EP3239328A1 - Stahlblech für den einsatz bei niedriger temperatur mit hervorragender oberflächenbearbeitungsqualität und verfahren zur herstellung davon - Google Patents

Stahlblech für den einsatz bei niedriger temperatur mit hervorragender oberflächenbearbeitungsqualität und verfahren zur herstellung davon Download PDF

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Publication number
EP3239328A1
EP3239328A1 EP15873529.0A EP15873529A EP3239328A1 EP 3239328 A1 EP3239328 A1 EP 3239328A1 EP 15873529 A EP15873529 A EP 15873529A EP 3239328 A1 EP3239328 A1 EP 3239328A1
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Prior art keywords
steel
surface processing
excellent surface
low temperature
austenite
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Granted
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EP15873529.0A
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English (en)
French (fr)
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EP3239328B1 (de
EP3239328A4 (de
Inventor
Soon-Gi Lee
In-Shik Suh
Yong-Jin Kim
Sang-Deok Kang
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Posco Holdings Inc
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Posco Co Ltd
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    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—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
    • 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
    • C22C38/001—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—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
    • 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
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present disclosure relates to steel for low temperature environments having excellent surface processing qualities and a method of manufacturing the same.
  • Steel used for storage containers containing liquefied natural gas, liquid nitrogen, or the like, and used for offshore platforms and facilities in polar regions may be provided as steel for low temperature environments maintaining sufficient toughness and strength even at extremely low temperatures.
  • Such steel for low temperature environments should have excellent low-temperature toughness, strength, and magnetic properties, as well as having relatively low coefficients of thermal expansion and thermal conductivity.
  • Patent Document 1 having excellent extreme low temperature properties through the addition of relatively large amounts of manganese (Mn) and carbon (C), with nickel (Ni) completely excluded, to stabilize austenite and including aluminum (Al) have been used.
  • Patent Document 2 having excellent low-temperature toughness in such a manner that a mixed structure of austenite and epsilon martensite is secured by adding Mn thereto has been used.
  • deformation behavior is implemented by slips and twin crystals in a manner different from general carbon steel.
  • deformation behavior is usually implemented by slips corresponding to uniform deformation, but twin crystals corresponding to nonuniform deformation are subsequently accompanied thereby.
  • size of grains is relatively large, stress required to form twin crystals is reduced, thereby easily generating twin crystals even in the case of a relatively low degree of deformation.
  • deformation of twin crystals occurs in coarse grains in the early stage of deformation, thereby causing nonuniform deformation.
  • An aspect of the present disclosure may provide steel for low temperature environments having excellent surface processing qualities and a method of manufacturing the same.
  • steel for low temperature environments having excellent surface processing qualities includes 15 wt% to 35 wt% of manganese (Mn), carbon (C) satisfying 23.6C+Mn ⁇ 28 and 33.5C-Mn ⁇ 23, 5 wt% or lower of copper (Cu) (excluding 0 wt%), chrome (Cr) satisfying 28.5C+4.4Cr ⁇ 57 (excluding 0 wt%), 0.01 wt% to 0.5 wt% of titanium (Ti), 0.003 wt% to 0.2 wt% of nitrogen (N), iron (Fe) as a residual component, and inevitable impurities.
  • Ti and N satisfy Relational Formula 1 below.
  • a method of manufacturing steel for low temperature environments having excellent surface processing qualities includes providing a slab including 15 wt% to 35 wt% of Mn, C satisfying 23.6C+Mn ⁇ 28 and 33.5C-Mn ⁇ 23, 5 wt% or lower of Cu (excluding 0 wt%), Cr satisfying 28.5C+4.4Cr ⁇ 57 (excluding 0 wt%), 0.01 wt% to 0.5 wt% of Ti, 0.003 wt% to 0.2 wt% of N, Fe as a residual component, and inevitable impurities, Ti and N satisfying Relational Formula 1 below; heating the slab at a temperature of 1050 °C to 1250 °C; and manufacturing heat-rolled steel by heat rolling the slab that has been heated.
  • 1.0 ⁇ Ti / N ⁇ 4.5 where Mn, C, Cr, Ti, and N in each expression refer to wt% of a content of each component.
