EP4265795A1 - Ultradicke stahlplatte mit hervorragender tieftemperaturschlagzähigkeit und verfahren zur herstellung davon - Google Patents

Ultradicke stahlplatte mit hervorragender tieftemperaturschlagzähigkeit und verfahren zur herstellung davon Download PDF

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Publication number
EP4265795A1
EP4265795A1 EP21906913.5A EP21906913A EP4265795A1 EP 4265795 A1 EP4265795 A1 EP 4265795A1 EP 21906913 A EP21906913 A EP 21906913A EP 4265795 A1 EP4265795 A1 EP 4265795A1
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EP
European Patent Office
Prior art keywords
steel plate
temperature
ultra
rolling
impact toughness
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
EP21906913.5A
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English (en)
French (fr)
Inventor
Woo-Gyeom KIM
Sang-Ho Kim
Dae-Woo BAEK
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Posco Holdings Inc
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Posco Co Ltd
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Filing date
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Publication of EP4265795A1 publication Critical patent/EP4265795A1/de
Pending 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • 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
    • C22C38/04—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—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
    • C21D2211/005—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
    • C21D2211/009—Pearlite

Definitions

  • the present disclosure relates to structural steel materials which can be used, for example, as a material for marine, bridge, and construction and, more specifically, to an ultra-thick steel plate having excellent low-temperature impact toughness and a method for manufacturing the same.
  • An ultra-thick steel plate having a certain thickness or more may be manufactured through a thick plate process, and in this case, a rolling method may be divided into general rolling, normalizing rolling, and thermo-mechanical controlled rolling (TMCP), and the like.
  • TMCP thermo-mechanical controlled rolling
  • a heat treatment process may be performed after rolling, and in this case, the heat treatment process includes a normalizing heat treatment process, a quenching heat treatment process, a quenching-tempering heat treatment, and the like.
  • general rolling is a method of rolling without controlling a rolling temperature, which may be mainly applied to general steel not requiring impact toughness.
  • TMCP performs recrystallization region rolling and non-recrystallization region rolling through temperature control, and it is possible to secure strength and impact toughness through cooling, as necessary.
  • TMCP performs recrystallization region rolling and non-recrystallization region rolling through temperature control, and it is possible to secure strength and impact toughness through cooling, as necessary.
  • a long waiting time is required to adjust a rolling temperature, resulting in a serious decrease in productivity.
  • Normalizing rolling is finished at a relatively high temperature, so strength and toughness may decrease due to grain growth during air cooling.
  • the ultra-thick steel plate may be applied to various structural industries such as infrastructure industries such as ships, and various frames of offshore structures, bridges, construction, and the like, and wind power substructures, and the like.
  • a metallurgical disadvantage of ultra-thick steel plates is that it is difficult to realize strength and secure toughness due to a decrease in a rolling amount and limitations in a cooling process.
  • Patent Document 1 Korean Patent Publication No. 10-2014-0003010
  • An aspect of the present disclosure is to provide an ultra-thick steel plate having excellent strength and low-temperature impact toughness by overcoming metallurgical disadvantages of the existing ultra-thick steel plate and a method for manufacturing the same.
  • An object of the present disclosure is not limited to the above description.
  • the object of the present disclosure will be understood from the entire content of the present specification, and a person skilled in the art to which the present disclosure pertains will understand an additional object of the present disclosure without difficulty.
  • an ultra-thick steel plate having excellent low-temperature impact toughness including, by weight: 0.06 to 0.1% of carbon (C), 0.3 to 0.5% of silicon (Si), 1.35 to 1.65% of manganese (Mn), 0.015 to 0.04% of aluminum (sol.Al), 0.015 to 0.04% of niobium (Nb), 0.005 to 0.02% of titanium (Ti), 0.15 to 0.4% of chromium (Cr), 0.3 to 0.5% of nickel (Ni), 0.002 to 0.008% of nitrogen (N), 0.01% or less (excluding 0%) of phosphorus (P), 0.003% or less (excluding 0%) of sulfur (S), with a balance of iron (Fe) and inevitable impurities, satisfying the following Relational Expression 1,
  • ultra-thick steel plate includes, by area fraction: 80 to 90% of ferrite and a remainder of pearlite as a microstructure.
  • a method for manufacturing an ultra-thick steel plate having excellent low-temperature impact toughness including operations of: preparing a steel slab satisfying the above-described alloy composition and Relational Expression 1; heating the steel slab at a temperature within a range of 1020 to 1150°C; subjecting the heated steel slab to rough rolling at 1000°C or higher; finish hot rolling the steel slab at a temperature directly above a no-recrystallization temperature (Tnr) or at a temperature within a range of Tnr to A3 after the rough rolling; and air cooling the same after the finish hot rolling.
  • Tnr no-recrystallization temperature
  • an ultra-thick steel plate having excellent strength and low-temperature impact toughness for an ultra-thick steel plate having a thickness of 100 to 200 mm may be provided.
  • the ultra-thick steel plate of the present disclosure may be used in various fields, such as infrastructure industries such as ships, various frames of marine structures, bridges, construction, and the like, and wind power substructures, and the like.
  • FIG. 1 illustrates a photograph of a microstructure of an ultra-thick steel plate according to an embodiment of the present disclosure.
