EP4324954A2 - Tôle d'acier à dureté élevée et son procédé de fabrication - Google Patents

Tôle d'acier à dureté élevée et son procédé de fabrication Download PDF

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Publication number
EP4324954A2
EP4324954A2 EP24150998.3A EP24150998A EP4324954A2 EP 4324954 A2 EP4324954 A2 EP 4324954A2 EP 24150998 A EP24150998 A EP 24150998A EP 4324954 A2 EP4324954 A2 EP 4324954A2
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EP
European Patent Office
Prior art keywords
steel sheet
less
hardness
content
excluding
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
EP24150998.3A
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German (de)
English (en)
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EP4324954A3 (fr
Inventor
Young-Roc Im
Jun-Sang JANG
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Posco Holdings Inc
Original Assignee
Posco Co Ltd
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Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Publication of EP4324954A2 publication Critical patent/EP4324954A2/fr
Publication of EP4324954A3 publication Critical patent/EP4324954A3/fr
Pending legal-status Critical Current

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Classifications

    • 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
    • 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
    • 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
    • C21D8/0247—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
    • C22C38/02—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
    • C22C38/40—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
    • 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
    • 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
    • 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
    • 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 disclosure relates to a high-hardness steel sheet used in various fields and a manufacturing method thereof .
  • a steel sheet having high hardness is excellent in terms of wear resistance and load supporting ability, thus guaranteeing long service life as well as durability, and is used in various components.
  • a steel grade is defined on the basis of Brinell hardness, and steel is manufactured to have various levels of hardness, from a Brinell hardness (HB) grade of 350 to a HB grade of 600, according to the related art.
  • HB Brinell hardness
  • a steel sheet having high hardness also has high strength, and thus may even be used in a field requiring a structure having high strength, such as a collision member or a reinforcing member.
  • the steel sheet described above may have good economic value in terms of lightweightness and efficiency.
  • a steel sheet is phase-transformed to a martensite or bainite structure in a cooling process from an austenite temperature range to room temperature, so high hardness and strength, which a low temperature transformation structure has, are generally provided.
  • An aspect of the present disclosure may provide a high-hardness steel sheet having a Brinell hardness of 500 HB or more in which a steel composition is set using a minimum carbon content relation for obtaining a Brinell hardness of 500 HB or more.
  • Another aspect of the present disclosure may provide a method of manufacturing a high-hardness steel sheet having a Brinell hardness of 500 HB or more by setting a steel composition according to a minimum carbon content relation for obtaining a Brinell hardness of 500 HB or more.
  • a high-hardness steel sheet having a Brinell hardness of 500 HB or more the steel sheet manufactured by including cooling of a hot rolled steel sheet, includes carbon (C) : 0.05 wt% to 0.3 wt%, silicon (Si): 0.5 wt% or less (excluding 0%), manganese (Mn) : 2.5 wt% or less (excluding 0%), chrome (Cr): 1.5 wt% or less (excluding 0%), molybdenum (Mo) : 1.0wt% or less (excluding 0%), nickel (Ni) : 1.0 wt% or less (excluding 0%), niobium (Nb) : 0.1 wt% or less (excluding 0%), titanium (Ti): 0.1 wt% or less (excluding 0%), vanadium (V) : 0.1 wt% or less (excluding 0%), boron (B) : 0.01 wt% or less (excluding 0%), aluminum
  • Mn, Si, Cr, Ni, and Mo are values representing the content of each element by wt%
  • C.R. is a value representing a cooling rate during cooling of a hot-rolled steel sheet, and the unit thereof is °C/sec.
  • a method of manufacturing a high-hardness steel sheet includes hot-rolling and cooling a steel slab including carbon (C): 0.05 wt% to 0.3 wt%, silicon (Si): 0.5 wt% or less (excluding 0%), manganese (Mn): 2.5 wt% or less (excluding 0%), chrome (Cr) : 1.5 wt% or less (excluding 0%), molybdenum (Mo): 1.0 wt% or less (excluding 0%), nickel (Ni) : 1.0 wt% or less (excluding 0%), niobium (Nb): 0.1 wt% or less (excluding 0%), titanium (Ti): 0.1 wt% or less (excluding 0%), vanadium (V) : 0.1 wt% or less
  • Mn, Si, Cr, Ni, and Mo are values representing the content of each element by wt%
  • C.R. is a value representing a cooling rate during cooling of a hot-rolled steel sheet, and the unit thereof is °C/sec.
  • a component of a more economical and unified steel sheet may be designed.
