WO2017111489A1 - Matériau en acier austénitique présentant une excellente résistance à la fragilisation par l'hydrogène - Google Patents

Matériau en acier austénitique présentant une excellente résistance à la fragilisation par l'hydrogène Download PDF

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WO2017111489A1
WO2017111489A1 PCT/KR2016/015085 KR2016015085W WO2017111489A1 WO 2017111489 A1 WO2017111489 A1 WO 2017111489A1 KR 2016015085 W KR2016015085 W KR 2016015085W WO 2017111489 A1 WO2017111489 A1 WO 2017111489A1
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less
embrittlement resistance
steel
hydrogen
austenitic
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Ceased
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PCT/KR2016/015085
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English (en)
Korean (ko)
Inventor
이순기
김성규
강상덕
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Posco Holdings Inc
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Posco Co Ltd
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Priority to CA3009463A priority Critical patent/CA3009463C/fr
Priority to CN201680075016.6A priority patent/CN108431275A/zh
Priority to KR1020187019341A priority patent/KR20180085797A/ko
Priority to US16/065,062 priority patent/US20190010590A1/en
Priority to JP2018533257A priority patent/JP6703608B2/ja
Priority to EP16879356.0A priority patent/EP3395989B1/fr
Publication of WO2017111489A1 publication Critical patent/WO2017111489A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and 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
    • 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, 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
    • C22C38/02—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
    • C22C38/06—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
    • C22C38/08—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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • 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
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to an austenitic steel having excellent hydrogen embrittlement resistance, and more particularly, to an austenitic steel having excellent hydrogen embrittlement resistance, which can be preferably applied to a high pressure hydrogen gas storage tank, a pipe and a transportation facility. .
  • Hydrogen vehicles have been most commonly used in the form of compressing hydrogen at high pressure and storing it in a high-pressure gas, and such a container has to withstand high pressure, and therefore high strength and especially to minimize hydrogen loss due to hydrogen permeation.
  • the hydrogen permeability must be low and the hydrogen embrittlement resistance must be excellent to suppress embrittlement by hydrogen infiltration.
  • Typical FCC-based materials used for this purpose are austenitic stainless steels of Cr-Ni. These austenitic stainless steels are used in high pressure gas storage containers or liners and piping materials because of their excellent hydrogen embrittlement resistance under high pressure hydrogen gas environments.
  • Japanese Laid-Open Patent Publication No. 5-98391 and International Publication No. 2014-111285 disclose a technique of increasing the strength of austenitic stainless steel by cold working, but by cold working. The increase is not suitable as a container for storing hydrogen because the increase in ductility and toughness and the stability of austenite can be reduced to generate an organic martensite.
  • Korean Patent Publication No. 10-2006-0018250 discloses a technique for securing the stability of austenite by performing two cold working in different directions, but to increase the stability of austenite Since a large amount of Cr, Ni is added as an element, this is disadvantageous in terms of cost.
  • Ni an expensive alloy element of the conventional austenitic stainless steel, is replaced with a low-cost alloy element Mn.
  • a technique is still contained, which also contains a large amount of expensive alloying elements, which is an obstacle to commercialization.
  • One of several objects of the present invention is to provide an austenitic steel having excellent hydrogen embrittlement resistance without the addition of expensive alloying elements.
  • one aspect of the present invention by weight, C: 0.1 ⁇ 0.5%, Cu: 5% or less (excluding 0%), N: 1% or less (excluding 0%) Mn content satisfies Mn ⁇ -10.7C + 24.5, Cr: 10% or less, Ni: 5% or less, Mo: 5% or less, Si: 4% or less, Al: 5% or less, balance Fe And elongation at break (T-El 2 ) according to tensile test under high pressure hydrogen conditions of 25 ° C. and 70 MPa to breakdown elongation (T-El 1 ) according to tensile test under atmospheric conditions of 25 ° C. and 1 atm, including unavoidable impurities. It provides an austenitic steel having excellent hydrogen embrittlement resistance of the ratio (T-El 2 / T-El 1 ) of 0.5 or more.
  • the austenitic steel of the present invention has an advantage of having excellent hydrogen embrittlement resistance without the addition of expensive alloying elements.
  • 1 is a graph showing the composition range of carbon and manganese of the present invention.
  • Figure 2 is a photograph of the fracture surface after the room temperature tensile test for the specimen according to Inventive Example 1.
  • Containers for storing or transporting hydrogen should basically have a low transmittance of hydrogen. Therefore, in the case of steel materials, it is essential to secure an FCC structure with a low transmittance of hydrogen.
  • the FCC structure needs to be stably maintained even for external deformation such as plastic deformation.
  • the present inventors attempted to improve the hydrogen embrittlement resistance of steel materials by appropriately controlling the relationship between carbon and manganese content while relatively lowering the carbon content, and as a result, the present invention has been derived.
  • the alloy component and the preferred content range of the austenitic steels will be described in detail. It is noted that the content of each component described below is based on weight unless otherwise specified.
  • Carbon is an element that stabilizes austenite and improves the strength of steel, and in particular, serves to lower Ms and Md, which are transformation points of austenite into epsilon or alpha martensite by cooling or processing. If the carbon content is insufficient, the austenite stability may be insufficient, and the hydrogen embrittlement resistance may be drastically deteriorated because it is not easy to maintain the FCC structure due to the process organic transformation into epsilon or alpha martensite due to external stress. Therefore, in the present invention, the carbon content is preferably controlled to 0.1% or more, more preferably 0.15% or more, and even more preferably 0.2% or more.
