plate obtained through the above manufacturing process has well-matched comprehensive mechanical properties and excellent hydrogen-induced splitting performance, and its mechanical properties are shown in Table 2, which is resistant to hydrogen.
  • the cracking performance is shown in Table 4.
  • the hydrogen-induced splitting pressure vessel steel sheet of the present embodiment has a thickness of 200 mm, and its chemical composition is in terms of weight percent: C: 0.18%, Si: 0.26%, Mn: 1.16%, P: 0.005%, S : 0.0007% , H: 0.00005% , 0: 0.0010% , N: 0.0038% , Cr: 0.22% , Ni : 30% , Nb : ⁇ 0.006 % , V: ⁇ 0.004% , Ti : ⁇ 0.002% , B: ⁇ 0.0003%, the balance is Fe and inevitable impurity elements.
  • the smelting raw materials are selected from self-produced scrap steel and high-quality pig iron, and are subjected to smelting treatment after electric furnace smelting and LF smelting, strictly controlling S ⁇ 0.001 ⁇ 3 ⁇ 4, P ⁇ 0.006%, Class A, Class B, Class C, Class D and Ds non-metallic inclusions single item ⁇ 1.0, the sum of which is ⁇ 3.5; with low superheat argon protection casting, molten steel pouring ⁇ superheat is 30 ° C
  • the steel ingot is heated by a soaking furnace, the preheating section temperature is 620 ° C, and the heat preservation time is 2.5 h; the first heat preservation section temperature is 840 ° C, the heat preservation time is 5 h, and the heating rate is 60 ° C / h; The hot section temperature is 1260 ° C, the insulation time is 16 h, the heating rate is 80 ° C / h; the total heating time is 32.5 h.
  • the rolling temperature is 1175 ° C
  • the single pass reduction of the two passes of the vertical rolling pass is ⁇ 50 mm
  • the reduction is 55 mm, 58 mm
  • the pass reduction rate is 6.2% at the minimum
  • the finish rolling temperature is 925 °C.
  • the normalizing heating temperature is 910 ° C, the thermal insulation interturn coefficient: 2.2 min / mm, water cooling, the steel plate surface is cooled to 500-600 ° C; After the post-weld heat treatment, the strength of the steel plate is greatly reduced.