  • steel for low temperature environments having excellent surface processing qualities even after being processed due to an austenite structure having uniform particle sizes and a method of manufacturing the same may be provided.
  • the inventors recognized that, in the case of steel having an austenite structure, containing a relatively large amount of carbon (C) and manganese (Mn), partial recrystallization and grain growth of the austenite structure occurs in a rolling temperature range of the related art, thereby generating abnormally coarse austenite; in general, critical stress required to form a twin crystal is higher than that of a slip, but in a case in which a size of a grain is relatively great for the reason described above, stress required to form the twin crystal is reduced, thereby causing deformation of the twin crystal in the early state of deformation, so that a problem in which surface quality may be degraded due to discontinuous deformation may occur. In addition, the inventors have conducted in-depth research to solve the problem described above.
  • Ti Ti
  • (Ti) -based precipitate is properly educed by adding Ti thereto, in order to suppress significant coarsening of an austenite grain and realized the present disclosure.
  • the steel for low temperature environments having excellent surface processing qualities includes 15 wt% to 35 wt% of manganese (Mn), carbon (C) satisfying 23.6C+Mn ⁇ 28 and 33.5C-Mn ⁇ 23, 5 wt% or lower of copper (Cu) (excluding 0 wt%), chrome (Cr) satisfying 28.5C+4.4Cr ⁇ 57 (excluding 0 wt%), 0.01 wt% to 0.5 wt% of titanium (Ti), 0.003 wt% to 0.2 wt% of nitrogen (N), iron (Fe) as a residual component, and inevitable impurities.
  • Ti and N satisfy Relational Formula 1 below. 1.0 ⁇ Ti / N ⁇ 4.5 , where Mn, C, Cr, Ti, and N in each expression refer to wt% of a content of each component.
  • Mn is an element playing a role in stabilizing austenite in an exemplary embodiment. 15% or more of Mn may be contained to stabilize an austenite phase at extremely low temperatures.
  • an Mn content is lower than 15%, when a C content is relatively low, metastable phase epsilon martensite is formed and easily transformed into ⁇ -martensite by strain induced transformation at extremely low temperatures, thereby not securing toughness.
  • the C content is increased to stabilize austenite to prevent the case described above, physical properties thereof may be dramatically degraded due to carbide precipitation.
  • the Mn content may be higher than or equal to 15%.
  • the Mn content may be limited to a range of 15% to 35%.
  • C is an element stabilizing austenite and increasing strength.
  • C plays a role in reducing Ms and M d , transformation points in which austenite is transformed into epsilon martensite or ⁇ -martensite by a cooling process or a process.
  • Ms and M d transformation points in which austenite is transformed into epsilon martensite or ⁇ -martensite by a cooling process or a process.
  • stability of austenite is insufficient, thereby not obtaining stable austenite at extremely low temperatures.
  • external stress causes strain induced transformation in which austenite is easily transformed into epsilon martensite or ⁇ -martensite, and toughness and the strength of steel is reduced.
  • the C content is significantly high, toughness is dramatically degraded due to carbide precipitation, and workability is degraded due to a significant increase in strength.
  • the C content in an exemplary embodiment may be decided in consideration of a relationship between C and other elements added thereto.
  • a relationship between C and Mn in forming a carbide that the inventor has discovered is illustrated in FIG. 3 .
  • the carbide is formed using C.
  • C does not independently affect formation of the carbide, but affects a tendency to form the carbide in combination with Mn.
  • FIG. 3 illustrates a proper C content.
  • a value of 23.6C+Mn in the case of C and Mn, a content of each component is expressed using wt%) may be controlled to be higher than or equal to 28.
  • the value refers to a leftward diagonal line in a hexagonal area in FIG. 3 .
  • stability of austenite is decreased, and strain induced transformation is generated by impacts at extremely low temperatures, thereby degrading impact toughness.
  • C may be added to satisfy an entirety of Mn: 15% to 35%, 23.6C+Mn ⁇ 28, and 33.5C-Mn ⁇ 23.
  • a lowermost limit of the C content is 0%, within a range satisfying the expression above.
  • Cu has significantly low solid solubility in the carbide and is relatively slow in spreading in austenite, thereby being concentrated in austenite and at an interface of a nucleated carbide. Thus, spreading of C is interrupted, thereby effectively slowing carbide growth. As a result, a generation of the carbide is suppressed.