  • the carbon content is preferably controlled to 0.5% or less, more preferably 0.45% or less.
  • the content of manganese is preferably determined by paying attention to the relationship between the carbon and other elements added together, and after the room temperature tensile test to ensure a stable austenitic or epsilon martensite with a low permeability of hydrogen stable hydrogen Manganese content range that can improve the chemical conversion is shown in FIG.
  • the graph of FIG. 1 is a result derived by various experiments of the present inventors.
  • Copper is an element that stabilizes the austenite structure for obtaining hydrogen embrittlement resistance and promotes slippage by increasing stacking defect energy.
  • copper when high carbon is added, copper has a very low solid solubility in carbides and a slow diffusion in austenite, concentrating at the interface between austenite and nucleated carbides. It is effectively slowed down and consequently serves to suppress the production of carbides. The suppression of the formation of carbides reduces the diffusion sites of carbon to improve hydrogen embrittlement resistance, and also to improve the ductility and toughness of steel materials.
  • the copper content is preferably controlled to 5% or less, and more preferably to 3.5% or less.
  • nitrogen is an element that stabilizes austenite to improve the toughness of steel.
  • nitrogen is a very advantageous element for enhancing the strength of steel through solid solution strengthening, such as carbon.
  • it is well known as an element that promotes the slip effectively by increasing the stacking defect energy.
  • the content is excessive, since the surface quality and physical properties of the steel may be degraded by forming coarse nitride, in the present invention, it is preferable to control the content of nitrogen to 1% or less, 0.5% or less This is more preferable.
  • the austenitic steels of the present invention may include Cr, Ni, Mo, Si, and Al.
  • Chromium stabilizes austenite up to the range of the proper addition amount, thereby increasing hydrogen embrittlement resistance, and is dissolved in austenite to increase the strength of steel.
  • chromium is also an element for improving the corrosion resistance of steel materials.
  • chromium is a carbide forming element, when the content thereof is excessive, it forms a carbide at the austenite grain boundary to provide a place for easy hydrogen diffusion and deteriorates the toughness of the steel. Therefore, in the present invention, the content of chromium is preferably controlled to 10% or less, more preferably 8% or less.
  • Nike is a very effective austenite stabilizing element and serves to lower Ms and Md, which are transformation points of austenite into epsilon or alpha martensite by cooling or processing.
  • Ms and Md transformation points of austenite into epsilon or alpha martensite by cooling or processing.
  • it is well known as an element that promotes the slip effectively by increasing the stacking defect energy.
  • nickel is an expensive alloy element, when the content is excessive, there is a problem that the economic efficiency is lowered. Therefore, in the present invention, it is preferable to control the content of nickel to 5% or less.
  • Molybdenum stabilizes austenite in an appropriate amount range, and serves to improve hydrogen embrittlement resistance of steel by lowering Ms and Md, which are transformation points of austenite into epsilon or alpha martensite by cooling or processing.
  • Ms and Md transformation points of austenite into epsilon or alpha martensite by cooling or processing.
  • it is dissolved in the steel to increase the strength of the steel, it is organized in the austenite grain boundary to increase the stability of the grain boundary to reduce the energy, thereby acting to suppress the grain boundary precipitation of carbonitride.
  • Equation 1 it is well known as an element that promotes the slip effectively by increasing the stacking defect energy.
  • it is well known as an element that promotes the slip effectively by increasing the stacking defect energy.
  • molybdenum even if molybdenum is not added, there is no major problem in terms of securing physical properties.
  • molybdenum is an expensive alloying element, and when its content is excessive, there is a problem that the economical efficiency is lowered. Therefore, in the present invention, the content of molybdenum is preferably controlled to 5% or less, more preferably 4% or less.
  • Silicon is an element that improves the castability of molten steel and, in particular, when added to an austenitic steel, is dissolved in the steel to effectively increase the strength of the steel.
  • silicon even if silicon is not added, there is no major problem in terms of securing physical properties.
  • the content is excessive, the stacking defect energy is reduced to encourage the generation of partial potential and cause stress concentration, thereby reducing the hydrogen embrittlement resistance of the steel. Therefore, in the present invention, it is preferable to control the content of silicon to 4% or less.
  • Aluminum stabilizes austenite in an appropriate amount range, and serves to improve hydrogen embrittlement resistance of steel by lowering Ms and Md, which are transformation points of austenite into epsilon or alpha martensite by cooling or processing.
  • Ms and Md transformation points of austenite into epsilon or alpha martensite by cooling or processing.
  • it is employed in the steel material to increase the strength of the steel, affect the activity of the carbon in the steel to effectively suppress the formation of carbides, and serves to increase the toughness of the steel.
  • it is an element that greatly increases the stacking defect energy of steel to induce cross-slip, suppress partial stress generation, reduce stress concentration, and increase hydrogen embrittlement resistance.
  • even if aluminum is not added, there is no major problem in terms of securing physical properties.
  • the rest is Fe.
  • impurities which are not intended from the raw material or the surrounding environment may be inevitably mixed, and thus cannot be excluded. Since these impurities are known to those skilled in the art, not all of them are specifically mentioned in the present specification. On the other hand, addition of an effective component other than the said composition is not excluded.
  • the austenitic steel of the present invention may have a stacking defect energy (SFE) of 30mJ / m 2 or more, which is defined by Equation 1 below.
  • SFE stacking defect energy
