WO2019117536A1 - Tôle d'acier destinée à un récipient sous pression présentant une excellente force de traction et une excellente résistance aux chocs à basse température et procédé destiné à sa production - Google Patents

Tôle d'acier destinée à un récipient sous pression présentant une excellente force de traction et une excellente résistance aux chocs à basse température et procédé destiné à sa production Download PDF

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Publication number
WO2019117536A1
WO2019117536A1 PCT/KR2018/015424 KR2018015424W WO2019117536A1 WO 2019117536 A1 WO2019117536 A1 WO 2019117536A1 KR 2018015424 W KR2018015424 W KR 2018015424W WO 2019117536 A1 WO2019117536 A1 WO 2019117536A1
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Prior art keywords
steel sheet
tensile strength
steel
low
temperature
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PCT/KR2018/015424
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English (en)
Korean (ko)
Inventor
홍순택
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주식회사 포스코
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Priority to JP2020532603A priority Critical patent/JP7161536B2/ja
Priority to CN201880079767.4A priority patent/CN111465711B/zh
Publication of WO2019117536A1 publication Critical patent/WO2019117536A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/10—Reduction of greenhouse gas [GHG] emissions
    • Y02P10/122—Reduction of greenhouse gas [GHG] emissions by capturing or storing CO2

Definitions

  • the present invention the tensile strength and low-temperature impact toughness of the high pressure vessel steel sheet and a manufacturing method for, and more particularly, CO 2 storage tanks and pressure vessels, etc. of the material, preferably applied tensile strength and low-temperature impact toughness, which may in And a method of manufacturing the same.
  • the steel sheet is composed of 0.25% or less of C, 0.15 to 0.50% of Si, 1.00 to 1.50% of Mn, 0.08% or less of Mo and 0.08% or less of Cu,
  • As rolled or normalized or normalizing + SR (Stress Relief) heat treatment pattern is applied using a steel sheet material composed of not more than 0.25% of Ni, not more than 0.25% of Cr, not more than 0.025% of P, not more than 0.025% of P and not more than 0.025% of S .
  • SR Stress Relief
  • a post-weld heat treatment is performed in order to remove the stress generated during the welding.
  • PWHT post-weld heat treatment
  • the steel sheet subjected to the PWHT process for a long time has a problem that the tensile strength and low-temperature impact toughness of the steel sheet are largely lowered due to the coarsening of the structure.
  • Non-Patent Document 1 A612 / A612M-12: Standard Specification for Pressure Vessel Plates, Carbon Steel, High Strength, Moderate and Lower Temperature Service
  • One aspect of the present invention is to provide a steel sheet for a pressure vessel excellent in tensile strength and impact resistance at low temperatures even after PWHT heat treatment and a method for manufacturing the same.
  • An embodiment of the present invention is a steel sheet comprising, by weight%, 0.12 to 0.20% of C, 0.30 to 0.40% of Si, 1.50 to 1.70% of Mn, 0.03 to 0.10% of Mo, 0.05 to 0.30% of Cu, 0.001 to 0.10%, Ni: 0.03 to 0.25%, Cr: 0.03 to 0.25%, Al: 0.005 to 0.06%, Ca: 0.0005 to 0.0030%, P: 0.025% : 0.003 to 0.015%, Nb: 0.005 to 0.025%, and Ta: 0.002 to 0.050%, and the balance Fe and other unavoidable impurities, wherein the microstructure comprises ferrite; Tempered bainite; And a mixture of a pearlite and a degenerate pearlite, wherein the percentage of the tempered bainite is 5 to 50% by area, to provide.
  • a method of manufacturing a semiconductor device comprising: 0.12 to 0.20% of C, 0.30 to 0.40% of Si, 1.50 to 1.70% of Mn, 0.03 to 0.10% of Mo, 0.05 to 0.30% of Cu, 0.001 to 0.10%, Ni: 0.03 to 0.25%, Cr: 0.03 to 0.25%, Al: 0.005 to 0.06%, Ca: 0.0005 to 0.0030%, P: 0.025% : 0.003 to 0.015%, Nb: 0.005 to 0.025%, and Ta: 0.002 to 0.050%, and the remainder Fe and other unavoidable impurities are reheated at 950 to 1200 ° C step; Hot-rolling the reheated steel slab to a reduction ratio of 2.5 to 30% per pass to obtain a hot-rolled steel sheet; Subjecting the hot-rolled steel sheet to a normalizing heat treatment at 820 to 930 ⁇ for 1.3 ⁇ t + (10 to 30 minutes) (t is the
  • C is an element that improves strength.
  • the content is less than 0.12%, the strength of the matrix of the matrix decreases.
  • the content exceeds 0.20%, there is a problem that the strength decreases and the weldability deteriorates due to excessive strength.
  • Si is an effective element for deoxidation and solid solution strengthening and is an element accompanied by an increase in the impact transition temperature.
  • it is required to be added by 0.30% or more, but when it is added in excess of 0.40%, the weldability is lowered and the impact toughness is deteriorated.
  • Mn is an alloy element which has an important influence on the strength of steel and low-temperature toughness. If the Mn content is too low, the strength and toughness may be deteriorated. Therefore, the Mn content is preferably 1.50% or more. However, when the content is too high, the weldability is lowered, and there is a fear of an increase in steel manufacturing cost. Therefore, the upper limit is preferably limited to 1.70%.
