WO2024127180A1 - Tôle d'acier laminée à chaud à haute résistance à l'usure et son procédé de fabrication - Google Patents

Tôle d'acier laminée à chaud à haute résistance à l'usure et son procédé de fabrication Download PDF

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Publication number
WO2024127180A1
WO2024127180A1 PCT/IB2023/062361 IB2023062361W WO2024127180A1 WO 2024127180 A1 WO2024127180 A1 WO 2024127180A1 IB 2023062361 W IB2023062361 W IB 2023062361W WO 2024127180 A1 WO2024127180 A1 WO 2024127180A1
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Prior art keywords
steel plate
temperature
steel
hot rolled
rolled steel
Prior art date
Application number
PCT/IB2023/062361
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English (en)
Inventor
David QUIDORT
Céline KNAFOU
Alexandre GIORGI
Original Assignee
Arcelormittal
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Publication date
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Publication of WO2024127180A1 publication Critical patent/WO2024127180A1/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
    • C21D1/18—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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • 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
    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D1/84—Controlled slow cooling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C22C38/18—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
    • C22C38/48—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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Definitions

  • the present invention relates to a hot rolled steel plate having high wear resistance, high strength and high toughness, and to a method to obtain such steel plate.
  • the purpose of the invention therefore is to solve the above-mentioned problem and to provide a steel plate having high hardness above or equal to 400HB and preferably to 440HB at mid thickness of the plate and above or equal to 430HB and preferably to 450 HB at the surface of the plate, and high toughness with Charpy impact energy at -40°C above or equal to 25 J, and easily processable on conventional process route.
  • the hot rolled steel plate has a yield strength YS above or equal to 970MPa and preferably above or equal to 980 MPa.
  • the hot rolled steel plate has a tensile strength TS above or equal to 1400MPa.
  • the object of the present invention is achieved by providing a steel plate according to claim 1 .
  • Another object is achieved by providing the method according to claim 2.
  • composition of the steel according to the invention will now be described, the content being expressed in weight percent.
  • the carbon content is from 0.10% to 0.25 %. If the carbon content is too high, the weldability of the steel is insufficient. If the carbon content is lower than 0.10%, the austenite fraction is not stabilized enough to obtain targeted properties. In a preferred embodiment of the invention, the carbon content is from 0.15% and 0.20%.
  • the manganese content is from 3.0% to 5.0 %. Above 5.0% of addition, the risk of central segregation increases to the detriment of the toughness. Below 3.0%, the final structure comprises an insufficient retained austenite fraction to obtain the desired properties. In a preferred embodiment of the invention the manganese content is between 3.5% and 4.5%.
  • the silicon content is from 0.80% to 1.60%.
  • a silicon addition of at least 0.80% helps to stabilize a sufficient amount of retained austenite.
  • silicon is detrimental for toughness.
  • silicon oxides form at the surface, which impairs the coatability of the steel.
  • the silicon content is from 1.00% to 1.60%.
  • the aluminium content is from 0.10% to 0.60 %, as it is a very effective element for deoxidizing the steel in the liquid phase during elaboration. Moreover, aluminium improves weldability of the steel. The aluminium content is lower than 0.60% to avoid the occurrence of inclusions and to avoid oxidation problems.
  • the boron content can be from 0.0003% and 0.004%.
  • the presence of boron can increase the toughness.
  • boron improves weldability of the steel. Above 0.004%, the formation of borocarbides at the prior austenite grain boundaries is promoted, making the steel more brittle. Below 0.0003%, there is not a sufficient concentration of free B that segregates at the prior austenite grain boundaries to increase toughness of the steel.
  • Titanium can be added optionally up to 0.06% to provide precipitation strengthening.
  • a minimum of 0.01 % of titanium is added in addition of boron to protect boron against the formation of BN.
  • Niobium can be added up to 0.05% to refine the austenite grains during hot-rolling and to provide precipitation strengthening.
  • the minimum amount of niobium added is 0.0010%.
  • Molybdenum can optionally be added, in a limit of maximum 0.3 %. Molybdenum stabilizes the austenite and increases toughness of the steel. Moreover, molybdenum improves weldability of the steel. Above 0.3%, the addition of molybdenum is costly and ineffective in view of the properties which are required. Preferably, the minimum amount of molybdenum is 0.0010%.
  • chromium A maximum of 0.80% of chromium is allowed. Above, a saturation effect is noted, and adding chromium is both useless and expensive. Preferably, the minimum amount of chromium is 0.0010%.
  • Copper can be added up to 0.2% in order to increase the toughness of the steel.