  • the prior art related to a high-hardness steel sheet has proposed various components and process control methods in order to obtain a level of hardness required, according to the components, but fails to provide a component criteria for unified hardness acquisition.
  • the present inventors have conducted studies and experiments on the conditions of component design for securing a required level of hardness, when a microstructure of a steel sheet is formed to have 95 vol. % or more of a martensite structure in order to secure a high level of hardness and strength, and the present invention has been completed on the basis of the results thereof.
  • one of the main technical features of the present invention is to provide the conditions of a component design for securing a required level of hardness when a microstructure of a steel sheet is formed as 95 vol.% or more of a martensite structure in order to secure high hardness and strength, and thus, more economically manufacturing a microstructure including 95 vol.% or more of a martensite phase and a steel sheet having a Brinell hardness of 500 HB or more, and obtaining unified hardness.
  • the content of carbon (C) may be 0.05% to 0.3%.
  • the content of carbon (C) may be 0.19 wt% to 0.3%.
  • the content of silicon (Si) may be 0.5% or less (excluding 0%).
  • Silicon is a preferred alloying element in applications in which hardness is used, because silicon increases the wear resistance of steel. However, when an amount of Si is excessive, surface properties and plating properties of the steel become poor, and a complete austenitization may not be performed during reheating.
  • the content of silicon (Si) may be 0.21% to 0.5%.
  • the content of silicon (Si) may be 0.253% to 0.34%.
  • Manganese (Mn) and chrome (Cr) are elements significantly lowering martensite transformation temperatures, and manganese and chrome are elements, which may be used economically as low-cost elements, since manganese and chrome have an effect of reducing a transformation temperature less than that of carbon, among elements generally added to steel.
  • An upper limit of the manganese content is preferably limited to 2.5%, and an upper limit of the chromium content is preferably limited to 1.5%.
  • austenite may remain at room temperature, so 95 vol.% or more of a martensitic structure, a targeted amount, may not be obtained.
  • the content of manganese may be 1.4% to 2.5%.
  • the content of manganese may be 2.1% to 2.5%.
  • Molybdenum (Mo) and nickel (Ni) are elements lowering a martensite transformation start temperature.
  • a degree of lowering a martensite transformation start temperature is smaller than those of Mn and Cr. Due to being relatively expensive elements, an upper limit of an addition amount of each of these elements is preferably limited to 1.0%.
  • Each of niobium (Nb) and titanium (Ti) may be added in an amount of 0.1% or less (excluding 0%), and may have an effect of improving the impact characteristics of a steel sheet through austenite grain refinement.
  • the excessive addition of Nb and Ti may cause coarsening of Nb carbonitride, fixing grain boundaries, so a crystal grain refinement effect may be lost.
  • an upper limit of each of Nb and Ti is preferably limited to 0.1%.
  • Ti when B is added, Ti may be essentially added to protect B from N. Titanium (Ti) first reacts with carbon or nitrogen in steel, so TiC or TiN is formed. Thus, an addition effect of boron (B) may be increased. In this case, the content of titanium (Ti) may satisfy Relation 2 depending on stoichiometry, with respect to an amount of nitrogen in steel. Ti wt % > N wt % ⁇ 3.42
  • V Vanadium (V): 0.1% or less (excluding 0%)
  • Vanadium (V) may be added in an amount of 0.1% or less (excluding 0%), and may serve to prevent precipitation hardening through the formation of fine V carbides and the deterioration of physical properties of a welded portion.
  • an addition amount of V is excessive, the effect described above may be reduced due to the coarsening of a carbide, so that an upper limit of the content of V is preferably limited to 0.1%.
  • B Boron (B) may be added in an amount of 0.01% or less (excluding 0%), and B is an element significantly increasing hardenability of steel by inhibiting nucleation of ferrite and pearlite. Even when a thickness of steel is great, utilization thereof is significant.
  • a final microstructure may be provided as 95 vol.% or more of martensite.
  • a manufacturing method thereof is not particularly limited, so B may be added to secure hardenability as required. However, when the content of B is excessively added, B may rather act as a nucleation site on ferrite or pearlite to deteriorate hardenability, so an upper limit of the content of B is preferably limited to 0.01%.
  • Aluminum (Al) is added for deoxidization and grain refinement, and the content of Al is preferably limited to 0.1% or less (excluding 0%).
  • the remainder excluding elements described above include iron (Fe) and other unavoidable impurities.
  • a minimum content of carbon (C) may satisfy Relation (1).