  • Mo is an element effective for improving the ingot qualities of steel and preventing sulphide cracking as well as for improving the strength of steel by precipitation of fine carbides after quenching and sintering. In order to obtain such effects in the present invention, it is preferable to add 0.03% or more. However, if the content is too high, there is a risk of rising steel production cost, so the upper limit is preferably limited to 0.10%.
  • Cu is an element effective for increasing the strength. It is desirable to add Cu in an amount of 0.05% or more. However, since the Cu is expensive, its upper limit is preferably limited to 0.30%.
  • V is an element capable of easily forming fine carbides and nitrides, and the above effect can be obtained by adding 0.03% or more.
  • the upper limit is preferably limited to 0.30%.
  • Ni is the most effective element for improving the low-temperature toughness, and the above effect can be obtained by adding 0.03% or more thereof. However, it is preferable that Ni is added in an amount of 0.25% or less.
  • Cr is an element for increasing the strength
  • Cr should be added in an amount of 0.03% or more.
  • the production cost is increased.
  • Al is one of the strong deoxidizers in the steelmaking process together with Si.
  • the deoxidizing effect is insignificant.
  • the content exceeds 0.06%, the deoxidizing effect is saturated and the manufacturing cost is increased.
  • Ca is generated as CaS and acts to inhibit nonmetallic inclusions of MnS, so Ca is added in an amount of 5 ppm or more. However, if the addition amount is excessive, it reacts with O contained in the steel to produce CaO which is a nonmetallic inclusion, which is not good for physical properties, so the upper limit is limited to 30 ppm.
  • P is an impurity which is inevitably added in the steel, and is an element that increases susceptibility to shrinkage while lowering low-temperature toughness. Therefore, it is preferable to control the content as low as possible. In the present invention, the P content is controlled to 0.025% or less.
  • S is an impurity which is inevitably contained in steel and lowers the low-temperature toughness and forms MnS inclusions, thereby deteriorating the toughness of steel. Therefore, it is preferable to control the content as low as possible. In the present invention, the S content is controlled to 0.025% or less.
  • the steel sheet of the present invention preferably further comprises at least two selected from the group consisting of 0.003 to 0.015% of Ti, 0.005 to 0.025% of Nb, and 0.002 to 0.050% of Ta in addition to the alloy composition described above.
  • Ti is an effective element to prevent softening of the base structure by forming fine carbides or nitrides.
  • the content should be 0.003% or more, but it is preferable to limit the upper limit to 0.015% because it is an expensive element.
  • Nb is an effective element to prevent softening of the matrix by forming fine carbides or nitrides.
  • the content should be 0.005% or more, but it is preferable to limit the upper limit to 0.025% because it is an expensive element.
  • Ta 0.002 to 0.050%
  • Ta is an effective element to prevent softening of the base structure by forming fine carbides or nitrides.
  • 0.002% or more should be added, but it is preferable to limit the upper limit to 0.050% because it is an expensive element.
  • the remainder of the present invention is iron (Fe).
  • impurities which are not intended from the raw material or the surrounding environment may be inevitably incorporated, so that it can not be excluded. These impurities are not specifically mentioned in this specification, as they are known to any person skilled in the art of manufacturing.
  • the steel sheet for a pressure vessel of the present invention is characterized in that its microstructure is ferrite; Tempered bainite; And a mixed structure comprising at least one of pearlite and degenerate pearlite. By securing such microstructure, excellent strength and impact resistance at low temperature can be ensured even after PWHT.
  • the fraction of the tempered bainite is preferably 5 to 50% by area.
  • the PWHT resistance can be improved by securing at least 5% by area of tempered bainite in the mixed structure. However, if it exceeds 50% by area, the strength may excessively increase. It is more preferable that the fraction of the tempered bainite is in the range of 5 to 50 area%.
  • the PWHT resistance can be further improved by controlling the precipitates as described above. If the size of the precipitate is less than 5 nm, it may be difficult to ensure the desired strength. If the size exceeds 80 nm, the impact toughness may be deteriorated. If the fraction of the precipitate is less than 0.003% by volume, the effect of improving the strength may not be sufficient. If it exceeds 0.15% by volume, the impact toughness may be deteriorated.
  • the size of the precipitate refers to the equivalent circular diameter of the particles detected by observing the thickness direction cross section of the steel sheet.
