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WO2020085849A1 - Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication - Google Patents

Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication Download PDF

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Publication number
WO2020085849A1
WO2020085849A1 PCT/KR2019/014166 KR2019014166W WO2020085849A1 WO 2020085849 A1 WO2020085849 A1 WO 2020085849A1 KR 2019014166 W KR2019014166 W KR 2019014166W WO 2020085849 A1 WO2020085849 A1 WO 2020085849A1
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Prior art keywords
steel
less
strength
magnetic
weldability
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Ceased
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PCT/KR2019/014166
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English (en)
Korean (ko)
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WO2020085849A8 (fr
Inventor
이동호
김성규
이운해
강상덕
한상호
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Posco Holdings Inc
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Posco Co Ltd
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Priority to CN201980068247.8A priority Critical patent/CN112888803A/zh
Priority to EP19875440.0A priority patent/EP3872209B1/fr
Publication of WO2020085849A1 publication Critical patent/WO2020085849A1/fr
Publication of WO2020085849A8 publication Critical patent/WO2020085849A8/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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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
    • C22C38/02—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
    • C22C38/06—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a non-magnetic steel material that can be suitably used in parts that generate eddy currents, such as a switchboard and a transformer, and more particularly, to a non-magnetic steel material having excellent strength and ductility as well as weldability and a method for manufacturing the same.
  • Ferritic or martensitic stainless steel may be applied to increase the strength of the non-magnetic steel, but since the ferritic or martensitic stainless steel has high magnetism, not only does power loss due to eddy current occur, but also the price is very high. It has the disadvantage of being expensive.
  • steel materials having an austenite phase have been developed by controlling the contents of manganese (Mn) and carbon (C) in steel.
  • These austenite steel grades have the advantage of stably maintaining the austenite phase even at room temperature and cryogenic temperature by controlling the content of the two elements, so that the non-magnetic properties can be well maintained.
  • One aspect of the present invention is to provide a non-magnetic steel material having excellent high weldability and high strength and high ductility at a low manufacturing cost from optimizing alloy composition.
  • Another aspect of the present invention is to provide a method for manufacturing the non-magnetic steel described above.
  • carbon (C) 0.03 ⁇ 0.50%, silicon (Si): 0.3% or less, manganese (Mn): 15-30%, chromium (Cr): 2.0% or less (0 % Excluded), molybdenum (Mo): 0.5% or less (excluding 0%), titanium (Ti): 0.01 to 0.1%, vanadium (V): 0.01 to 0.5%, aluminum (Al): 0.2 to 1.0%, phosphorus ( P): 0.1% or less, sulfur (S): 0.01 wt% or less, nitrogen (N): 0.03% or less, the balance contains other unavoidable impurities and Fe, high strength and high ductility visa with excellent weldability with austenite single phase structure Provides sex steel.
  • the present invention provides a method of manufacturing a high strength and high ductility nonmagnetic steel material having excellent weldability.
  • the steel material of the present invention is not only excellent in strength and ductility, but also has an effect of having excellent weldability.
  • 1 is a graph showing the results of measuring the permeability of invention steel and comparative steel according to an embodiment of the present invention.
  • the inventors of the present invention have studied in depth to provide a non-magnetic steel material having excellent strength and high ductility as well as excellent non-magnetic properties and excellent weldability. As a result, it was found that it is possible to provide an optimum component system capable of significantly improving the phase stability of the non-magnetic steel.
  • Al is added at a certain content to prevent carbon from forming carbides, and by further adding Cr and Mo, strength, ductility, and weldability can be further improved. There will be technical significance to it.
  • High-strength and highly ductile non-magnetic steel with excellent adhesion is in weight percent, carbon (C): 0.03 to 0.50%, silicon (Si): 0.3% or less, manganese (Mn): 15 to 30% , Chrome (Cr): 2.0% or less (excluding 0%), molybdenum (Mo): 0.5% or less (excluding 0%), titanium (Ti): 0.01 to 0.1%, vanadium (V): 0.01 to 0.5%, aluminum (Al): 0.2 to 1.0%, phosphorus (P): 0.1% or less, sulfur (S): 0.01 wt% or less, nitrogen (N): 0.03% or less.
  • the content of each component means weight%, and the proportion of tissue is based on the area.
  • Carbon (C) is an important element for securing an austenite structure in steel, and by containing such C in a certain amount or more, the stability of austenite can be sufficiently secured.
  • the C may be included in an amount of 0.03% or more, and on the other hand, when the content of the C exceeds 0.30%, carbides are precipitated when exposed to a high temperature such as a roll for a long time, so that the non-magnetic properties Although lowered, in the present invention, since the formation of carbide is reduced by adding a certain amount of aluminum (Al), C may be included up to 0.50%.
  • C can be contained in an amount of 0.03 to 0.50%.
  • Si Silicon (Si) does not significantly affect the lamination defect energy of steel and is usually used as a deoxidizer. When the Si content exceeds 0.3%, manufacturing costs increase, and oxides are excessively formed, and thus the surface quality of the product may be deteriorated.
  • the Si may be included in an amount of 0.3% or less, and 0% is excluded in consideration of a level inevitably added in the steel manufacturing process.
  • Manganese (Mn) is an important element that plays a role in stabilizing the austenite structure, and it needs to be contained at 15% or more in order to obtain a low permeability of steel.
  • Mn Manganese
  • the content of C is low
  • the Mn is added to less than 15%, an ⁇ '-martensitic phase is formed, thereby degrading the non-magnetic properties.
  • the content of the Mn exceeds 30%, the manufacturing cost increases significantly, and there is a problem in that the surface quality is deteriorated by forming internal oxidation or processing cracks during heating in the hot working step.
  • Mn may be included in 15 to 30%.
  • Chromium (Cr) is an effective element for improving the strength by suppressing high-temperature oxidation to reduce surface defects and strengthen solid solution.
  • the Cr may be included in an amount of 2.0% or less, and 0% is excluded.
  • Molybdenum (Mo) is an effective element for increasing the precipitation strengthening effect by making the precipitation phase fine.
  • Mo Molybdenum
  • the alloy cost increases, and the precipitation phase becomes coarse, so that the above-described effect cannot be sufficiently obtained. Therefore, in consideration of this, the Mo may be included in 0.5% or less, and 0% is excluded.
  • Titanium (Ti) is an element that reacts with nitrogen (N) inside the steel to precipitate nitrides and form twins, and can be added to secure the strength and formability of the steel.
  • Ti forms a precipitation phase to improve the yield strength. Since such an effect can be obtained even with a small amount of addition, it can be added at 0.01% or more. However, if the content exceeds 0.1%, the precipitates are excessively formed, which may cause cracks during rolling or forging, and may deteriorate formability and weldability.