  • Nickel can be added up to 0.30% to limit the risk of delayed fracture due to hydrogen embrittlement.
  • the remainder of the composition of the steel is iron and impurities resulting from the smelting.
  • P, S and N at least are considered as residual elements which are unavoidable impurities.
  • Their content is below or equal to 0.010 % for S, below or equal to 0.020 % for P and below or equal to 0.008 % for N.
  • the hot rolled steel plate has a microstructure consisting of, in surface fraction, from 5% to 10% of retained austenite, the balance being auto tempered martensite.
  • the steel plate is hot rolled with a final rolling temperature FRT above Ac1 .
  • the FRT is below Ac3 and the microstructure consists of ferrite and austenite. During the subsequent cooling, ferrite and a part of austenite are transformed in martensite.
  • the FRT is above or equal to Ac3
  • the microstructure is fully austenitic.
  • austenite is transformed in martensite.
  • the martensite is auto tempered, because of the slow cooling rate of the subsequent cooling, which leads to obtain the targeted mechanical properties.
  • the steel plate can have a thickness above 25mm, and below 40mm.
  • a heating step up to a temperature TH from 850°C to 950°C is necessary to obtain a homogeneous microstructure of austenite in the thickness of the plate.
  • a temperature TQ below 400°C a part of this austenite is transformed in martensite. This martensite is then auto-tempered during the subsequent air cooling.
  • a part of the austenite remains in the final microstructure.
  • This retained austenite contributes to obtain a great wear resistance and is beneficial for toughness.
  • the retained austenite will be transformed to martensite inducing a volume expansion from the fee to bcc structure, which can fill impact cracks and stop their propagation.
  • the TRIP effect induces also a great workhardening in service, which largely contribute to improve the wear resistance of the bare material.
  • the steel plate according to the invention can be produced by any appropriate manufacturing method and the man skilled in the art can define one. It is however preferred to use the method according to the invention comprising the following steps:
  • a semi-product able to be further hot-rolled is provided with the steel composition described above.
  • the semi product is heated to a temperature of 1100°C to 1300°C, so to make it possible to ease hot rolling, with a final hot rolling temperature FRT above Ac1.
  • FRT is above Ac1 +100°C, more preferably above Ac1 +150°C.
  • the microstructure will not contain enough austenite to ensure the hardness and toughness of the plate.
  • the FRT is below Ac3.
  • the FRT is above or equal to Ac3.
  • the hot-rolled steel plate having a thickness above or equal to 5mm and below 40 mm is then air cooled.
  • the cooling rate at mid thickness of the plate is below 5°C/s.
  • the steel plate is reheated to a temperature TH of 850°C to 950°C and maintained at said temperature for a holding time below or equal to 30 minutes, in order to obtain an homogeneous microstructure in all the thickness of the plate.
  • the plate is then quenched at a cooling rate higher than 1 °C/s to a temperature TQ below 400°C, in order to obtain at mid thickness of the steel plate a temperature of 300°C to 400°C at the end of the quenching, before being air cooled to room temperature.
  • Calculations done with the use of a software like Forge® allow to determine the duration of the quenching to obtain a temperature of 300°C to 400°C at mid thickness of the steel plate at the end of the quenching.
  • the quenching temperature TQ is above or equal to 200°C, more preferably above or equal to 250°C.
  • the tested compositions are gathered in the following table wherein the element contents are expressed in weight percent.
  • phase percentages of the microstructure of the obtained hot rolled steel plate were determined at quarter thickness d/4 of the steel plate.
  • the surface fractions of phases in the microstructure are determined through the following method: a specimen is cut from the hot rolled plate, polished and etched with a reagent known per se, to reveal the microstructure. The section is afterwards examined through scanning electron microscope, for example with a Scanning Electron Microscope with a Field Emission Gun (“FEG-SEM”) at a magnification greater than 5000x, in secondary electron mode.
  • FEG-SEM Field Emission Gun
  • the steel part of trials 4-6 have a chemical composition with lower manganese.
  • the quenching step in trial 4 is performed down to room temperature at a slow cooling rate. A part of austenite is then transformed in martensite, being auto tempered because of the slow cooling but also in bainite, which is detrimental for hardness.
  • the quenching step is done down to room temperature, at a higher cooling rate. Austenite is thus totally transformed into martensite. The absence of austenite is detrimental for toughness.
  • Trials 2 and 6 undergo the same process, the difference being in the chemical composition.
  • the low level of manganese combined to the absence of boron in trial 6 lead to low toughness.
  • the high thickness steel plate of trial 7 is reheated and quenched.
  • This quenching step is interrupted at a temperature of 350°C before being air cooled to room temperature.
  • Austenite formed during the heating step is then partly transformed into martensite.
  • This martensite is auto-tempered during the air cooling step, leading to the high hardness and toughness level.

