WO2015099363A1 - 표면 가공 품질이 우수한 저온용강 - Google Patents

표면 가공 품질이 우수한 저온용강 Download PDF

Info

Publication number
WO2015099363A1
WO2015099363A1 PCT/KR2014/012601 KR2014012601W WO2015099363A1 WO 2015099363 A1 WO2015099363 A1 WO 2015099363A1 KR 2014012601 W KR2014012601 W KR 2014012601W WO 2015099363 A1 WO2015099363 A1 WO 2015099363A1
Authority
WO
WIPO (PCT)
Prior art keywords
weight
steel
less
austenite
low
Prior art date
Application number
PCT/KR2014/012601
Other languages
English (en)
French (fr)
Korean (ko)
Other versions
WO2015099363A8 (ko
Inventor
이순기
서인식
이학철
박인규
Original Assignee
주식회사 포스코
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Priority to CN201480070844.1A priority Critical patent/CN105849302B/zh
Priority to EP14873409.8A priority patent/EP3088555A4/en
Priority to CN201811116893.0A priority patent/CN109266959B/zh
Priority to JP2016560327A priority patent/JP6615773B2/ja
Priority to US15/102,662 priority patent/US20160319407A1/en
Publication of WO2015099363A1 publication Critical patent/WO2015099363A1/ko
Publication of WO2015099363A8 publication Critical patent/WO2015099363A8/ko