  • Cu stabilizes austenite to improve extreme low-temperature toughness.
  • an uppermost limit may be limited to 5%.
  • the Cu content to obtain an effect of suppressing the carbide as described above may be higher than or equal to 0.5%.
  • Cr plays a role in improving impact toughness at low temperatures by stabilizing austenite and increasing the strength of steel through being solubilized in austenite within a range of a proper content thereof.
  • Cr is an element improving corrosion resistance of steel.
  • Cr is a carbide element.
  • Cr is also an element forming the carbide in an austenite grain boundary to reduce the impact of low-temperatures.
  • a Cr content in an exemplary embodiment may be determined in consideration of the relationship between C and other elements added thereto.
  • a value of 28.5C+4.4Cr (in the case of C and Cr, a content of each component is expressed using wt%) may be controlled to be lower than or equal to 57.
  • the value of 28.5C+4.4Cr is higher than 57, the generation of the carbide in the austenite grain boundary is difficult to suppress effectively, due to significant contents of Cr and C, thereby causing a problem in which impact toughness at low temperatures is degraded.
  • Cr may be added to satisfy 28.5C+4.4Cr ⁇ 57 in an exemplary embodiment.
  • Ti is an element forming a TiN precipitate in combination with nitrogen (N).
  • N nitrogen
  • a portion of the austenite grain may be significantly coarse.
  • growth of the austenite grain may be suppressed by properly educing TiN.
  • at least 0.01% or more of Ti is required to be added.
  • a Ti content is higher than 0.5%, an effect of growth of the austenite grain may not be improved anymore.
  • coarse TiN is educed, thereby reducing an effect of growth of the austenite grain.
  • the Ti content may be limited to a range of 0.01% to 0.5%.
  • N is required to be added simultaneously.
  • 0.003% or more of N may be added.
  • solid solubility of N is lower than or equal to 0.2%, an addition of 0.2% or greater of N is significantly difficult, and 0.2% or less thereof is sufficient to educe TiN, thereby limiting an uppermost limit thereof to 0.2%.
  • an N content may be limited to a range of 0.003% to 0.2% in an exemplary embodiment.
  • a residual component of an exemplary embodiment is Fe.
  • unintentional impurities may be inevitably mixed from a raw material or a surrounding environment, unintentional impurities are unavoidable. Since the impurities are known to those skilled in the manufacturing process of the related art, descriptions thereof will not be provided in detail in an exemplary embodiment.
  • a weight ratio of Ti to N may satisfy Relational Formula 1 below. 1.0 ⁇ Ti / N ⁇ 4.5
  • the Ti/N ratio is higher than 4.5
  • coarse TiN is crystallized in molten steel, thereby adversely affecting a property of steel and not obtaining uniform distribution of TiN.
  • surplus Ti that has not been educed to be TiN is present in a state of solid solution, thereby adversely affecting heat-affected zone toughness.
  • the Ti/N ratio is lower than 1.0, an amount of solute N in a base metal is increased, thereby adversely affecting heat-affected zone toughness.
  • the Ti/N ratio may be controlled to be 1.0 to 4.5.
  • the steel for low temperature environments according to an exemplary embodiment described above may include the TiN precipitate having a size of 0.01 ⁇ m to 0.3 ⁇ m.
  • the size of the TiN precipitate may be within a range of 0.01 ⁇ m to 0.3 ⁇ m.
  • the steel for low temperature environments may include the TiN precipitate in an amount of 1.0 ⁇ 10 7 to 1.0 ⁇ 10 10 per 1 mm 2 .
  • the TiN precipitate In a case in which the TiN precipitate is present in an amount less than 1.0 ⁇ 10 7 per 1 mm 2 , a grain pinning effect is insignificant, thereby not effectively suppressing growth of a coarse grain. On the other hand, in a case in which the TiN precipitate is present in an amount greater than 1.0 ⁇ 10 7 per 1 mm 2 , the size of the TiN precipitate becomes relatively small, so that the TiN precipitate may be unstable, and impact toughness of a material thereof may be degraded. Thus, the amount of the TiN precipitate may be 1.0 ⁇ 10 7 to 1.0 ⁇ 10 10 per 1 mm 2 .
  • the steel for low temperature environments limits the number of coarse austenite grains having a size of 200 ⁇ m or greater in the microstructure to 5 or less per 1 cm 2 .
  • the size thereof may be limited to 200 ⁇ m or greater.
  • the density of a grain having a size of 200 ⁇ m or greater may be limited to 5 or less per 1 cm 2 .
  • the steel for low temperature environments may include an austenite structure in an area fraction of 95% or higher.