  • C a minimum content of carbon C ⁇ 0.481 ⁇ 0.104 Mn ⁇ 0.035 Si ⁇ 0.088 Cr ⁇ 0.054 Ni ⁇ 0.035 Mo ⁇ 0.0003 C .R .
  • Mn, Si, Cr, Ni, and Mo are values representing the content of each element by wt%
  • C.R. is a value representing a cooling rate during cooling of a hot-rolled steel sheet, and the unit thereof is °C/sec.
  • Relation (1) represents a minimum content of a carbon (C) for obtaining a Brinell hardness of 500 HB or more from a composition of silicon (Si), manganese (Mn), chrome (Cr), molybdenum (Mo), nickel (Ni), and chrome (Cr).
  • Relation (1) may be designed using, for example, Relation (3) .
  • HB Brinell hardness 100.4 + 830.5 * C + 86.5 * Mn + 28.8 * Si + 73.4 * Cr + 44.5 * Ni + 28.8 * Mo + 0.252 * C .R .
  • C, Mn, Si, Cr, Ni, and Mo are values representing the content of each element by wt%
  • C.R. is a value representing a cooling rate during cooling of a hot-rolled steel sheet, and the unit thereof is °C/sec.
  • Relation (1) with respect to a minimum carbon content for HB ⁇ 500 may be derived from Relation (3).
  • Relation (3) by using Relation (3) within a steel sheet component range of the present invention, proper alloying element design conditions to obtain any required level of hardness of 350 HB or more may be derived.
  • a microstructure of a steel sheet according to the present invention may include 95 vol.% or more of a martensite phase.
  • the microstructure of a steel sheet according to the present invention may include one or two of ferrite and bainite, in an amount of less than 5.0 vol.%, as a second phase structure, other than martensite.
  • the steel sheet according to the present invention may have Brinell hardness of 500 HB or more.
  • a steel slab including carbon (C): 0.05 wt% to 0.3 wt%, silicon (Si): 0.5 wt% or less (excluding 0%), manganese (Mn) : 2.5 wt% or less (excluding 0%), chrome (Cr): 1.5 wt% or less (excluding 0%), molybdenum (Mo): 1.0 wt% or less (excluding 0%), nickel (Ni) : 1.0 wt% or less (excluding 0%), niobium (Nb): 0.1 wt% or less (excluding 0%), titanium (Ti): 0.1 wt% or less (excluding 0%), vanadium (V): 0.1 wt% or less (excluding 0%), boron (B): 0.01 wt% or less (excluding 0%), aluminum (Al): 0.1 wt% or less (excluding 0%), a balance of iron (Fe): 1.0 wt% or less (excluding 0%), manganese (M
  • a minimum content of carbon (C) in the steel slab satisfies Relation (1).
  • C a minimum content of carbon C ⁇ 0.481 ⁇ 0.104 Mn ⁇ 0.035 Si ⁇ 0.088 Cr ⁇ 0.054 Ni ⁇ 0.035 Mo ⁇ 0.0003 C .R .
  • Mn, Si, Cr, Ni, and Mo are values representing the content of each element by wt%
  • C.R. is a value representing a cooling rate during cooling of a hot-rolled steel sheet, and the unit thereof is °C/sec.
  • a steel slab Before the steel slab is hot-rolled as a hot-rolled steel sheet, a steel slab may be reheated.
  • Conditions for reheating a slab are not particularly limited, and the conditions are sufficient as long as homogenization is allowed.
  • a slab reheating temperature is preferably 1100°C to 1300°C.
  • the hot-rolling conditions are preferably not limited, and a hot finish rolling temperature is sufficient as long as austenitization is allowed.
  • the hot finish rolling temperature may be, for example, 870°C to 930°C, and whole hot-rolling may be performed within a temperature range of 1150°C to a hot finish rolling temperature, after extraction from a heating furnace.
  • a cooling rate during cooling the hot-rolled steel sheet is not preferably limited while a cooling rate allows 95 vol.% or more of a martensite phase to be obtained.
  • the cooling rate is 20°C/sec or more, and preferably, 20°C/sec to 150°C/sec.
  • a cooling end temperature during cooling the hot-rolled steel sheet is the Ms point (a martensite transformation start temperature) or below, and is not particularly limited as long as a cooling end temperature allows 95 vol.% or more of a martensite phase to be obtained.
  • compositions of steels of Table 1 satisfy a composition range of the present invention.
  • a second phase structure of Table 2 indicates a second phase structure, other than martensite. Moreover, a structure other than a second phase structure is martensite, and 100% martensite is referred to as 100%M.
  • F indicates ferrite
  • B indicates bainite
  • M indicates martensite
  • a Brinell hardness (HB) value is 500 HB or more.
  • a high-hardness steel sheet the steel sheet provided by cooling a hot rolled steel sheet, comprising:
  • a method of manufacturing a high-hardness steel sheet comprising: hot-rolling and cooling a steel slab including carbon (C) : 0.05 wt% to 0.3 wt%, silicon (Si): 0.5 wt% or less (excluding 0%), manganese (Mn): 2.5 wt% or less (excluding 0%), chrome (Cr): 1.5 wt% or less (excluding 0%), molybdenum (Mo) : 1.0 wt% or less (excluding 0%), nickel (Ni): 1.0 wt% or less (excluding 0%), niobium (Nb): 0.1 wt% or less (excluding 0%), titanium (Ti): 0.1 wt% or less (excluding 0%), vanadium (V): 0.1 wt% or less (excluding 0%), boronitride, silicon (Si): 0.5 wt% or less (excluding 0%), manganese (Mn): 2.5 wt% or less (excluding 0%),
  • a cooling end temperature during the cooling the hot-rolled steel sheet is the Ms point (a martensite transformation start temperature) or below.