  • the ultra-thick steel plate having target physical properties can be provided by optimizing an alloy composition system of the ultra-thick steel plate and a rolling process, and thus the present disclosure was provided.
  • the present disclosure has technical significance in that it is possible to solve a problem of productivity of the existing TMCP steel material, a problem of securing physical properties of a general rolling material and heat treatment material, a problem of heat treatment material costs, and the like.
  • an ultra-thick steel plate having excellent low-temperature impact toughness may include, by weight: 0.06 to 0.1% of carbon (C), 0.3 to 0.5% of silicon (Si), 1.35 to 1.65% of manganese (Mn), 0.015 to 0.04% of aluminum (sol.Al), 0.015 to 0.04% of niobium (Nb), 0.005 to 0.02% of titanium (Ti), 0.15 to 0.4% of chromium (Cr), 0.3 to 0.5% of nickel (Ni), 0.002 to 0.008% of nitrogen (N), 0.01% or less (excluding 0%) of phosphorus (P), 0.003% or less (excluding 0%) of sulfur (S).
  • a content of each element is based on weight, and a ratio of structure is based on area.
  • Carbon (C) is an element causing solid solution strengthening and combining with Nb, and the like in steel to form carbonitrides, which is advantageous for securing strength of steel.
  • C may be included in an amount of 0.06% or more, but when the C content exceeds 0.1%, a pearlite phase is excessively formed as a microstructure, so that there is a problem impact and fatigue properties at a low temperature deteriorates. In addition, as a content of solid solution C increases, the impact properties decrease.
  • the C may be included in an amount of 0.06 to 0.1%, and more advantageously, in an amount of 0.07% or more and 0.09% or less.
  • Si serves to deoxidize molten steel together with aluminum (Al).
  • Al aluminum
  • Si has an effect on improving strength, but when the Si content is excessive, impact and fatigue properties at a low temperature may be impaired, so that it is necessary to add Si in an appropriate amount.
  • Si may be included in an amount of 0.3 to 0.5%.
  • Manganese (Mn) is an element having a great effect on improving strength by solid solution strengthening, and may be included in an amount of 1.35% or more. However, when the Mn content is excessive, since there is a concern that toughness may be deteriorated due to formation of MnS inclusions and center portion segregation, Mn may be included in an amount of 1.65% or less in consideration thereof.
  • Aluminum (Sol.Al) is a major deoxidizer of steel, and is advantageous for fixing nitrogen (N) in steel.
  • N nitrogen
  • similar to Si there is a problem in that low-temperature toughness and low-temperature fatigue properties are deteriorated by accelerating the formation of the MA phase in a base material and a weld heat-affected zone.
  • Al may be included in an amount of 0.015 to 0.04%.
  • Niobium (Nb) 0.015 to 0.04%
  • Niobium (Nb) has a solid solution strengthening effect, and is advantageous in improving strength by suppressing recrystallization during rolling or cooling by forming a carbonitride to finely form a structure.
  • Nb may be contained in an amount of 0.015% or more.
  • the content of Nb is excessive, C concentration occurs due to C affinity, so that the formation of the MA phase is promoted and there is a problem of impairing toughness and fatigue properties at a low temperature, so that the content of Nb may be limited to be 0.04% or less in consideration thereof.
  • Nb may be included in an amount of 0.015 to 0.04%, more advantageously, Nb may be included in an amount of 0.02% or more.
  • Titanium (Ti) combines with nitrogen (N), which may deteriorate impact properties and surface quality of steel, to form a Ti-based nitride (TiN), and serves to reduce a content of dissolved N.
  • the Ti-based precipitate contributes to refinement by suppressing coarsening of a structure, and is useful for improving toughness.
  • Ti may be contained in an amount of 0.005% or more, but when the Ti content exceeds 0.02%, causing destruction due to coarsening of precipitates, and dissolved Ti remaining after combining with N forms a Ti-based carbide (TiC), so that there is a problem of impairing toughness a base material and a weld zone.
  • TiC Ti-based carbide
  • Ti may be included in an amount of 0.005 to 0.02%, and more advantageously, Ti may be included in an amount of 0.01% or more.
  • Chromium (Cr) is an element advantageous for improving strength by increasing hardenability of steel.
  • Cr may be included in an amount of 0.15% or more, but when a content of Cr exceeds 0.4%, not only weldability is deteriorated, but also there is a problem of causing an increase in manufacturing costs as an expensive element.
  • Cr may be included in an amount of 0.15 to 0.4%.
  • Nickel (Ni) is an element that can simultaneously improve strength and toughness of steel.
  • Ni may be contained in an amount of 0.3% or more.
  • the Ni content exceeds 0.5%, the above-described effect is saturated, but there is a problem in that manufacturing cost increases.
  • Ni may be included in an amount of 0.3 to 0.5%.
  • Nitrogen (N) combines with Ti, Nb, Al, and the like in steel to form precipitates, and these precipitates are effective in improving strength and toughness by forming a fine austenite structure during reheating.
  • N may be included in an amount of 0.002 to 0.008%.
  • Phosphorus (P) is an element which causes grain boundary segregation, which may cause brittleness of steel. Therefore, the content of P should be controlled to be as low as possible.
  • the P content may be limited to be 0.01% or less.
  • 0% may be excluded, considering an inevitably added level.
  • S Sulfur mainly combines with Mn in steel, to form MnS inclusions, which is a factor impairing low-temperature toughness.
  • the S content should be controlled to be as low as possible, and may be preferably limited to be 0.003% or less. However, 0% may be excluded, considering an inevitably added level.
  • a remainder of the present disclosure may be iron (Fe).
  • Fe iron
  • inevitable impurities may be inevitably added from raw materials or an ambient environment, and thus, impurities may not be excluded.