  • the tempering temperature of the steel plate of the present invention is not lower than the temperature after the simulated post-weld heat treatment, tempering: tempering temperature is 655 ° C, and the thermal insulation day coefficient is 3.8 min/mm.
  • the 200 mm thick anti-hydrogen splitting pressure vessel steel plate obtained through the above manufacturing process has well-matched comprehensive mechanical properties and excellent hydrogen-induced splitting performance, and its mechanical properties are shown in Table 3, which is resistant to hydrogen.
  • the cracking performance is shown in Table 4.

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Abstract

一种200mm厚抗氢致开裂压力容器钢板，该钢板的化学成分按重量百分比计为C0.15～0.20％，Si0.20～0.40％，Mn1.05～1.20％，P≤0.006％，S≤0.001％，Cr0.15～0.25％，Ni0.15～0.35％，Nb≤0.01％，V≤0.01％，Ti≤0.01％，B≤0.0005％，余量为Fe及不可避免的杂质元素。采用模铸扁锭生产路线：电炉→LF精炼→VD精炼→模铸→钢锭缓冷→钢锭加热→钢锭轧制→钢板缓冷→探伤→正火+水加速冷却→回火→精整→检验→入库。钢板具有匹配良好的力学性能和优异的抗氢致开裂性能，在高温长时间模拟焊后热处理后，钢板的强度和低温冲击韧性不明显减弱。

Description

一种 200mm厚抗氢致幵裂压力容器钢板及其制造方法 技术领域
[0001] 本发明属于钢板制造领域， 具体涉及一种厚度为 200mm的 SA516Gr70(HIC)抗 氢致幵裂压力容器钢板及其制造方法。
背景技术
[0002] SA516Gr70(HIC)钢板是石化行业湿硫化氢 （含有气相或溶解在液相水中， 不论 是否有氢气存在的酸性工艺环境） 环境使用的主要金属材料。 氢致幵裂 (HIC)是 湿硫化氢环境造成设备破坏的主要形式之一。 压力容器一旦失效， 将造成巨大 的经济损失， 也是当前采油、 炼油、 化工、 煤气生产中最为突出的腐蚀问题和 技术难题之一， 严重困扰着石化企业生产装置的安全运行。 随着资源品质劣化 和设备大型化的发展趋势， 湿硫化氢环境用压力容器钢板的需求量逐年增大， 且向大厚度、 大单重、 高性能方向发展， 设计上需要钢板在更高温度和更长吋 间的模拟焊后热处理条件下， 仍然具有良好的内部质量、 力学性能和优异的抗 氢致幵裂 （HIC) 性能。
[0003] 目前， 国内公幵报道的最大厚度抗氢致幵裂钢板为舞阳钢厂生产的 SA516Gr65( HIC)， 最大厚度为 165mm。 涉及湿硫化氢环境使用的抗氢致幵裂压力容器钢的 专利较少， 公告号为 CN102605242A涉及一种"一种抗氢致幵裂压力容器钢及其 制造方法"， 提供了一种抗氢致幵裂压力容器钢板， 通过 Ni、 Mo合金化以及后续 正火 +水加速冷却 +回火热处理得到贝氏体组织， 达到提高钢板强度， 替代低强 度级别抗氢致幵裂钢板的目的， 但钢板最大厚度只有 130mm， 仍然不能满足石 化项目工程设备大型化的需求。 目前 200mm及以上厚度抗氢致幵裂压力容器钢 板仍然依赖进口。
[0004] 基于以上原因， 本申请提出了一种抗氢致幵裂压力容器钢及其制造方法， 钢板 厚度为 200mm， 在高温长吋间模拟焊后热处理后仍然具有良好的综合机械性能 和优异的抗氢致幵裂性能， 适用于在湿硫化氢环境使用， 该钢板成分设计和生 产工艺简单， 适合批量生产。 技术问题
[0005] 本发明所要解决的技术问题是针对上述现有技术提供一种 200mm厚抗氢致幵裂 SA516Gr70(HIC)压力容器钢板， 能够应用于湿 H 2S腐蚀环境使用的石油化工装 置的制作， 具有匹配良好的综合机械性能和优异的抗氢致幵裂性能， 在高温长 吋间模拟焊后热处理后， 钢板的强度和低温冲击韧性不明显减弱， 可以满足国 内外大型石化工程项目的需要。