Links

Images

Classifications

    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • 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
    • 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
    • C22C38/06—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
    • C22C38/20—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to low temperature molten steel with excellent surface finish quality. More particularly, the present invention relates to low temperature molten steel with excellent surface quality after machining, which can be used at a wide range of temperatures from low temperature to room temperature, such as liquefied gas storage tanks and transportation facilities. .
  • Steels used for storage vessels such as liquefied natural gas and liquid nitrogen, marine structures and polar structures should be low temperature molten steel that maintains sufficient toughness and strength even at cryogenic temperatures.
  • Such low-temperature molten steel should have low thermal expansion and thermal conductivity as well as excellent low-temperature toughness and strength, and magnetic properties are also a problem.
  • Cr-Ni-based stainless steel such as AISI304, 9% Ni steel, and 5000-series aluminum alloy have been used.
  • the cost of the material is high and the design strength of the structure is increased due to the low strength, and there is a problem in that the use is limited due to poor weldability.
  • Cr-Ni-based stainless steel and 9% Ni steel, etc. require expensive nickel content and heat treatment to increase manufacturing costs, and welding materials also contain a large amount of expensive nickel, which has been a problem in a wide range of applications.
  • Patent Document 1 (Republic of Korea Patent Publication No. 1998-0058369) and Patent Document 2 (International Publication No. WO2007-080646) are described as technologies for reducing expensive nickel content and adding manganese, chromium, etc. instead. Can be.
  • the patent document 1 is a technology to improve the cryogenic toughness by reducing the nickel content to 1.5 ⁇ 4%, and instead of adding manganese, chromium 16 ⁇ 22%, 2 ⁇ 5.5% to secure austenite structure, Patent Document 2 It reduces the nickel content to about 5.5% and adds manganese and chromium below 2.0% and 1.5%, respectively, to make the ferrite grains fine through repeated heat treatment and tempering to secure cryogenic toughness.
  • Patent Documents 1 and 2 still contain expensive nickel, and in order to secure cryogenic toughness, the repetitive heat treatment and tempering are performed at various stages, and thus are not advantageous in terms of cost or simplification of the process.
  • Patent Document 3 U.S. Patent No. 4257808 adds 5% manganese instead of 9% nickel and refines the crystal grains through four iterative heat treatments in an ideal temperature range where austenite and ferrite coexist. It is a technology that improves cryogenic toughness by tempering after.
  • Patent Document 4 Korean Patent Laid-Open Publication No.
  • the present invention is to provide a low-temperature molten steel having excellent surface processing quality even after processing such as tensile and bending.
  • the present invention is manganese (Mn): 15 to 35% by weight, carbon (C): a range satisfying the conditions of 23.6C + Mn ⁇ 28 and 33.5C-Mn ⁇ 23, copper (Cu): 5% by weight or less (0 % By weight), nitrogen (N): 1% by weight or less (except 0% by weight), chromium (Cr): 28.5C + 4.4Cr ⁇ 57, satisfying the condition, nickel (Ni): 5% by weight Molybdenum (Mo): 5 wt% or less, Silicon (Si): 4 wt% or less, aluminum (Al): 5 wt% or less, including the remaining iron (Fe) and other unavoidable impurities, It is achieved by the low temperature molten steel which is excellent in the quality of the surface processing which the lamination defect energy (SFE) calculated
  • required is 24 mJ / m ⁇ 2> or more.
  • the present invention increases the stacking fault energy by adjusting the composition and composition range of the steel, it can provide a steel with excellent surface processing quality irrespective of non-ideal coarse grains formed in the steel. have.
  • FIG. 1 is a photograph of a microstructure of a conventional steel material in which austenite grains are coarsened to form non-ideal coarse grains.
  • Figure 2 is a photograph taken after pulling the conventional steel of Figure 1 is a photograph showing that the surface of the steel is non-uniform.
  • FIG. 3 is a photograph of the microstructure of the steel of an embodiment of the present invention in which the austenite grains are coarsened to form non-ideal coarse grains.
  • Figure 4 is a photograph taken after pulling the steel of the embodiment of the present invention of Figure 3 is a photograph showing that the surface is uniform.
  • 5 is a graph showing the range of carbon and manganese controlled by the present invention.
  • the present invention relates to a low-temperature molten steel having excellent surface processing quality even after a processing process such as tension and bending, regardless of whether non-ideally coarse grains are formed inside the steel, and a manufacturing method thereof.
  • the deformation behavior is usually caused by slip and twin, unlike ordinary carbon steel, and the initial deformation is mainly caused by slip, which is uniformly deformed. do.