  • a person skilled in the art of a general manufacturing process may be aware of the impurities, and thus, the descriptions of the impurities may not be provided in the present disclosure.
  • the content of C may be limited to be 0.10% or less.
  • the relationship between Mn, Ni, and Cr in steel is controlled by the Relational Expression 1, so that it is not adversely affected to secure strength, even when the C content is relatively lowered.
  • the ultra-thick steel plate of the present disclosure satisfying the above-described alloy composition and Relational Expression 1 may have a microstructure composed of a composite structure of ferrite and pearlite.
  • the ultra-thick steel plate of the present disclosure includes, by area fraction: 80 to 90% of ferrite, and a remainder of pearlite.
  • the fraction of the ferrite When the fraction of the ferrite is less than 80%, it is difficult to secure low-temperature toughness of the ultra-thick steel plate. On the other hand, when the fraction of the ferrite exceeds 90%, the fraction of pearlite is insufficient, making it impossible to secure the target level of strength.
  • the ultra-thick steel plate of the present disclosure has a fine structure as an average grain size of the ferrite is 50 ⁇ m or less.
  • the average grain size is based on a circle equivalent diameter.
  • the present disclosure has an effect capable of securing excellent strength and low-temperature toughness at the same time, by finely implementing the structure of the ultra-thick steel plate.
  • the ultra-thick steel plate of the present disclosure may have a yield strength of 300 MPa or more and an impact toughness of 200 J or more at -20°C, showing high strength and excellent low-temperature impact toughness.
  • the steel plate may be manufactured by preparing a steel slab satisfying the alloy composition and Relational Expression 1 proposed in the present disclosure, then subjecting the steel slab to the processes of [heating - rolling - air cooling].
  • a rolling process is performed in a normalizing heat-treatment region as a rolling process without performing a separate heat treatment after completing the rolling process.
  • a heating process may be performed in a temperature range of 1020 to 1150°C.
  • the steel slab may have a thickness of 400 mm or less to secure a sufficient amount of rolling to secure strength and toughness, while having a maximum thickness of 200 mm by a subsequent rolling process.
  • a hot-rolled steel sheet may be manufactured by hot rolling the steel slab heated according to the above.
  • the hot rolling is preferably performed in an operation of [recrystallization region rolling (rough rolling) - non-recrystallization region rolling (finish rolling)].
  • the rough rolling may be performed at 1000°C or higher, so that austenite may be completely recrystallized.
  • finish rolling may be performed in an austenite single phase region at a temperature directly above a no-recrystallization temperature (Tnr) or at a temperature within a range of Tnr to A3.
  • Tnr no-recrystallization temperature
  • the temperature directly above the Tnr may be expressed as a temperature range of greater than Tnr to Tnr+50°C.
  • Tnr and A3 temperatures may be obtained by the following formulas, where each element means a weight content.
  • Tnr 887 + 464 C + 6445 Nb ⁇ 644 ⁇ Nb + 732 V ⁇ 230 ⁇ V + 890 Ti + 363 Al ⁇ 357 Si
  • a 3 910 ⁇ 203 ⁇ C ⁇ 15.2 Ni + 44.7 Si + 104 V + 31.5 Mo ⁇ 30 Mn + 11 Cr + 20 Cu ⁇ 700 P ⁇ 400 Al ⁇ 400 Ti
  • the finish rolling may be completed in a temperature range of 820 to 900°C.
  • a residual rolling reduction immediately after the rough rolling is controlled to be 25 to 35%.
  • the residual rolling reduction is less than 25%, there is a problem that a rough rolling process is prolonged and productivity is lowered.
  • the residual rolling reduction ratio exceeds 35% there is a concern that sound rolling may not be achieved due to generation of a load on a rolling mill during finish rolling after rough rolling.
  • the residual rolling reduction refers to an amount of finish rolling remaining to the target thickness after rough rolling.
  • Cooling may be performed on a hot-rolled steel sheet obtained by completing the rolling process according to the above, and in this case, it is preferable to perform air cooling in order to realize a normalizing effect.
  • both excellent strength and toughness characteristics may be secured for ultra-thick steel having a thickness of 100 to 200 mm.
  • a steel plate manufactured by a conventional normalizing heat treatment has a carbon content higher than that of a TMCP steel material manufactured by control rolling + cooling, so that the steel material manufactured by the conventional normalizing heat treatment tends to have inferior impact toughness even after a heat treatment.
  • the heat treatment temperature is too high, or a time for the heat treatment is too long, the strength compared to the steel plate in a rolled state before the heat treatment may decrease due to grain growth.
  • the present disclosure proposes a manufacturing method capable of overcoming the disadvantages of the ultra-thick plate produced by the above-described process, and by optimizing rolling and cooling conditions for a slab having a specific alloy component system, an ultra-thick plate having excellent strength and low-temperature toughness characteristics may be provided.
  • a steel slab having alloy compositions shown in Table 1 was prepared.
  • a content of the alloy compositions is weight %, and a remainder thereof includes Fe and inevitable impurities.
  • the steel plates have a yield strength of 300 MPa or more, and an impact toughness of 200 J or more at -20°C, which has high strength and excellent low-temperature impact toughness.
  • Comparative Example 1 satisfying the alloy composition system proposed in the present disclosure but having an excessively high end temperature during finish rolling, coarse ferrite was formed, resulting in inferior strength and toughness.
  • FIG. 1 is a photograph of the microstructure of Inventive Example 3, and it can be confirmed that a composite structure with pearlite is formed with a fine ferrite phase as a main phase.