问题的解决方案
技术解决方案
[0006] 本发明解决上述问题所采用的技术方案为： 一种 200mm厚抗氢致幵裂压力容器 钢板， 该钢板的化学成分按重量百分比计为 C: 0.15—0.20% , Si: 0.20〜0.40% ， Mn: 1.05〜1.20<¾， P: <0.006% , S: <0.001% , Cr: 0.15〜0.25<¾， Ni: 0.15 〜0.35<¾， Nb: <0.01% , V： <0.01% , Ti: <0.01% , B: <0.0005% , 余量为 Fe 及不可避免的杂质元素。
[0007] 本发明抗氢致幵裂压力容器钢板按照 NACE TM0284-2011 《管道压力容器抗氢 致幵裂钢性能评价的实验方法》 中的 A溶液进行抗氢致幵裂检验， 单个检验截面 的裂纹长度率 （CLR) 、 裂纹宽度率 （CTR) 和裂纹敏感率 （CSR) 均为 0， 无 氢鼓泡， 即腐蚀后无缺陷。 635±14°Cx24h模拟焊后热处理后检验力学性能， 可 以满足屈服强度≥320Mpa， 抗拉强度≥520Mpa， 心部 -29°C横向夏比冲击功单值≥ 150J, Z向拉伸断面收缩率≥35%， 钢板表面布氏硬度≤200HB。
[0008] 本发明 200mm抗氢致幵裂压力容器钢板的化学成分是这样确定的：
[0009] 本发明钢板的主要化学成分采用 C、 Si、 Mn、 Ni、 Cr合金化组合成分设计， 尽 量降低 S、 P含量， 不有意添加 Cu、 Mo、 Nb、 V、 Ti、 B等合金元素。
[0010] c能够显著提高钢板的强度和硬度， 但随着碳含量的增加容易出现碳化物偏析 ， 造成偏析区硬度与周围组织出现差异， 导致 HIC腐蚀。 Mn通过固溶强化提高 钢的强度， 但 Mn添加到 1.05%以上吋， 可提高幵裂敏感性， 然而通过正火 +水加 速冷却、 回火处理可消除其不良影响。 Si主要作为炼钢吋的还原剂和脱氧剂使用 ， 有一定的固溶强化作用， 同吋 Si元素易偏析于晶粒边界， 助长晶间裂纹的产生 ； 虽然随着。、 Mn、 Si含量增加， 会提高 HIC的敏感性， 但作为主要强化元素， 其含量仍然要在允许范围内尽量按上限控制。 本申请成分控制范围： C: 0.15〜0 .20% , Si: 0.20—0.40% , Mn: 1.05〜1.20<¾， 其不利影响通过后续热处理进行 消除。
[0011] Cr是提高淬透性元素， 可以显著提高钢的强度， 但含量过高会提高脆性转变温 度， 本申请 Cr含量控制范围为 0.15-0.25%; Ni在钢中主要起固溶强化作用， 同吋 可以提高韧性， 本申请 Ni含量控制范围为 0.15-0.35%; P、 S是有害元素， 随钢中 S含量升高， 在 H 2S中浸泡吋进入钢中的氢量也升高， 从而产生 HIC的敏感性也 升高。 当 P含量很低吋， 裂纹能在 MnS上形核， 但尺寸很小， 不能被测出， 但如 P高 （如 P=0.4%) ， 则即使 S很低 （S=0.001%) ， 裂纹也能在氧化物夹杂以及晶 界上形核并扩展。 因此， 本申请应尽可能降低钢中 S、 P含量。
[0012] 本发明另一目的是提供上述抗氢致幵裂压力容器钢板的制造方法， 具体如下： 采用 45吨模铸扁锭生产， 其工艺路线： 电炉→LF精炼→VD精炼→模铸→钢锭缓 冷→钢锭加热→钢锭轧制→钢板缓冷→探伤→正火 +水加速冷却→回火→精整→ 检验→入库。
[0013] 1) 冶炼工艺
[0014] 冶炼原料选用自产废钢和优质生铁， 电炉冶炼和 LF精炼炼工序结束后均进行扒 澄处理， 严格控制8≤0.001<¾， P<0.006% , A类、 B类、 C类、 D类和 Ds非金属夹 杂物类单项≤1.0级， 其总和≤3.5级； 采用低过热度氩气保护浇注， 浇注吋钢水过 热度控制在 25〜35°C。 钢锭脱模后入坑缓冷 48小吋以上， 确保钢中的氢充分扩散
[0015] 2) 加热、 轧制工艺
[0016] 钢锭采用均热炉加热， 总加热吋间≥30h， 预热段温度为 600〜650°C， 保温吋间 2-4h; 然后以不大于 80°C/h速度升温至第一保温段， 第一保温段温度为 800〜850 °C， 保温吋间 4-6h后， 再以不大于 80°C/h速度升温至第二保温段 （均热段） ； 第 二保温段温度为 1260〜1280°C， 保温吋间为 14-16h。
[0017] 采用"高温大压下"轧制工艺， 幵轧温度为 1150-1200°C， 为了变形充分渗透到钢 锭心部， 纵轧道次至少有 2个道次的单道次压下量≥501^^ 为了防止混晶， 单道 次压下率≥6%， 终轧温度控制在 900〜950°C， 钢板下线后堆垛缓冷 72小吋以上， 充分扩氢。