  • the stress required to generate twins is the main parameter of stacking defect energy and grain size, which are functions of additive elements. In particular, the larger the grain size, the less stress is required to form twins, and twins are easily generated even under small deformation. If a few coarse grains are present in the microstructure, twin strains occur at the initial coarse grains, resulting in non-uniform deformations, resulting in inferior surface properties of the material, causing uneven thickness of the final structure.
  • steels containing a large amount of carbon and manganese may cause partial recrystallization and grain growth of the austenite structure in the usual rolling temperature range, resulting in non-ideal coarse austenite.
  • the critical stress required for twin formation is higher than that of slip, but when the grain is large for the same reason, the stress required for twin formation decreases and twin deformation occurs at the initial stage of deformation, resulting in surface quality deterioration due to discontinuous deformation.
  • the formation of strain twins can be suppressed by increasing the critical stress required for strain twins.
  • the low-temperature molten steel having excellent surface finish quality of the present invention is manganese (Mn): 15 to 35% by weight, carbon (C): 23.6C + Mn ⁇ 28 and 33.5C-Mn ⁇ 23, copper (Cu ): 5% by weight or less (excluding 0% by weight), nitrogen (N): 1% by weight or less (excluding 0% by weight), chromium (Cr): 28.5C + 4.4Cr ⁇ 57 Nickel (Ni): 5 wt% or less, Molybdenum (Mo): 5 wt% or less, Silicon (Si): 4 wt% or less, Aluminum (Al): 5 wt% or less, remaining iron (Fe) and other unavoidable impurities It should not be included, and the stacking fault energy (SFE) as determined from the relational expression 1 is more than 24mJ / m 2.
  • SFE stacking fault energy
  • Equation 1 is a relational expression indicating a change in stacking fault energy according to the content of the alloying element added, and is a relational expression derived from a calculated value based on the existing theory and various experiments of the present inventors.
  • FIG. 3 shows a photograph of the microstructure of the steel of an embodiment of the present invention that satisfies the above-described composition range and the condition of Equation 1, and FIG. 1 shows a photograph of the microstructure of a conventional steel. . 1 and 3 it can be seen that the microstructure has non-ideally coarse grains formed.
  • Figure 2 is a photograph of the surface of the steel after pulling the steel having a microstructure of Figure 1 which is a conventional steel, it can be seen that the non-uniformity occurred.
  • FIG. 3 which is an embodiment of the present invention
  • FIG. 4 which photographs the surface of the steel
  • the microstructure differs from FIG. 2 even though non-ideal coarse grains are formed. It can be confirmed that no nonuniformity has occurred.
  • the critical stress required for twin generation is higher than that of slip, but as can be seen from Equation 2, as the grain size becomes coarse, the stress generated by twins decreases. Since twins are generated locally in the grains, the deterioration of surface quality is caused by discontinuous deformation.
  • Manganese is an element that serves to stabilize austenite in the present invention.
  • it in order to stabilize the austenite phase at cryogenic temperature, it is preferably included 15 wt% or more. That is, when the content of manganese is less than 15% by weight, when the carbon content is small, metastable epsilon martensite is formed, and since it is easily transformed into alpha martensite by processing organic transformation at cryogenic temperature, toughness cannot be secured.
  • the content of manganese is preferably at least 15% by weight.
  • the content of manganese exceeds 35% by weight, there is a problem in that the corrosion rate of the steel is lowered and the economy decreases due to the increased content. Therefore, the content of manganese is preferably limited to 15 to 35% by weight.
  • Carbon (C) Satisfies the conditions of 23.6C + Mn ⁇ 28 and 33.5C-Mn ⁇ 23
  • Carbon is an element that stabilizes austenite and increases strength, and in particular, serves to lower M s and M d , which are transformation points from austenite to epsilon or alpha martensite by cooling or processing. Therefore, when carbon is added inadequately, the austenite stability is insufficient to obtain austenite stable at cryogenic temperatures, and it is easy to cause processing organic transformation into epsilon or alpha martensite due to external stress, thereby reducing toughness. In addition, when the carbon content is excessively reduced, toughness is rapidly deteriorated due to carbide precipitation, and the workability is deteriorated due to excessive increase in strength.
  • the content of carbon in the present invention is preferably determined by paying attention to the relationship between carbon and other elements added together, and for this purpose, the relationship between carbon and manganese for carbide formation found by the present inventor is shown in FIG. 5. .
  • carbides are, of course, formed by carbon, but carbon does not independently affect the formation of carbides, but rather acts in combination with manganese to affect its formation tendency.