  • Ti may be included in an amount of 0.01 to 0.1%.
  • V Vanadium (V): 0.01 ⁇ 0.5%
  • Vanadium (V) is useful for improving strength by forming carbides, nitrides, etc. by reacting with carbon, nitrogen, and the like inside the steel.
  • high solubility at a high temperature of 900 ° C or higher, and low solubility at a temperature of 600 to 800 ° C is an element having a large precipitation strengthening effect.
  • the content exceeds 0.5% precipitates are formed excessively, and hot workability, such as rolling or forging, decreases, and there is a risk of cracking.
  • V may be included in an amount of 0.01 to 0.5%.
  • Aluminum (Al) is added as a deoxidizer and is an effective element to prevent the formation of carbides in the steel.
  • the content exceeds 1.0%, the tendency to form oxide increases, and welding of the molten pool becomes poor during arc welding, resulting in poor welding, and the quality of the surface of the product is deteriorated due to the formation of oxide.
  • Al may be included in 0.2 to 1.0%, and more advantageously, in 0.2 to 0.8%.
  • Phosphorus (P) 0.1% or less
  • Phosphorus (P) is an element that promotes segregation and causes cracking during casting, and is preferably contained as low as possible. When the content of P exceeds 0.1%, castability may deteriorate, so the P may include 0.1% or less.
  • S is an element that inhibits the physical properties of steel by forming inclusions such as MnS. Therefore, it is preferable to contain as low as possible, and if the content exceeds 0.01%, there is a problem of hot brittleness. Therefore, the S may be included in 0.01% or less.
  • N Nitrogen
  • Ti titanium
  • the N may be included in 0.03% or less.
  • the remaining component of the invention is iron (Fe).
  • Fe iron
  • unintended impurities from the raw material or the surrounding environment may inevitably be mixed, and therefore cannot be excluded. Since these impurities are known to anyone skilled in the ordinary manufacturing process, they are not specifically mentioned in this specification.
  • the nonmagnetic steel of the present invention having the above-described alloy composition has an austenite single phase structure as a microstructure.
  • an austenite single-phase structure as described above it is possible to maintain non-magnetic properties even when receiving external energy.
  • the non-magnetic steel of the present invention has an austenite phase with high stability from optimization of alloy composition, and from this, may have a property of a relative magnetic permeability of 1.01 or less in a magnetic field of 50 kA / m.
  • the loss due to the eddy current of the material exposed to the electromagnetic field is closely related to the magnetism of the material.
  • magnetism is proportional to the permeability ( ⁇ ). That is, the magnetic permeability increases as the permeability increases.
  • the steel material of the present invention is a thick steel plate having a thickness of 10 to 40 mm, and has excellent strength and ductility, and can specifically secure a tensile strength of 450 MPa or more and an elongation of 55% or more.
  • the steel slab is reheated at 1100 to 1250 ° C.
  • the rolling load When the temperature of the steel slab is reheated to less than 1100 ° C, the rolling load may be excessively taken during subsequent hot rolling, whereas when the temperature exceeds 1250 ° C, internal oxidation occurs severely and surface quality may deteriorate.
  • the re-heating of the steel slab can be carried out at 1100 ⁇ 1250 °C.
  • the reheated steel slab can be hot rolled according to the above to produce a thick steel plate. At this time, it is preferable to finish hot rolling at 800 to 1000 ° C.
  • the temperature during finishing hot rolling is less than 800 ° C, there is a problem that the load increases during rolling.
  • the higher the temperature during the hot rolling of the finish the lower the deformation resistance and the easier rolling, whereas the target strength cannot be secured due to the coarsening of the structure, so it is preferable to limit it to 1000 ° C or less.
  • the thick steel plate manufactured according to the above-described method can be cooled.
  • the cooling is preferably performed at a cooling rate sufficient to suppress the formation of grain boundary carbides, and more preferably at a cooling rate of 10 ° C / s or more.
  • the present invention is advantageous as the cooling rate is faster, there is no need to specifically limit the upper limit as long as it is within the range of accelerated cooling.
  • the upper limit may be limited to 80 ° C / s or less.
  • cooling of the thick steel sheet may be stopped at 500 ° C or lower. Even if accelerated cooling is performed as described above, when cooling is stopped at an excessively high temperature, there is a fear that carbides are generated and grown. When a large amount of carbide is produced, there is a problem that the austenite stability decreases and the permeability characteristics decrease.
  • the cooling is performed at room temperature, there is no difficulty in securing the intended physical properties, and the lower limit of the cooling end temperature is not particularly limited.
  • the final steel (thick steel plate) of the present invention obtained by completing the process of hot rolling and cooling has a high-stability austenite phase as a microstructure, whereby it is excellent in high strength and high ductility as well as weldability and non-magnetic properties. Can have.
  • each steel slab having the alloy composition shown in Table 1 below, the steel slab was reheated at 1200 ° C, and then hot rolled at 950 ° C to prepare each thick steel sheet. Thereafter, the produced thick steel sheets were cooled to 20 ° C / s to complete cooling at 400 ° C.
  • yield strength (YS), tensile strength (TS), elongation (El)) and permeability of each of the thick steel plates prepared above were measured, and the results are shown in Table 2 below.
  • the yield strength (YS) is represented by a 0.2% offset value.
  • the permeability is expressed as the relative permeability, which is the ratio of the permeability in vacuum and the permeability in a specific atmosphere.
  • the relative permeability ( ⁇ ) which is the ratio of permeability in vacuum and atmosphere, was measured using paramagnetic measuring equipment.
  • FCAW flux cored arc welding
  • the invention steels 1 to 4 satisfying both the alloy composition and the manufacturing conditions of the present invention can be confirmed that the relative magnetic permeability is measured to be less than 1.01, and the strength and ductility as well as the weldability are good. can confirm.
  • the comparative steel 2 containing a large amount of Cr and the comparative steel 3 containing a large amount of C and lacking the Al content it can be seen that the permeability is very inferior to 1.01 or more.
  • the comparative steel 4 containing no large amounts of Cr and Mo, relatively high Al content containing comparative steels 1 and C, and excessive Al content has a magnetic permeability of 1.01 and poor weldability. It is judged that the arc stability is deteriorated due to the strong deoxidation effect by Al in the steel, and welding defects are caused due to surface bead defects. In addition, it has been confirmed that the recovery rate of other elements such as Ti is improved, resulting in deterioration of impact toughness, materials, etc., as precipitation phases of Al 2 O 3 and Ti (Al) (CN) are formed.
  • the alloy composition proposed in the present invention when satisfied as compared with a conventional steel containing a large amount of Cr and Ni, a non-magnetic steel material can be obtained at a lower cost.
  • the non-magnetic steel of the present invention is excellent in strength and ductility as well as weldability, it is described that the application uses will be expanded.