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

Abstract

L'invention concerne une tôle d'acier laminée à chaud ayant une composition comprenant, en pourcentage en poids : C : 0,10 à 0,25 %, Mn : 3,0 à 5,0 %, Si : 0,80 à 1,60 %, Al : 0,10 % à 0,60 %, S ≤ 0 010 %, P ≤ 0 020 %, N ≤ 0 008 %, le reste de la composition étant du fer et des impuretés inévitables résultant de la fusion, et ayant une microstructure constituée, en fraction de surface : de 5 à 10 % d'austénite résiduelle, le reste étant de la martensite auto-trempée.
PCT/IB2023/062361 2022-12-12 2023-12-07 Tôle d'acier laminée à chaud à haute résistance à l'usure et son procédé de fabrication WO2024127180A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
PCT/IB2022/062059 WO2024127058A1 (fr) 2022-12-12 2022-12-12 Tôle d'acier laminée à chaud à haute résistance à l'usure et son procédé de fabrication
IBPCT/IB2022/062059 2022-12-12

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WO2024127180A1 true WO2024127180A1 (fr) 2024-06-20

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PCT/IB2023/062361 WO2024127180A1 (fr) 2022-12-12 2023-12-07 Tôle d'acier laminée à chaud à haute résistance à l'usure et son procédé de fabrication

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103255341A (zh) * 2013-05-17 2013-08-21 宝山钢铁股份有限公司 一种高强度高韧性热轧耐磨钢及其制造方法
KR20140141842A (ko) * 2013-05-31 2014-12-11 현대제철 주식회사 고강도 강재 및 그 제조 방법
US20190010571A1 (en) * 2015-12-15 2019-01-10 Posco High hardness wear-resistant steel with excellent toughness and cutting crack resistance and method for manufacturing same
WO2021124094A1 (fr) * 2019-12-17 2021-06-24 Arcelormittal Tôle d'acier laminée à chaud et son procédé de fabrication
WO2021193310A1 (fr) * 2020-03-25 2021-09-30 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute résistance et son procédé de fabrication

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103255341A (zh) * 2013-05-17 2013-08-21 宝山钢铁股份有限公司 一种高强度高韧性热轧耐磨钢及其制造方法
KR20140141842A (ko) * 2013-05-31 2014-12-11 현대제철 주식회사 고강도 강재 및 그 제조 방법
US20190010571A1 (en) * 2015-12-15 2019-01-10 Posco High hardness wear-resistant steel with excellent toughness and cutting crack resistance and method for manufacturing same
WO2021124094A1 (fr) * 2019-12-17 2021-06-24 Arcelormittal Tôle d'acier laminée à chaud et son procédé de fabrication
WO2021193310A1 (fr) * 2020-03-25 2021-09-30 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute résistance et son procédé de fabrication

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