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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)
EP21906913.5A 2020-12-15 2021-11-25 Ultradicke stahlplatte mit hervorragender tieftemperaturschlagzähigkeit und verfahren zur herstellung davon Pending EP4265795A1 (de)

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Application Number Priority Date Filing Date Title
KR1020200175751A KR102498134B1 (ko) 2020-12-15 2020-12-15 저온 충격인성이 우수한 극후물 강판 및 이의 제조방법
PCT/KR2021/017472 WO2022131608A1 (ko) 2020-12-15 2021-11-25 저온 충격인성이 우수한 극후물 강판 및 이의 제조방법

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EP4265795A1 true EP4265795A1 (de) 2023-10-25

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JP3849244B2 (ja) * 1997-09-16 2006-11-22 Ｊｆｅスチール株式会社 繰返し大変形下での延性き裂進展抵抗の優れた鋼材及びその製造方法
JP4329583B2 (ja) * 2004-03-17 2009-09-09 Ｊｆｅスチール株式会社 耐震性に優れた低降伏比ｈ形鋼およびその製造方法
KR101417231B1 (ko) * 2011-12-28 2014-07-08 주식회사 포스코 저온인성 및 인장특성이 우수한 압력용기용 극후강판 및 그 제조 방법
KR101435258B1 (ko) 2012-06-28 2014-09-24 현대제철 주식회사 강재 제조 방법
JP5994819B2 (ja) * 2014-05-30 2016-09-21 新日鐵住金株式会社 耐衝撃性に優れた鋼板及びその製造方法
JP6007968B2 (ja) 2014-12-26 2016-10-19 新日鐵住金株式会社 高強度高延性厚板鋼板とその製造方法
KR102153170B1 (ko) * 2018-08-08 2020-10-26 주식회사 포스코 강도 및 dwtt 저온인성이 우수한 극후물 열연강판 및 그 제조방법

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KR20220085575A (ko) 2022-06-22
KR102498134B1 (ko) 2023-02-08
WO2022131608A1 (ko) 2022-06-23

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