  • the lamination defect energy is relatively low, so that a partial potential is relatively easily generated, and the slip of the partial potential is limited to a specific slip surface. Accumulation and stress concentration are likely to be caused. However, such concentration of stress facilitates the diffusion of hydrogen. In high-manganese steels such as the present invention, there is a possibility that the fracture strength of the material decreases due to the diffusion of hydrogen, that is, embrittlement by hydrogen may occur. Very high.
  • the degree of work hardening by stress concentration of the steel can be measured by the work hardening rate according to the tensile test.
  • the austenitic steel of the present invention may have a strain hardening rate of 14000 N / mm 2 or less according to a tensile test under atmospheric conditions of 25 ° C. and 1 atm. This work hardening rate can be calculated from true strain and true stress. If the maximum value of the work hardening rate by the tensile test exceeds 14000 N / mm 2 , the stress concentration due to the electric potential becomes too large to facilitate the diffusion and accumulation of hydrogen, which may cause hydrogen embrittlement.
  • the austenitic steel of the present invention may be a tensile strength of 800MPa or less according to the tensile test under the atmospheric conditions of 25 °C and 1 atm. If the tensile strength exceeds 800 MPa, hydrogen embrittlement resistance may be inferior due to high work hardening caused by stress concentration.
  • the austenitic steel of the present invention may include an austenite structure of 95 area% or more as its microstructure. If the area fraction of the austenitic structure is less than 95%, there is a fear that the target hydrogen embrittlement resistance may not be secured.
  • the austenitic steels of the present invention may be made of austenite tissue or epsilon martensite tissue and austenite tissue after the tensile test under the atmospheric conditions of 25 °C and 1 atm. If the microstructure includes a ferrite structure after the tensile test, there is a fear that the target hydrogen embrittlement resistance may not be secured.
  • the austenitic steels of the present invention can be manufactured according to a conventional method for producing steel using steel slabs satisfying the above-described component system, and for example, reheating steel slabs satisfying the above-described component system and rough rolling And after finishing rolling, it can manufacture by cooling.
  • the finishing rolling finish temperature needs to be controlled to a temperature exceeding the unrecrystallized temperature.
  • the strength of the steel is excessively increased due to the generation and accumulation of excessive dislocations, thereby facilitating stress concentration and breakdown by hydrogen, and also causing fermentation of hydrogen during tensile deformation. Can be generated early, which in turn makes it difficult to achieve the desired hydrogen embrittlement resistance.
  • the microstructure of the rolled material was observed, and the austenite fraction was measured. Thereafter, the rolled material was subjected to a tensile test under atmospheric conditions of 25 and 1 atm, and then tensile strength, work hardening rate, and elongation at break (T-El 1 ) were measured, and the ferrite fraction was measured. In addition, the tensile elongation (T-El 2 ) was measured after a tensile test was performed on the rolled material under high pressure hydrogen conditions of 25 and 70 MPa. The results are shown in Table 3 below.
  • Inventive Examples 1 to 5 satisfying the component range of the present invention is obtained a stable austenite in which no ferrite is produced after the tensile deformation at room temperature, low work hardening rate and tensile strength is controlled, in particular finishing finishing The temperature is rolled beyond the recrystallization temperature to suppress the generation and scale of dislocations, and the cooling rate satisfies the range controlled by the present invention, thereby effectively suppressing carbide formation, resulting in excellent hydrogen embrittlement resistance with a very high ratio of break elongation. It shows that austenitic steels can be obtained.
  • Comparative Example 1 the content of carbon and manganese did not satisfy the range controlled by the present invention, and it was found that the ratio of fracture elongation was low, that is, the hydrogen embrittlement resistance was inferior due to the high content of carbon. Can be.
  • Comparative Example 4 it is found that the addition of carbon in excess of the range controlled by the present invention results in a high work hardening rate and inferior hydrogen embrittlement resistance due to excessive precipitation of carbides at the austenite grain boundary.
  • Comparative Example 5 can be seen that the hydrogen embrittlement resistance is inferior because the content of manganese does not fall within the range controlled by the present invention does not obtain the target microstructure.
  • Figure 2 is a photograph observing the fracture surface after the room temperature tensile test for the specimen according to Inventive Example 1, the fracture form appeared dimples typical of ductile failure.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un matériau austénitique présentant une excellente résistance à la fragilisation par l'hydrogène, comprenant, en poids, de 0,1 à 0,5 % de C, 5 % ou moins (0 % exclus) de Cu, 1 % ou moins (0 % exclus) de N, une teneur en Mn satisfaisant à la relation Mn ≥ -10,7 C + 24,5, 10 % ou moins de Cr, 5 % ou moins de Ni, 5 % ou moins de Mo, 4 % ou moins de Si, 5 % ou moins d'Al, le reste étant constitué de Fe et d'impuretés inévitables, avec un rapport T-El2/T-El1 supérieur ou égal à 0,5, T-El1 étant un allongement à la rupture selon un essai de traction réalisé à 25 °C sous une condition atmosphérique de 1 atm et T-El2 étant un allongement à la rupture selon un essai de traction réalisé à 25 °C sous une condition d'hydrogène de 70 MPa.
PCT/KR2016/015085 2015-12-22 2016-12-22 Matériau en acier austénitique présentant une excellente résistance à la fragilisation par l'hydrogène Ceased WO2017111489A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
CA3009463A CA3009463C (fr) 2015-12-22 2016-12-22 Materiau en acier austenitique presentant une excellente resistance a la fragilisation par l'hydrogene
CN201680075016.6A CN108431275A (zh) 2015-12-22 2016-12-22 耐氢脆性优异的奥氏体系钢材
KR1020187019341A KR20180085797A (ko) 2015-12-22 2016-12-22 내수소취화성이 우수한 오스테나이트계 강재
US16/065,062 US20190010590A1 (en) 2015-12-22 2016-12-22 Austenitic steel material having excellent hydrogen-embrittlement resistance
JP2018533257A JP6703608B2 (ja) 2015-12-22 2016-12-22 耐水素脆化性に優れたオーステナイト系鋼材
EP16879356.0A EP3395989B1 (fr) 2015-12-22 2016-12-22 Matériau en acier austénitique présentant une excellente résistance à la fragilisation par l'hydrogène