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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 Sheet Steel (AREA)
EP24150998.3A 2015-08-21 2016-08-18 Tôle d'acier à dureté élevée et son procédé de fabrication Pending EP4324954A3 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
KR1020150117985A KR101696094B1 (ko) 2015-08-21 2015-08-21 고 경도 강판 및 그 제조방법
PCT/KR2016/009079 WO2017034216A1 (fr) 2015-08-21 2016-08-18 Tôle d'acier à dureté élevée et son procédé de fabrication
EP16839505.1A EP3339464B1 (fr) 2015-08-21 2016-08-18 Procédé de fabrication d'une tôle d'acier à dureté élevée

Related Parent Applications (2)

Application Number Title Priority Date Filing Date
EP16839505.1A Division-Into EP3339464B1 (fr) 2015-08-21 2016-08-18 Procédé de fabrication d'une tôle d'acier à dureté élevée
EP16839505.1A Division EP3339464B1 (fr) 2015-08-21 2016-08-18 Procédé de fabrication d'une tôle d'acier à dureté élevée

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Publication Number Publication Date
EP4324954A2 true EP4324954A2 (fr) 2024-02-21
EP4324954A3 EP4324954A3 (fr) 2024-05-22

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EP16839505.1A Active EP3339464B1 (fr) 2015-08-21 2016-08-18 Procédé de fabrication d'une tôle d'acier à dureté élevée
EP24150998.3A Pending EP4324954A3 (fr) 2015-08-21 2016-08-18 Tôle d'acier à dureté élevée et son procédé de fabrication

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US (1) US20180237875A1 (fr)
EP (2) EP3339464B1 (fr)
JP (1) JP6843119B2 (fr)
KR (1) KR101696094B1 (fr)
CN (1) CN107923023B (fr)
WO (1) WO2017034216A1 (fr)

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KR102031443B1 (ko) * 2017-12-22 2019-11-08 주식회사 포스코 우수한 경도와 충격인성을 갖는 내마모강 및 그 제조방법
KR102031446B1 (ko) * 2017-12-22 2019-11-08 주식회사 포스코 우수한 경도와 충격인성을 갖는 내마모강 및 그 제조방법
KR102045646B1 (ko) * 2017-12-26 2019-11-15 주식회사 포스코 재질 균일성이 우수한 내마모 강판 및 그 제조방법
KR102175570B1 (ko) * 2018-09-27 2020-11-06 주식회사 포스코 우수한 경도와 충격인성을 갖는 내마모강 및 그 제조방법
JP7163889B2 (ja) * 2019-08-21 2022-11-01 Ｊｆｅスチール株式会社 耐疲労特性に優れた耐摩耗鋼材の製造方法
JP7163887B2 (ja) * 2019-08-21 2022-11-01 Ｊｆｅスチール株式会社 耐疲労特性に優れた耐摩耗鋼材
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EP3339464B1 (fr) 2024-07-03
CN107923023A (zh) 2018-04-17
EP3339464A1 (fr) 2018-06-27
US20180237875A1 (en) 2018-08-23
EP4324954A3 (fr) 2024-05-22
KR101696094B1 (ko) 2017-01-13
CN107923023B (zh) 2020-04-24
WO2017034216A1 (fr) 2017-03-02
JP2018528325A (ja) 2018-09-27
EP3339464A4 (fr) 2018-08-08
JP6843119B2 (ja) 2021-03-17

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