  • the above-described steel sheet for a pressure vessel of the present invention can be produced by various methods, and the production method thereof is not particularly limited. However, as a preferable example, the following method can be applied.
  • the steel slab having the above-described alloy composition is reheated at 950 to 1200 ° C. If the reheating temperature is lower than 950 ⁇ , solute atoms hardly solidify, whereas when the reheating temperature is higher than 1200 ⁇ , the austenite grain size becomes excessively large, and the properties of the steel sheet may be deteriorated.
  • the reheated steel slab is hot-rolled at a reduction ratio of 2.5 to 30% per pass to obtain a hot-rolled steel sheet. If the reduction rate per pass is less than 2.5%, there is a possibility that an internal defect may occur due to a shortage of the reduction amount. If the reduction rate exceeds 30%, the reduction capability of the facility may be exceeded.
  • the hot-rolled steel sheet is subjected to a normalizing heat treatment at 820 to 930 ° C for 1.3 times t + (10 to 30 minutes) (t is the thickness (mm) of the steel sheet).
  • t is the thickness (mm) of the steel sheet.
  • the normalizing heat treatment temperature is lower than 820 ⁇ ⁇ , it is difficult to secure the strength because the solid solute elements are difficult to be reused.
  • the temperature exceeds 930 ⁇ ⁇ , the growth of the hardened steel is caused and the low temperature toughness is deteriorated. If the holding time is less than 1.3 x t + 10 min, the homogenization of the tissue may not be sufficient, and if the holding time exceeds 1.3 x t + 30 min, the productivity may be deteriorated.
  • the normalized heat-treated hot-rolled steel sheet is cooled at a cooling rate of 0.5 to 30 ⁇ ⁇ / s based on the value of 1 / 4t (t is the thickness (mm) of the steel sheet) in the temperature range from the normalizing temperature range to 450 ⁇ ⁇ do.
  • t is the thickness (mm) of the steel sheet
  • the cooling rate is less than 0.5 DEG C / s, proper bainite transformation is difficult to secure strength.
  • the cooling rate is more than 20 DEG C / s, excessive microstructure having a bainite fraction is obtained, The low-temperature toughness may also decrease.
  • the cooled hot-rolled steel sheet is subjected to tempering treatment at 550 to 680 ° C for 1.6 ⁇ t + (10 to 30 minutes) (t is the thickness (mm) of the steel sheet).
  • t is the thickness (mm) of the steel sheet.
  • the tempering heat treatment temperature is less than 550 ° C.
  • precipitation of fine precipitates is difficult, and it is difficult to secure strength.
  • the tempering temperature exceeds 680 ° C., precipitates are grown to deteriorate strength and low temperature toughness. If the holding time is 1.6 x t + 10 min, the homogenization of the structure may not be sufficient. If the holding time exceeds 1.6 x t + 30 min, the productivity may be deteriorated.
  • the steel sheet for a pressure vessel of the present invention manufactured through the heat treatment process is required to be subjected to a PWHT treatment in order to remove residual stress by a welding process added at the time of manufacturing a pressure vessel.
  • a PWHT treatment for a long time, the strength and the toughness deteriorate.
  • the steel sheet produced by the present invention has a high strength and toughness even after heat treatment at a temperature range of 580 to 650 ° C, which is a typical PWHT condition, There is an advantage that it is possible.
  • the steel sheet for a pressure vessel of the present invention has a tensile strength of 590 MPa or more and a Charpy impact energy value at -50 ⁇ , even after 10 hours of post-weld heat treatment (PWHT) in a temperature range of 580 to 650 ⁇ It can be over 150J.
  • PWHT post-weld heat treatment
  • a steel slab having the alloy composition shown in the following Table 1 was reheated at 1140 ⁇ for 300 minutes and hot rolled in the recrystallization region under the conditions of a reduction ratio of 10 to 15% per pass to obtain a hot-rolled steel sheet, ⁇ t + 20 min (where t is the thickness (mm) of the steel sheet), and the normalized heat-treated hot-rolled steel sheet is subjected to heat treatment at a temperature of 1 / (t is the thickness (mm) of the steel sheet) at 650 deg. C for 1.6 x t + 20 minutes (where t is the thickness (mm) of the steel sheet) A steel sheet for a pressure vessel was produced.
  • the resulting steel sheet was observed for microstructure and subjected to PHWT heat treatment, and then the yield strength, tensile strength, elongation and low-temperature impact toughness were measured, and the results are shown in Table 2 below.
  • the low-temperature impact toughness is a Charpy impact energy value obtained by performing a Charpy impact test on a specimen having a V notch at -50 ° C.
  • the inventive steels 1 to 3 satisfying the alloy composition and the manufacturing conditions of the present invention have excellent mechanical properties such as tensile strength and low-temperature impact toughness even if the PWHT time is 10 hours or less .
  • tensile strength is about 70 MPa and low-temperature impact toughness is about 150 J or more lower than Inventive Steel 1 to 3 even if the manufacturing conditions of the present invention are satisfied .