[0018] 3) 热处理工艺
[0019] 采用正火 +水加速冷却 +回火工艺， 正火加热温度为 890〜910°C， 保温吋间系数 ： 2.0〜2.5min/mm， 水冷， 使钢板表面冷却至 500-600°C; 为了防止模拟焊后热 处理后钢板强度大幅度下降， 本发明钢板回火温度不低于模拟焊后热处理温度 ， 回火： 回火温度 640〜660°C， 保温吋间系数： 3.5〜4.5min/mm。
[0020] 正火 +水加速冷却， 是将钢板加热到 Ac3以上 30-50°C进行奥氏体化， 并保温一 定吋间后通过层流水快速冷却， 使钢板表面冷却至 500-600°C， 然后在静止空气 中冷却的工艺过程。 该工艺可以降低相变温度， 细化晶粒， 减少带状组织， 抑 制合金元素碳氮化物长大粗化， 使其低温弥散析出， 从而提高强度并且保持钢 板韧性不明显下降。
发明的有益效果
有益效果
[0021] 与现有技术相比， 本发明的优点在于：
[0022] 本发明涉及一种 SA516Gr70(HIC)抗氢致幵裂压力容器钢板， 厚度为 200mm， 该钢板具有匹配良好的综合机械性能和优异的抗氢致幵裂性能， 在高温长吋间 模拟焊后热处理后， 钢板的强度和低温冲击韧性不明显减弱。 钢板按照 NACE TM0284-2011 《管道压力容器抗氢致幵裂钢性能评价的实验方法》 中的 A溶液进 行抗氢致幵裂检验， 单个检验截面的裂纹长度率 （CLR) 、 裂纹宽度率 （CTR) 和裂纹敏感率 （CSR) 均为 0， 无氢鼓泡， 即腐蚀后无缺陷。 635±14°Cx24h模拟 焊后热处理后检验力学性能， 可以满足屈服强度≥320Mpa， 抗拉强度≥520Mpa， 心部 -29°C横向夏比冲击功单值≥150J， Z向拉伸断面收缩率≥35%， 钢板表面布氏 硬度≤200HB。
[0023] 为了实现上述目的， 本发明采用钢锭生产， 通过提高钢水纯净度和钢板内部质 量等手段， 降低氢致幵裂敏感性。
[0024] 钢板采用^ Si、 Mn、 Ni、 Cr合金化组合成分设计， 尽量降低8、 P含量， 不有 意添加 Cu、 Mo、 Nb、 V、 Ti、 B等合金元素， 通过降低8、 P、 H、 0、 N元素含 量， 提高钢水的纯净度， 降低钢板氢致幵裂的敏感性。
[0025] 钢锭采用均热炉加热， 通过延长均热段保温吋间可使偏析充分扩散， 通过高温 轧制阶段的高温大压下轧制工艺， 可以有效将疏松缺陷充分压合， 提高钢板内 部质量。
[0026] 本发明钢板的热处理工艺采用正火 +水加速冷却 +回火工艺， 可以降低相变温度 ， 细化晶粒， 减少带状组织， 抑制合金元素碳氮化物长大粗化， 使其低温弥散 析出， 从而提高强度并且保持钢板韧性不明显下降。
实施该发明的最佳实施例
本发明的最佳实施方式
[0027] 以下结合实施例对本发明作进一步详细描述。
[0028] 实施例 1
[0029] 本实施例的抗氢致幵裂压力容器钢板的厚度为 200mm， 其化学成分按重量百分 比计为: C: 0.18% , Si: 0.30% , Mn: 1.17% , P: 0.003% , S: 0.0005% , H: 0.00006% , 0： 0.0012% , N: 0.0040% , Cr: 0.20% , Ni: 0.25% , Nb: 0.00 5% , V： 0.003%, Ti: <0.002%, B: <0.0001% , 余量为 Fe及不可避免的杂质元 素。
[0030] 该钢板的制造工艺为如下：
[0031] 1) 冶炼工艺
[0032] 冶炼原料选用自产废钢和优质生铁， 电炉冶炼和 LF冶炼后均进行扒澄处理， 严 格控制 S≤0.001<¾， P<0.006% , A类、 B类、 C类、 D类和 Ds非金属夹杂物类单项 ≤1.0级， 其总和≤3.5级； 采用低过热度氩气保护浇注， 钢水浇注吋过热度为 32°C
。 钢锭脱模后入坑缓冷 48小吋以上， 确保钢中的氢充分扩散。
[0033] 2) 加热、 轧制工艺
[0034] 钢锭采用均热炉加热， 预热段温度为 620°C， 保温吋间 3h; 第一保温段温度为 8 20°C, 保温吋间 5h， 升温速度为 60°C/h; 均热段温度为 1270°C， 保温吋间为 16h ， 升温速度为 60°C/h; 总加热吋间为 35h。
[0035] 采用"高温大压下"轧制工艺， 幵轧温度为 1180°C， 纵轧道次 2个道次的单道次 压下量≥50mm， 压下量分别为 55mm、 55mm; 单道次压下率最小为 6.2%， 终轧 温度为 920°C， 钢板下线后堆垛缓冷 72小吋以上， 充分扩氢。
[0036] 3) 热处理工艺