Applications Claiming Priority (2)

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KR20150184291 2015-12-22
KR10-2015-0184291 2015-12-22

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US (1) US20190010590A1 (fr)
EP (1) EP3395989B1 (fr)
JP (1) JP6703608B2 (fr)
KR (1) KR20180085797A (fr)
CN (1) CN108431275A (fr)
CA (1) CA3009463C (fr)
WO (1) WO2017111489A1 (fr)

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FR3106898B1 (fr) 2020-01-30 2022-10-07 Psa Automobiles Sa Procede d’analyse de la fragilisation par l’hydrogene de pieces en aciers nus ou revetus utilisees dans les vehicules automobiles
EP4515012A1 (fr) * 2022-04-29 2025-03-05 United States Steel Corporation Alliages d'acier à faible teneur en ni ayant une résistance à la dégradation par l'hydrogène
JP7424550B1 (ja) 2022-07-14 2024-01-30 Ｊｆｅスチール株式会社 水素輸送鋼管用高強度鋼板及びその製造方法並びに水素輸送用鋼管
WO2024071358A1 (fr) 2022-09-29 2024-04-04 Ｊｆｅスチール株式会社 Matériau d'acier pour tuyau de conduite à haute résistance présentant une excellente ténacité à la rupture dans l'hydrogène, son procédé de fabrication, tube d'acier pour tuyaux de conduite à haute résistance et son procédé de fabrication
KR102803122B1 (ko) 2022-12-01 2025-05-07 리녹스 주식회사 내수소취성이 향상된 스테인리스강의 제조방법
EP4628604A4 (fr) 2023-02-14 2026-03-18 Jfe Steel Corp Feuille d'acier à haute résistance pour tuyaux en acier de transport d'hydrogène, son procédé de fabrication et tuyau en acier de transport d'hydrogène

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