  • Austenite a representative soft structure in which ductile fracture is generated even at low temperatures, is an essential microstructure to secure low-temperature toughness and should be included in an area fraction of 95% or higher.
  • austenite is not sufficient to secure low-temperature toughness, that is, impact toughness of 41 J or greater at a temperature of -196°C, so that a lowermost limit thereof may be limited to 95%.
  • the carbide present in the austenite grain boundary may be lower than or equal to 5% in an area fraction.
  • the carbide is a representative structure that may be present, beside austenite. The carbide is educed in an austenite grain boundary and becomes a cause of grain boundary rupture, thereby degrading low-temperature toughness and ductility. Thus, an uppermost limit thereof may be limited to 5%.
  • the method of manufacturing the steel for low temperature environments having excellent surface processing qualities includes providing a slab satisfying the alloy composition described above, heating the slab at a temperature of 1050°C to 1250°C, and manufacturing hot-rolled steel by hot rolling the slab that has been heated.
  • the slab satisfying the alloy composition described above is provided.
  • a reason for controlling the alloy composition is the same as described above.
  • the slab is heated at the temperature of 1050 °C to 1250°C.
  • a process described above is performed for the sake of solution and homogenization of a cast structure, segregation, and secondary phases generated in a process of manufacturing the slab.
  • the temperature is lower than 1050°C
  • homogenization thereof is insufficient or a temperature of a heating furnace is significantly low, thereby causing a problem in which deformation resistance is increased during heat rolling.
  • the temperature is higher than 1250°C
  • partial melting may occur and surface qualities may be degraded in segregation in the cast structure, and TiN may be crystallized, thereby not contributing to austenite refinement, but degrading properties thereof.
  • a heating temperature of the slab may be in a range of 1050°C to 1250°C.
  • the slab that has been heated is heat rolled, thereby manufacturing the hot-rolled steel.
  • the alloy composition and the heating temperature of the slab, described above, may be satisfied, thereby manufacturing the steel for low temperature environments having excellent surface processing qualities.
  • it is not necessary to control a condition of the manufacturing hot-rolled steel and the manufacturing hot-rolled steel may be performed using a general method.
  • Inventive Examples 1 to 5 it can be confirmed that a component system and a composition range controlled in an exemplary embodiment are satisfied, and high-quality steel for low temperature environments without uneven surfaces may be obtained in such a manner that a density of a coarse austenite grain is controlled to be 5 or less per 1 cm 2 by minute eduction of TiN, and Inventive Examples 1 to 5 are processed.
  • stable austenite in which fraction of austenite in the microstructure is controlled to be 95% or higher, and fraction of the carbide is controlled to be lower than 5% may be obtained, thereby securing excellent toughness at extremely low temperatures.
  • Comparative Examples 1 to 3 it can be confirmed that TiN may not be educed, since Ti is not added thereto, thereby generating a coarse grain and unevenness of surfaces after Comparative Examples 1 to 3 are processed.
  • Comparative Example 4 it can be confirmed that, since the component system and the composition range controlled in an exemplary embodiment are not satisfied, ferrite is generated, thereby significantly degrading impact toughness. In addition, it can be confirmed that, since a size and the number of TiN controlled in an exemplary embodiment are not satisfied, the number of coarse grains is increased, thereby generating unevenness of surfaces.
  • FIG. 1A is an image of the microstructure of steel of the related art in which a nonideal coarse grain is formed by coarsening of the austenite grain.
  • FIG. 1B is an image of unevenness occurring on a surface of steel after steel of FIG. 1A is tensioned. As such, it can be confirmed that, in a case in which the austenite grain is coarsened to generate the nonideal coarse grain in the microstructure of steel, surface qualities are degraded after a process thereof as described in FIG. 1B .
  • FIG. 2 illustrating an image of the microstructure of Inventive Examples, uniform grains without a nonideal coarse austenite grain is formed, thereby generating excellent surface processing qualities even after the process thereof.