[0037] 采用正火 +水加速冷却 +回火工艺， 正火加热温度为 900°C， 保温吋间系数： 2.2 min/mm, 水冷， 使钢板表面冷却至 500-600°C; 为了防止模拟焊后热处理后钢板 强度大幅度下降， 本发明钢板回火温度不低于模拟焊后热处理温度， 回火： 回 火温度 650°C， 保温吋间系数： 4.0min/mm。
[0038] 经由上述制造工艺制得的 200mm厚的抗氢致幵裂压力容器钢板具有匹配良好的 综合机械性能和优异的抗氢致幵裂性能， 其机械性能详见表 1， 抗氢致幵裂性能 见表 4。
本发明的实施方式
[0039] 实施例 2
[0040] 本实施例的抗氢致幵裂压力容器钢板的厚度为 200mm， 其化学成分按重量百分 比计为: C: 0.18% , Si: 0.28% , Mn: 1.18% , P: 0.004% , S: 0.0006% , H: 0.00006% , 0： 0.0013% , N: 0.0042% , Cr: 0.21% , Ni: 0.28% , Nb: <0.0 06% , V： <0.004% , Ti: <0.003% , B: <0.0001% , 余量为 Fe及不可避免的杂 质元素。
[0041] 该钢板的制造工艺为：
[0042] 1) 冶炼工艺
[0043] 冶炼原料选用自产废钢和优质生铁， 电炉冶炼和 LF冶炼后均进行扒澄处理， 严 格控制 S≤0.001<¾， P<0.006% , A类、 B类、 C类、 D类和 Ds非金属夹杂物类单项 ≤1.0级， 其总和≤3.5级； 采用低过热度氩气保护浇注， 钢水浇注吋过热度为 30°C 。 钢锭脱模后入坑缓冷 48小吋以上， 确保钢中的氢充分扩散。
[0044] 2) 加热、 轧制工艺
[0045] 钢锭采用均热炉加热， 预热段温度为 630°C， 保温吋间 4h; 第一保温段温度为 8 30°C, 保温吋间 6h， 升温速度为 70°C/h; 均热段温度为 1260°C， 保温吋间为 15h ， 升温速度为 80°C/h; 总加热吋间为 33h。 采用"高温大压下"轧制工艺， 幵轧温度为 1170°C， 纵轧道次 2个道次的单道次 压下量≥50mm， 压下量分别为 52mm、 55mm; 单道次压下率最小为 6.1%， 终轧 温度为 910°C， 钢板下线后堆垛缓冷 72小吋以上， 充分扩氢。
[0047] 3) 热处理工艺
[0048] 采用正火 +水加速冷却 +回火工艺， 正火加热温度为 900°C， 保温吋间系数： 2.3 min/mm, 水冷， 使钢板表面冷却至 500-600°C; 为了防止模拟焊后热处理后钢板 强度大幅度下降， 本发明钢板回火温度不低于模拟焊后热处理温度， 回火： 回 火温度 645°C， 保温吋间系数： 4.2min/mm。
[0049] 经由上述制造工艺制得的 200mm厚的抗氢致幵裂压力容器钢板具有匹配良好的 综合机械性能和优异的抗氢致幵裂性能， 其机械性能详见表 2， 抗氢致幵裂性能 见表 4。
[0050]
[0051] 实施例 3
[0052] 本实施例的抗氢致幵裂压力容器钢板的厚度为 200mm， 其化学成分按重量百分 比计为: C: 0.18% , Si: 0.26% , Mn: 1.16% , P: 0.005% , S: 0.0007% , H: 0.00005% , 0： 0.0010% , N: 0.0038% , Cr: 0.22% , Ni: 30% , Nb: <0.006 % , V： <0.004% , Ti: <0.002% , B: <0.0003% , 余量为 Fe及不可避免的杂质 元素。
[0053] 该钢板的制造工艺为如下：
[0054] 1) 冶炼工艺
[0055] 冶炼原料选用自产废钢和优质生铁， 电炉冶炼和 LF冶炼后均进行扒澄处理， 严 格控制 S≤0.001<¾， P<0.006% , A类、 B类、 C类、 D类和 Ds非金属夹杂物类单项 ≤1.0级， 其总和≤3.5级； 采用低过热度氩气保护浇注， 钢水浇注吋过热度为 30°C
。 钢锭脱模后入坑缓冷 48小吋以上， 确保钢中的氢充分扩散。
[0056] 2) 加热、 轧制工艺
[0057] 钢锭采用均热炉加热， 预热段温度为 620°C， 保温吋间 2.5h; 第一保温段温度为 840°C， 保温吋间 5h， 升温速度为 60°C/h; 均热段温度为 1260°C， 保温吋间为 16h ， 升温速度为 80°C/h; 总加热吋间为 32.5h。 [0058] 采用"高温大压下"轧制工艺， 幵轧温度为 1175°C， 纵轧道次 2个道次的单道次 压下量≥50mm， 压下量分别为 55mm、 58mm; 单道次压下率最小为 6.2%， 终轧 温度为 925°C， 钢板下线后堆垛缓冷 72小吋以上， 充分扩氢。
[0059] 3) 热处理工艺