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

La présente invention concerne une tôle d'acier destinée à un récipient sous pression présentant une excellente force de traction et une excellente résistance aux chocs à basse température, et un procédé destiné à sa production. Selon un mode de réalisation, la présente invention fournit une tôle d'acier destinée à un récipient sous pression présentant une excellente force de traction et une excellente résistance aux chocs à basse température, et un procédé destiné à sa production, la tôle d'acier comprenant, en % en poids, 0,12 à 0,20 % de C, 0,30 à 0,40 % de Si, 1,50 à 1,70 % de Mn, 0,03 à 0,10 % de Mo, 0,05 à 0,30 % de Cu, 0,03 à 0,10 % de V, 0,03 à 0,25 % de Ni, 0,03 à 0,25 % de Cr, 0,005 à 0,06 % d'Al, 0,0005 à 0,0030 % de Ca, 0,025 % ou moins de P et 0,025 % ou moins de S, comprenant en outre au moins deux types choisis dans le groupe constitué de 0,003 à 0,015 % de Ti, de 0,005 à 0,025 % de Nb et de 0,002 à 0,050 % de Ta, et comprenant un reste de Fe et d'autres impuretés inévitables, et la microstructure comprenant de la ferrite ; de la bainite revenue ; et une structure mixte comprenant un ou deux éléments parmi la perlite et la perlite dégénérée, la fraction de la bainite revenue étant de 5 à 50 % en surface.
PCT/KR2018/015424 2017-12-15 2018-12-06 Tôle d'acier destinée à un récipient sous pression présentant une excellente force de traction et une excellente résistance aux chocs à basse température et procédé destiné à sa production WO2019117536A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
JP2020532603A JP7161536B2 (ja) 2017-12-15 2018-12-06 引張強度及び低温衝撃靭性に優れた圧力容器用鋼板及びその製造方法
CN201880079767.4A CN111465711B (zh) 2017-12-15 2018-12-06 拉伸强度和低温冲击韧性优异的用于压力容器的钢板及其制造方法

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KR1020170173648A KR101998991B1 (ko) 2017-12-15 2017-12-15 인장강도 및 저온충격인성이 우수한 압력용기용 강판 및 그 제조방법
KR10-2017-0173648 2017-12-15

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CN112831724A (zh) * 2021-01-04 2021-05-25 南京钢铁股份有限公司 一种s420高强度低温结构钢及其正火轧制制备方法
CN114032368A (zh) * 2021-11-26 2022-02-11 成都先进金属材料产业技术研究院股份有限公司 一种铁素体不锈钢00Cr18Mo2的热处理方法
CN114341382A (zh) * 2019-09-03 2022-04-12 株式会社Posco 具有优异的低温侧向膨胀的压力容器用钢板及其制造方法
CN114585760A (zh) * 2019-10-22 2022-06-03 株式会社Posco 高温焊后热处理耐性优异的压力容器用钢板及其制造方法
CN114807766A (zh) * 2022-05-05 2022-07-29 重庆钢铁股份有限公司 一种低温压力容器用微合金钢板及其生产方法
WO2022262071A1 (fr) * 2021-06-17 2022-12-22 南京钢铁股份有限公司 Plaque d'acier pour récipient standard américain sous conditions de service à basse température, et procédé de production associé

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KR102349426B1 (ko) * 2020-05-18 2022-01-11 현대제철 주식회사 저온 충격인성이 우수한 강재 및 그 제조방법
CN112522610B (zh) * 2020-11-18 2022-03-25 北京交通大学 控制V-Ti复合型贝氏体非调质钢组织及其制作方法
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