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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)

Abstract

La présente invention concerne un acier non magnétique qui peut être utilisé de manière appropriée pour des composants dans lesquels un courant de Foucault survient, tel qu'une carte de distribution et un transformateur et, plus spécifiquement, une forte pente non magnétique ayant d'excellentes résistance, ductilité et soudabilité, et son procédé de fabrication.
PCT/KR2019/014166 2018-10-25 2019-10-25 Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication Ceased WO2020085849A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
CN201980068247.8A CN112888803A (zh) 2018-10-25 2019-10-25 焊接性优良的高强度、高延性、非磁性钢材及其制造方法
EP19875440.0A EP3872209B1 (fr) 2018-10-25 2019-10-25 Acier non magnétique à haute résistance et ductilité élevée ayant une excellente soudabilité, et son procédé de fabrication

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020180128433A KR102119962B1 (ko) 2018-10-25 2018-10-25 용접성이 우수한 고강도 및 고연성 비자성 강재 및 이의 제조방법
KR10-2018-0128433 2018-10-25

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WO2020085849A1 true WO2020085849A1 (fr) 2020-04-30
WO2020085849A8 WO2020085849A8 (fr) 2020-10-08

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KR (1) KR102119962B1 (fr)
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117165851A (zh) * 2023-08-29 2023-12-05 南京钢铁股份有限公司 一种高性能建筑用20Mn23AlV无磁钢板及其制备方法

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JPS621823A (ja) * 1985-06-25 1987-01-07 Kobe Steel Ltd 被削性にすぐれた高Ｍｎ非磁性鋼の製造方法
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JP2016196703A (ja) * 2015-04-02 2016-11-24 新日鐵住金株式会社 極低温用高Ｍｎ鋼材

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