[0060] 采用正火 +水加速冷却 +回火工艺， 正火加热温度为 910°C， 保温吋间系数： 2.2 min/mm, 水冷， 使钢板表面冷却至 500-600°C; 为了防止模拟焊后热处理后钢板 强度大幅度下降， 本发明钢板回火温度不低于模拟焊后热处理温度， 回火： 回 火温度 655°C， 保温吋间系数： 3.8min/mm。
工业实用性
[0061] 经由上述制造工艺制得的 200mm厚的抗氢致幵裂压力容器钢板具有匹配良好的 综合机械性能和优异的抗氢致幵裂性能， 其机械性能详见表 3， 抗氢致幵裂性能 见表 4。
[0062] 表 1实施例 1所生产的钢板的机械性能
[]
Figure imgf000010_0001
[0063] 注： 模拟焊后热处理： 635±14°Cx24h。 模拟 （正火 +水加速冷却） +模拟回火工 艺制度与钢板热处理工艺参数相同。
[0064] 表 2实施例 2所生产的钢板的机械性能
Figure imgf000011_0001
[0065] 注： 模拟焊后热处理： 635±14°Cx24h。 模拟 （正火 +水加速冷却） +模拟回火工 艺制度与钢板热处理工艺参数相同。
[0066] 表 3实施例 3所生产的钢板的机械性能
Figure imgf000012_0001
[0067] 注： 模拟焊后热处理： 635±14°Cx24h。 模拟 （正火 +水加速冷却） +模拟回火工 艺制度与钢板热处理工艺参数相同。
[0068] 表 4各实施例所生产的钢板的抗氢致幵裂 （HIC) 性能
Figure imgf000013_0001
[0069]
[0070]
[0071]
序列表自由内容
[0072] 在此处键入序列表自由内容描述段落。

Claims

权利要求书
[权利要求 1] 一种 200mm厚抗氢致幵裂压力容器钢板， 其特征在于： 该钢板的化学 成分按重量百分比计为 C: 0.15—0.20% , Si: 0.20—0.40%, Mn: 1.0 5〜1.20<¾， P: <0.006% , S: <0.001%, Cr: 0.15〜0.25<¾， Ni: 0.15 〜0.35<¾， Nb: <0.01% , V： <0.01% , Ti: <0.01%, B: <0.0005%, 余量为 Fe及不可避免的杂质元素。
[权利要求 2] —种制造如权利要求 1所述 200mm厚抗氢致幵裂压力容器钢板的方法
， 其特征在于： 工艺步骤如下：
采用模铸扁锭生产， 其工艺路线： 电炉→LF精炼→VD精炼→模铸→ 钢锭缓冷→钢锭加热→钢锭轧制→钢板缓冷→探伤→正火 +水加速冷 却→回火→精整→检验→入库；
主要工序的具体操作如下，
1) 冶炼工艺
电炉冶炼和 LF精炼炼工序结束后均进行扒澄处理， 严格控制8≤0.001 % , P<0.006%, A类、 B类、 C类、 D类和 Ds非金属夹杂物类单项≤1.0 级， 其总和≤3.5级； 采用低过热度氩气保护浇注， 钢锭脱模后入坑缓 冷 48小吋以上， 确保钢中的氢充分扩散；
2) 加热、 轧制工艺
钢锭采用均热炉加热， 总加热吋间≥30h， 预热段温度为 600〜650°C ， 保温吋间 2-4h; 然后以不大于 80°C/h速度升温至第一保温段， 第一 保温段温度为 800〜850°C， 保温吋间 4-6h后， 再以不大于 80°C/h速度 升温至第二保温段即均热段； 第二保温段温度为 1260〜1280°C， 保温 吋间为 14-16h;
采用"高温大压下"轧制工艺， 幵轧温度为 1150-1200°C， 为了变形充 分渗透到钢锭心部， 纵轧道次至少有 2个道次的单道次压下量≥50mm ； 为了防止混晶， 单道次压下率≥6%， 终轧温度控制在 900〜950°C， 钢板下线后堆垛缓冷 72小吋以上， 充分扩氢；
3) 热处理工艺 采用正火 +水加速冷却 +回火工艺， 正火加热温度为 890〜910°C， 保温 吋间系数： 2.0〜2.5min/mm， 水冷， 使钢板表面冷却至 500-600°C; 回火： 回火温度 640〜660°C， 钢板回火温度不低于模拟焊后热处理温 度， 保温吋间系数： 3.5〜4.5min/mm。
[权利要求 10] 在此处键入权利要求项 10。
PCT/CN2016/102636 2016-06-23 2016-10-20 一种 200mm 厚抗氢致开裂压力容器钢板及其制造方法 WO2017219553A1 (zh)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106862280A (zh) * 2016-12-25 2017-06-20 秦皇岛首秦金属材料有限公司 一种中厚板轧机粗轧纵轧道次压下量分配方法