  • the appropriate carbon content is shown in the figure.
  • the value of 23.6C + Mn (C and Mn represent the content of each component in weight% unit) to 28 or more, provided that the other components meet the range defined by the present invention. It is desirable to. This means the inclined left boundary of the parallelogram region of the figure.
  • Copper is concentrated at the austenite and nucleated carbide interface due to its very low solubility in carbides and slow diffusion in austenite, which effectively slows carbide growth by interfering with the diffusion of carbon and eventually inhibits carbide formation.
  • carbide precipitation can be suppressed through accelerated cooling during the manufacturing process, but the welding heat affected zone is not easy to control the cooling rate, and thus, in the present invention, copper, which is a very effective element for suppressing carbide precipitation, is added.
  • copper has an effect of stabilizing austenite to improve cryogenic toughness.
  • the upper limit is preferably limited to 5% by weight.
  • the content of copper for obtaining the above-mentioned carbide suppression effect it is more preferable that it is 0.5 weight% or more.
  • nitrogen is an element that stabilizes austenite to improve toughness, and is particularly advantageous for improving strength through solid solution strengthening such as carbon.
  • Equation 1 it is well known as an element that promotes slippage by increasing stacking defect energy effectively.
  • the stress required for twinning is more than the stress value corresponding to the processing amount of ordinary steel, and coarse nitride is formed to deteriorate the surface quality and physical properties of the steel. Therefore, it is preferable to limit an upper limit to 1 weight%.
  • the austenitic steel of the present invention may include Cr, Ni, Mo, Si, Al.
  • Chromium stabilizes austenite up to the range of an appropriate amount of addition, thereby improving impact toughness at low temperatures, and solid-solution in austenite increases the strength of steel. Chromium is also an element that improves the corrosion resistance of steels.
  • chromium is a carbide element, in particular, an element that reduces carbide impact by forming carbide at the austenite grain boundary. Therefore, the content of chromium added in the present invention is preferably determined by paying attention to the relationship with carbon and other elements added together, in order to prevent carbide formation, on the premise that other components meet the range defined in the present invention. It is preferable to control the value of 28.5C + 4.4Cr (C, Cr is the content of each component by weight% unit) under 57.
  • chromium is preferably added so as to satisfy 28.5C + 4.4Cr ⁇ 57.
  • Nickel is an effective austenite stabilizing element and lowers M s and M d , which are transformation points of austenite to epsilon or alpha martensite by cooling or processing, thereby improving the toughness of steel.
  • M s and M d transformation points of austenite to epsilon or alpha martensite by cooling or processing, thereby improving the toughness of steel.
  • Equation 1 it is well known as an element that promotes slippage by increasing stack defect energy very effectively.
  • the stress necessary for twin generation is unnecessary because it exceeds the stress value corresponding to the processing amount of ordinary steel, and because it is an expensive element, the economical efficiency decreases. It is preferable to limit to 5% by weight.
  • Molybdenum is an element that stabilizes austenite in the range of proper addition and lowers M s and M d , which are transformation points of austenite to epsilon or alpha martensite by cooling or processing, and improves toughness of steel.
  • M s and M d transformation points of austenite to epsilon or alpha martensite by cooling or processing, and improves toughness of steel.
  • it is an element that is dissolved in the steel material to increase the strength, in particular, segregated in the austenite grain boundary to increase the stability of the grain boundary to reduce the energy, it is an element that serves to suppress the precipitation of the grain boundary of the carbonitride.
  • Equation 1 it is well known as an element that promotes slippage by increasing stacking defect energy effectively.
  • the upper limit is preferably limited to 5% by weight.
  • Silicon is an element that improves the castability of molten steel and, in particular, when added to an austenitic steel, is dissolved in the steel to effectively increase the strength.
  • the upper limit is preferably limited to 4% by weight.
  • Aluminum is an element that stabilizes austenite in the range of proper addition and lowers M s and M d , which are transformation points from austenite to epsilon or alpha martensite by cooling or processing, thereby improving the toughness of steel.
  • M s and M d are transformation points from austenite to epsilon or alpha martensite by cooling or processing, thereby improving the toughness of steel.
  • it is an element that increases strength by being dissolved in steel, and particularly, it affects the activity of carbon in steel and effectively suppresses carbide formation to increase toughness.