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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)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
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EP15873529.0A 2014-12-24 2015-12-11 Stahlblech für den einsatz bei niedriger temperatur mit hervorragender oberflächenbearbeitungsqualität und verfahren zur herstellung davon Active EP3239328B1 (de)

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KR1020140189137A KR101665821B1 (ko) 2014-12-24 2014-12-24 표면 가공 품질이 우수한 저온용 강판 및 그 제조방법
PCT/KR2015/013554 WO2016105002A1 (ko) 2014-12-24 2015-12-11 표면 가공 품질이 우수한 저온용 강판 및 그 제조방법

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EP3239328B1 EP3239328B1 (de) 2021-11-17

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Cited By (1)

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EP3699313A4 (de) * 2017-10-18 2020-08-26 Posco Manganstahl für tieftemperaturen mit ausgezeichneter oberflächenqualität und verfahren zu seiner herstellung

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BR112019022088A2 (pt) * 2017-04-26 2020-05-05 Jfe Steel Corp aço alto mn e método de produção do mesmo
CN107190201B (zh) * 2017-07-17 2019-03-26 武汉钢铁有限公司 液化石油气运输船用钢及制造方法
EP3679594A4 (de) 2017-09-07 2021-06-02 Monash University Kapazitive energiespeichervorrichtung und verfahren zu ihrer herstellung
KR102031455B1 (ko) 2017-12-26 2019-10-11 주식회사 포스코 저온인성이 우수한 열연강판, 강관 및 그 제조방법
EP3594374A4 (de) * 2018-03-29 2020-06-10 Nippon Steel Corporation Austenitisches abriebfestes stahlblech
KR102255827B1 (ko) * 2018-10-25 2021-05-26 주식회사 포스코 표면품질이 우수한 극저온용 오스테나이트계 고망간 강재 및 그 제조방법

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KR970001324B1 (ko) * 1994-03-25 1997-02-05 김만제 열간가공성이 우수한 고망간강 및 그 열간압연 방법
JPH09195007A (ja) * 1996-01-19 1997-07-29 Kawasaki Steel Corp 耐食性に優れたＣｒ−Ｍｎ−Ｎ系オーステナイトステンレス鋼
JP4141557B2 (ja) * 1998-12-18 2008-08-27 松下電器産業株式会社 電子部品の実装装置および実装方法
EP1444373B1 (de) * 2001-11-16 2007-09-12 Posco Stahlplatte mit überlegener zähigkeit in der von der schweisshitze beeinflussten zone und verfahren zu ihrer herstellung; schweisskonstruktion unter verwendung davon
JP4529872B2 (ja) 2005-11-04 2010-08-25 住友金属工業株式会社 高Ｍｎ鋼材及びその製造方法
KR20120097160A (ko) * 2011-02-24 2012-09-03 현대제철 주식회사 고장력 강판 및 그 제조 방법
KR101461736B1 (ko) * 2012-12-21 2014-11-14 주식회사 포스코 피삭성 및 용접 열영향부 극저온 인성이 우수한 오스테나이트계 강재 및 그의 제조방법
KR101353843B1 (ko) * 2011-12-27 2014-01-20 주식회사 포스코 용접 열영향부 극저온 인성이 우수한 오스테나이트 강재
WO2013100614A1 (ko) * 2011-12-27 2013-07-04 주식회사 포스코 피삭성 및 용접 열영향부 극저온 인성이 우수한 오스테나이트계 강재 및 그의 제조방법
US20140356220A1 (en) * 2011-12-28 2014-12-04 Posco Wear resistant austenitic steel having superior machinability and ductility, and method for producing same
KR101412259B1 (ko) * 2012-03-29 2014-07-02 현대제철 주식회사 강판 및 그 제조 방법
KR101412327B1 (ko) * 2012-06-28 2014-06-25 현대제철 주식회사 각관용 열연강판 및 그 제조 방법
WO2014104706A1 (ko) * 2012-12-26 2014-07-03 주식회사 포스코 용접열영향부 인성이 우수한 고강도 오스테나이트계 강재 및 그 제조방법

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3699313A4 (de) * 2017-10-18 2020-08-26 Posco Manganstahl für tieftemperaturen mit ausgezeichneter oberflächenqualität und verfahren zu seiner herstellung
EP3974556A1 (de) * 2017-10-18 2022-03-30 Posco Manganstahl für tieftemperaturen mit ausgezeichneter oberflächenqualität

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WO2016105002A1 (ko) 2016-06-30
JP2018503742A (ja) 2018-02-08
US20170362675A1 (en) 2017-12-21
EP3239328B1 (de) 2021-11-17
JP6810691B2 (ja) 2021-01-06
JP6764510B2 (ja) 2020-09-30
KR20160078853A (ko) 2016-07-05
KR101665821B1 (ko) 2016-10-13
JP2020002465A (ja) 2020-01-09
CN107109602B (zh) 2022-02-25
EP3239328A4 (de) 2017-12-13
CN107109602A (zh) 2017-08-29
CA2970151A1 (en) 2016-06-30
CA2970151C (en) 2021-01-19
WO2016105002A8 (ko) 2016-12-15

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