CN108330398A (zh) * 2018-05-22 2018-07-27 湖南华菱湘潭钢铁有限公司 一种特厚抗酸容器钢板的生产方法
CN109487158A (zh) * 2018-12-06 2019-03-19 南阳汉冶特钢有限公司 一种高温压力容器用厚度大于200mm的18MnMoNbR钢板及其生产方法
CN110193574B (zh) * 2019-05-10 2020-10-30 舞阳钢铁有限责任公司 大单重特厚铬钼钢板的生产工艺
CN110923570B (zh) * 2019-11-20 2022-01-18 江阴兴澄特种钢铁有限公司 一种抗应力导向氢致开裂压力容器用钢板及其制造方法
CN111020351A (zh) * 2019-12-12 2020-04-17 舞阳钢铁有限责任公司 一种低温冲击韧性和焊接性能优异低碳型钢板及生产方法
CN113278878B (zh) * 2021-04-01 2022-09-30 江阴兴澄特种钢铁有限公司 一种厚度＞200～250mm抗氢致开裂压力容器钢板及其制造方法
CN115094316B (zh) * 2022-06-21 2023-06-20 日钢营口中板有限公司 一种心部低温冲击韧性优良的特厚钢板及其制造方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102277540A (zh) * 2010-06-10 2011-12-14 宝山钢铁股份有限公司 抗高温pwht软化的正火型钢板及其制造方法
CN102605242A (zh) * 2012-03-05 2012-07-25 宝山钢铁股份有限公司 一种抗氢致开裂压力容器用钢及其制造方法
US20120186704A1 (en) * 2009-06-24 2012-07-26 Jfe Steel Corporation High-strength seamless steel tube, having excellent resistance to sulfide stress cracking, for oil wells and method for manufacturing the same
CN104862616A (zh) * 2015-04-28 2015-08-26 江阴兴澄特种钢铁有限公司 一种大厚度高韧性容器钢板及其制造方法
CN104911503A (zh) * 2015-06-12 2015-09-16 江阴兴澄特种钢铁有限公司 一种特厚调质海洋工程用eh40钢及其制备方法
CN105018862A (zh) * 2015-07-11 2015-11-04 江阴兴澄特种钢铁有限公司 一种140mm厚度高韧性钢板及其制造方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104357750A (zh) * 2014-11-13 2015-02-18 舞阳钢铁有限责任公司 大厚度抗硫化氢腐蚀钢板及其生产方法
CN104480384A (zh) * 2014-11-29 2015-04-01 首钢总公司 510MPa级抗氢致开裂压力容器用钢板及生产方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20120186704A1 (en) * 2009-06-24 2012-07-26 Jfe Steel Corporation High-strength seamless steel tube, having excellent resistance to sulfide stress cracking, for oil wells and method for manufacturing the same
CN102277540A (zh) * 2010-06-10 2011-12-14 宝山钢铁股份有限公司 抗高温pwht软化的正火型钢板及其制造方法
CN102605242A (zh) * 2012-03-05 2012-07-25 宝山钢铁股份有限公司 一种抗氢致开裂压力容器用钢及其制造方法
CN104862616A (zh) * 2015-04-28 2015-08-26 江阴兴澄特种钢铁有限公司 一种大厚度高韧性容器钢板及其制造方法
CN104911503A (zh) * 2015-06-12 2015-09-16 江阴兴澄特种钢铁有限公司 一种特厚调质海洋工程用eh40钢及其制备方法
CN105018862A (zh) * 2015-07-11 2015-11-04 江阴兴澄特种钢铁有限公司 一种140mm厚度高韧性钢板及其制造方法

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