  • Equation 1 it is well known as an element that promotes slippage by increasing stacking defect energy effectively.
  • the stress required for twin generation is not necessary because it exceeds the stress value corresponding to the processing amount of ordinary steel, and it is inferior to castability and surface quality of steel through the formation of oxide and nitride. Therefore, it is preferable to limit an upper limit to 5 weight%.
  • the remaining components of the present invention are iron (Fe) and other unavoidable impurities.
  • iron Fe
  • impurities that are not intended from the raw material or the surrounding environment may be inevitably mixed, and thus cannot be excluded. Since these impurities are known to those skilled in the art of ordinary steel manufacturing, not all of them are specifically mentioned herein.
  • the low-temperature molten steel preferably contains at least 95% of the austenite structure as an area fraction.
  • Austenitic a representative soft tissue that exhibits soft fracture even at low temperatures, is an essential microstructure for securing low temperature toughness, and it is preferable to include 95% or more as an area fraction, and when it is less than 95%, sufficient low temperature toughness, that is, impact of 41J or more at -196 ° C.
  • the lower limit is preferably 95% because it is not sufficient to secure toughness.
  • the carbide present in the austenite grain boundary is preferably 5% or less in area fraction.
  • Twin-stressing stress of the low-temperature molten steel is preferably more than the tensile stress corresponding to 5% of the tensile strain of the low-temperature molten steel.
  • the twin stress generated means the value calculated by Equation 2 above
  • the tensile strain means that the tensile strain occurs 5% when uniaxially tensioned during the tensile test.
  • the amount of deformation given when forming a plate for manufacturing low-temperature structures such as a low temperature container is a tensile deformation, which is mostly within 5% in terms of tension, so that the twinning stress for suppressing non-uniform deformation is a tension corresponding to 5% of deformation in uniaxial tension. It is desirable to limit it to stress or more.
  • the present invention Preparing a steel slab having a steel composition of the present invention and having a stacking defect energy (SFE) of 24 mJ / m 2 or more obtained by Equation 1; Heating the slab to 1050-1250 ° C .; And a hot rolling step of finishing rolling the heated slab at 700 to 950 ° C.
  • SFE stacking defect energy
  • a steel slab having a stacking defect energy (SFE) of 24 mJ / m 2 or more obtained by the above-described alloy composition and relational formula 1 is prepared.
  • the heating temperature is preferably 1050 ⁇ 1250 °C. This is for the solidification and homogenization of the cast structure, segregation, and secondary phases produced in the slab manufacturing step. If the temperature is less than 1050 ° C, the homogenization is insufficient or the furnace temperature is too low, resulting in a large deformation resistance during hot rolling. If exceeded, partial melting in the segregation zone in the cast tissue and deterioration of the surface quality may occur. Therefore, the reheating temperature of the slab preferably has a range of 1050 ⁇ 1250 °C.
  • the hot rolling is preferably carried out so that the finish rolling temperature is 700 ⁇ 950 °C, when the finish rolling temperature is less than 700 °C carbide is precipitated at the austenite grain boundary to reduce the elongation and low temperature toughness Anisotropy may occur and anisotropy of mechanical properties may occur.
  • the finish rolling temperature exceeds 950 ° C., the austenite grains are coarsened and the strength and elongation are lowered, which is not preferable, so the finish rolling temperature is preferably in the range of 700 ⁇ 950 ° C.
  • the inventive steels 1 to 8 can obtain excellent steel materials without surface irregularities by satisfying the lamination defect energy of 24 mJ / m 2 or more according to Equation 1.
  • the stacking defect energy exceeds the range of Equation 1, but it can be seen that surface nonuniformity occurs even though excellent cryogenic toughness is obtained.
  • Comparative Examples 4 and 6 can be confirmed that the cryogenic toughness is lowered because the content of carbon and manganese does not fall within the component range of the present invention and thus does not obtain a target austenite fraction. It can be seen that the surface unevenness does not fall within the range of Equation 1.
  • Comparative Examples 5 and 7 do not satisfy the component range controlled by the present invention, it can be seen that the impact toughness is inferior, in particular, excessive addition of carbon generates an excessive fraction of carbide at the austenite grain boundary impact impact toughness It is eager.
  • the comparative example 8 does not satisfy the component range of this invention of this invention, even if lamination defect energy exceeded 24mJ / m ⁇ 2> , the surface nonuniformity generate
  • the elongation and impact toughness were inferior due to the anisotropy and high strength of the physical properties due to the lower rolling finish temperature.
PCT/KR2014/012601 2013-12-25 2014-12-19 표면 가공 품질이 우수한 저온용강 WO2015099363A1 (ko)

Priority Applications (5)

Application Number Priority Date Filing Date Title
CN201480070844.1A CN105849302B (zh) 2013-12-25 2014-12-19 表面加工品质优异的低温用钢
EP14873409.8A EP3088555A4 (en) 2013-12-25 2014-12-19 Steel for low-temperature service having excellent surface processing quality
CN201811116893.0A CN109266959B (zh) 2013-12-25 2014-12-19 表面加工品质优异的低温用钢
JP2016560327A JP6615773B2 (ja) 2013-12-25 2014-12-19 表面加工品質に優れた低温用鋼
US15/102,662 US20160319407A1 (en) 2013-12-25 2014-12-19 Steel for low-temperature service having excellent surface processing quality

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020130163369A KR101543916B1 (ko) 2013-12-25 2013-12-25 표면 가공 품질이 우수한 저온용강 및 그 제조 방법
KR10-2013-0163369 2013-12-25

Publications (2)

Publication Number Publication Date
WO2015099363A1 true WO2015099363A1 (ko) 2015-07-02
WO2015099363A8 WO2015099363A8 (ko) 2015-09-17

Family

ID=53479151

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/KR2014/012601 WO2015099363A1 (ko) 2013-12-25 2014-12-19 표면 가공 품질이 우수한 저온용강

Country Status (6)

Country Link
US (1) US20160319407A1 (zh)
EP (1) EP3088555A4 (zh)
JP (1) JP6615773B2 (zh)
KR (1) KR101543916B1 (zh)
CN (2) CN109266959B (zh)
WO (1) WO2015099363A1 (zh)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3392362A4 (en) * 2015-12-18 2018-10-24 Posco Wear resistant steel material excellent in toughness and internal quality, and method for manufacturing same
JP2019505675A (ja) * 2015-12-22 2019-02-28 ポスコＰｏｓｃｏ 耐水素脆化性に優れたオーステナイト系鋼材
CN114480980A (zh) * 2021-12-29 2022-05-13 中国铁路设计集团有限公司 一种铬铜合金化耐候型孪生诱发塑性钢及其制备方法
US11505853B2 (en) * 2016-12-22 2022-11-22 Posco High manganese steel having superior low-temperature toughness and yield strength and manufacturing method thereof

Families Citing this family (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6645103B2 (ja) * 2014-10-22 2020-02-12 日本製鉄株式会社 高Ｍｎ鋼材及びその製造方法
JP6589535B2 (ja) * 2015-10-06 2019-10-16 日本製鉄株式会社 低温用厚鋼板及びその製造方法
WO2018104984A1 (ja) * 2016-12-08 2018-06-14 Ｊｆｅスチール株式会社 高Ｍｎ鋼板およびその製造方法
KR101917473B1 (ko) 2016-12-23 2018-11-09 주식회사 포스코 내마모성과 인성이 우수한 오스테나이트계 강재 및 그 제조방법
CN110573642A (zh) * 2017-04-26 2019-12-13 杰富意钢铁株式会社 高Mn钢及其制造方法
KR102109270B1 (ko) * 2017-10-18 2020-05-12 주식회사 포스코 표면품질이 우수한 저온용 고 망간강재 및 제조방법
US20210164067A1 (en) * 2017-12-07 2021-06-03 Jfe Steel Corporation High-mn steel and method for manufacturing same
KR102020381B1 (ko) * 2017-12-22 2019-09-10 주식회사 포스코 내마모성이 우수한 강재 및 그 제조방법
WO2019156179A1 (ja) * 2018-02-07 2019-08-15 Ｊｆｅスチール株式会社 高Ｍｎ鋼およびその製造方法
KR102004654B1 (ko) * 2018-03-23 2019-07-26 서울과학기술대학교 산학협력단 극저온 인성이 우수한 알루미늄 첨가 오스테나이트계 경량 고망간강 및 그의 제조방법
US20190382875A1 (en) * 2018-06-14 2019-12-19 The Nanosteel Company, Inc. High Strength Steel Alloys With Ductility Characteristics
MY192988A (en) * 2018-08-03 2022-09-20 Jfe Steel Corp High-mn steel and method for producing same
WO2020035917A1 (ja) * 2018-08-15 2020-02-20 Ｊｆｅスチール株式会社 鋼板およびその製造方法
KR102255827B1 (ko) * 2018-10-25 2021-05-26 주식회사 포스코 표면품질이 우수한 극저온용 오스테나이트계 고망간 강재 및 그 제조방법
WO2020152498A1 (fr) * 2019-01-22 2020-07-30 Aperam Alliage fer-manganèse à soudabilité améliorée

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4257808A (en) 1979-08-13 1981-03-24 The United States Of America As Represented By The United States Department Of Energy Low Mn alloy steel for cryogenic service and method of preparation
JPH0941087A (ja) * 1995-05-22 1997-02-10 Kobe Steel Ltd 極低温用高Ｍｎ非磁性鋼及び製造方法
KR970043149A (ko) 1995-12-11 1997-07-26 김종진 저온인성이 우수한 고강도 페라이트계 망간강의 제조방법
KR19980058369A (ko) 1996-12-30 1998-09-25 서춘화 극저온 충격특수성이 우수한 고망간강 및 그 제조방법
WO2007080646A1 (ja) 2006-01-13 2007-07-19 Sumitomo Metal Industries, Ltd. 極低温用鋼
KR20110075610A (ko) * 2009-12-28 2011-07-06 주식회사 포스코 연성이 우수한 강재
JP2011246817A (ja) * 2003-07-22 2011-12-08 Arcelormittal France 強度を高められ、靱性に優れ、低温での成形に適した、鉄・炭素・マンガンのオーステナイト鋼板の製造方法並びにそのようにして製造された鋼板
KR20130075565A (ko) * 2011-12-27 2013-07-05 주식회사 포스코 용접 열영향부 극저온 인성이 우수한 오스테나이트 강재

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5896853A (ja) * 1981-11-17 1983-06-09 Sumitomo Metal Ind Ltd 耐食性および機械加工性に優れた極低温用高Ｍｎ鋼
JPS58197256A (ja) * 1982-05-12 1983-11-16 Kawasaki Steel Corp 耐候性および耐銹性にすぐれる高靭性高Ｍｎ鋼
JPH0742549B2 (ja) * 1990-09-28 1995-05-10 新日本製鐵株式会社 リニアモーターカー鋼橋用高Ｍｎ非磁性鋼
FR2878257B1 (fr) * 2004-11-24 2007-01-12 Usinor Sa Procede de fabrication de toles d'acier austenitique, fer-carbone-manganese a tres hautes caracteristiques de resistance et d'allongement, et excellente homogeneite
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
KR20120065464A (ko) * 2010-12-13 2012-06-21 주식회사 포스코 항복비 및 연성이 우수한 오스테나이트계 경량 고강도 강판 및 그의 제조방법
JP6078554B2 (ja) * 2011-12-27 2017-02-08 ポスコＰｏｓｃｏ 被削性及び溶接熱影響部における極低温靱性に優れたオーステナイト系鋼材及びその製造方法
WO2013100612A1 (ko) * 2011-12-28 2013-07-04 주식회사 포스코 피삭성 및 용접 열영향부 인성이 우수한 내마모 오스테나이트계 강재 및 그의 제조방법

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4257808A (en) 1979-08-13 1981-03-24 The United States Of America As Represented By The United States Department Of Energy Low Mn alloy steel for cryogenic service and method of preparation
JPH0941087A (ja) * 1995-05-22 1997-02-10 Kobe Steel Ltd 極低温用高Ｍｎ非磁性鋼及び製造方法
KR970043149A (ko) 1995-12-11 1997-07-26 김종진 저온인성이 우수한 고강도 페라이트계 망간강의 제조방법
KR19980058369A (ko) 1996-12-30 1998-09-25 서춘화 극저온 충격특수성이 우수한 고망간강 및 그 제조방법
JP2011246817A (ja) * 2003-07-22 2011-12-08 Arcelormittal France 強度を高められ、靱性に優れ、低温での成形に適した、鉄・炭素・マンガンのオーステナイト鋼板の製造方法並びにそのようにして製造された鋼板
WO2007080646A1 (ja) 2006-01-13 2007-07-19 Sumitomo Metal Industries, Ltd. 極低温用鋼
KR20110075610A (ko) * 2009-12-28 2011-07-06 주식회사 포스코 연성이 우수한 강재
KR20130075565A (ko) * 2011-12-27 2013-07-05 주식회사 포스코 용접 열영향부 극저온 인성이 우수한 오스테나이트 강재

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP3088555A4

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3392362A4 (en) * 2015-12-18 2018-10-24 Posco Wear resistant steel material excellent in toughness and internal quality, and method for manufacturing same
JP2019505675A (ja) * 2015-12-22 2019-02-28 ポスコＰｏｓｃｏ 耐水素脆化性に優れたオーステナイト系鋼材
US11505853B2 (en) * 2016-12-22 2022-11-22 Posco High manganese steel having superior low-temperature toughness and yield strength and manufacturing method thereof
CN114480980A (zh) * 2021-12-29 2022-05-13 中国铁路设计集团有限公司 一种铬铜合金化耐候型孪生诱发塑性钢及其制备方法
CN114480980B (zh) * 2021-12-29 2023-09-08 中国铁路设计集团有限公司 一种铬铜合金化耐候型孪生诱发塑性钢及其制备方法

Also Published As

Publication number Publication date
CN105849302A (zh) 2016-08-10
KR101543916B1 (ko) 2015-08-11
CN109266959B (zh) 2022-05-24
KR20150075315A (ko) 2015-07-03
JP2017507249A (ja) 2017-03-16
JP6615773B2 (ja) 2019-12-04
CN109266959A (zh) 2019-01-25
EP3088555A4 (en) 2017-04-05
US20160319407A1 (en) 2016-11-03
EP3088555A1 (en) 2016-11-02
CN105849302B (zh) 2018-08-28
WO2015099363A8 (ko) 2015-09-17

Similar Documents

Publication Publication Date Title
WO2015099363A1 (ko) 표면 가공 품질이 우수한 저온용강
WO2016105002A1 (ko) 표면 가공 품질이 우수한 저온용 강판 및 그 제조방법
WO2016104975A1 (ko) Ｐｗｈｔ 후 인성이 우수한 고강도 압력용기용 강재 및 그 제조방법
WO2017105107A1 (ko) 저온 변형시효 충격특성 및 용접 열영향부 충격특성이 우수한 고강도 강재 및 이의 제조방법
KR101647227B1 (ko) 표면 가공 품질이 우수한 저온용 강판 및 그 제조 방법
WO2018117712A1 (ko) 저온인성 및 항복강도가 우수한 고 망간 강 및 제조 방법
WO2019125083A1 (ko) 우수한 경도와 충격인성을 갖는 내마모강 및 그 제조방법
WO2010074473A2 (en) High strength steel plate for nuclear reactor containment vessel and method of manufacturing the same
WO2021091138A1 (ko) 저온 충격인성이 우수한 고강도 강재 및 그 제조방법
WO2018117450A1 (ko) 저온인성 및 후열처리 특성이 우수한 내sour 후판 강재 및 그 제조방법
WO2017105109A1 (ko) 저온 변형시효 충격특성이 우수한 고강도 강재 및 이의 제조방법
WO2017111489A1 (ko) 내수소취화성이 우수한 오스테나이트계 강재
WO2018117496A1 (ko) 고온 템퍼링 열처리 및 용접 후 열처리 저항성이 우수한 압력용기용 강재 및 이의 제조방법
WO2022139191A1 (ko) 저온 충격인성이 우수한 극후물 강재 및 그 제조방법
WO2019074236A1 (ko) 저온 변형시효 충격특성이 우수한 후강판 및 그 제조방법
WO2020111857A1 (ko) 크리프 강도가 우수한 크롬-몰리브덴 강판 및 그 제조방법
CN112912530A (zh) 屈服强度优异的奥氏体高锰钢材及其制备方法
WO2019125076A1 (ko) 우수한 경도와 충격인성을 갖는 내마모강 및 그 제조방법
WO2019132179A1 (ko) 고강도 고인성 열연강판 및 그 제조방법
WO2020085847A1 (ko) 표면품질 및 응력부식균열 저항성이 우수한 극저온용 오스테나이트계 고망간 강재 및 그 제조방법
WO2021080205A1 (ko) 고온 산화 저항성 및 고온 강도가 우수한 크롬 강판 및 그 제조 방법
WO2020085852A1 (ko) 항복강도가 우수한 오스테나이트계 고망간 강재 및 그 제조방법
WO2020085861A1 (ko) 형상이 우수한 극저온용 오스테나이트계 고망간 강재 및 그 제조방법
WO2017095049A1 (ko) 저온 충격 인성이 우수한 선재 및 그 제조방법
WO2020111547A1 (ko) 수소유기균열 저항성이 우수한 압력용기용 강재 및 그 제조방법

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 14873409

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 15102662

Country of ref document: US

ENP Entry into the national phase

Ref document number: 2016560327

Country of ref document: JP

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

REEP Request for entry into the european phase

Ref document number: 2014873409

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 2014873409

Country of ref document: EP