WO2021256587A1 - 형강 및 그 제조 방법 - Google Patents

형강 및 그 제조 방법 Download PDF

Info

Publication number
WO2021256587A1
WO2021256587A1 PCT/KR2020/007949 KR2020007949W WO2021256587A1 WO 2021256587 A1 WO2021256587 A1 WO 2021256587A1 KR 2020007949 W KR2020007949 W KR 2020007949W WO 2021256587 A1 WO2021256587 A1 WO 2021256587A1
Authority
WO
WIPO (PCT)
Prior art keywords
weight
less
section steel
mpa
temperature
Prior art date
Application number
PCT/KR2020/007949
Other languages
English (en)
French (fr)
Korean (ko)
Inventor
정준호
장홍기
Original Assignee
현대제철 주식회사
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 현대제철 주식회사 filed Critical 현대제철 주식회사
Priority to JP2021564649A priority Critical patent/JP7297096B2/ja
Priority to US17/609,965 priority patent/US20220316019A1/en
Priority to CN202080034335.9A priority patent/CN114080461B/zh
Priority to DE112020007334.3T priority patent/DE112020007334T5/de
Priority to PCT/KR2020/007949 priority patent/WO2021256587A1/ko
Publication of WO2021256587A1 publication Critical patent/WO2021256587A1/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
    • C22C38/18—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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/63—Quenching devices for bath quenching
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment 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
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/20—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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a section steel and a method for manufacturing the same, and more particularly, to a high-strength and high-performance section steel having fire/seismic resistance performance and a method for manufacturing the same.
  • the section steel generally refers to a steel material having a multifaceted cross-sectional shape. Recently, section steel is applied as structural steel such as columns of large buildings, and is also applied as temporary materials for civil works such as subways and bridges and piles for foundation.
  • the section steel can be manufactured by hot rolling a cast steel such as bloom, billet, beam blank, etc. manufactured by continuous casting.
  • An object of the present invention is to provide a high-strength and high-performance section steel having fire-resistance/seismic-resistance performance and a method for manufacturing the same.
  • a section steel according to an embodiment of the present invention for achieving the above object is carbon (C): 0.08 to 0.17 wt%, manganese (Mn): 0.50 to 1.60 wt%, silicon (Si): 0.10 to 0.50 wt%, chromium (Cr): 0.10 to 0.70% by weight, copper (Cu): more than 0 and 0.5% by weight or less, molybdenum (Mo): 0.30 to 0.70% by weight, phosphorus (P): more than 0 to 0.02% by weight or less, sulfur (S): More than 0 and not more than 0.01% by weight, nitrogen (N): greater than 0 and not more than 0.012% by weight, boron (B): greater than 0 and less than or equal to 0.003% by weight, nickel (Ni), vanadium (V), niobium (Nb) and titanium (Ti) Sum of at least any one of: 0.01 to 0.5% by weight and the remaining iron (Fe) and other un
  • the section steel may have a shock absorption energy of 200J or more at 0°C.
  • the final microstructure of the section steel may include bainite.
  • a method for manufacturing a section steel according to an embodiment of the present invention for achieving the above object is (a) carbon (C): 0.08 to 0.17 wt%, manganese (Mn): 0.50 to 1.60 wt%, silicon (Si): 0.10 ⁇ 0.50% by weight, chromium (Cr): 0.10 to 0.70% by weight, copper (Cu): more than 0 and 0.5% by weight or less, molybdenum (Mo): 0.30 to 0.70% by weight, phosphorus (P): more than 0, 0.02% by weight or less , sulfur (S): more than 0 and less than 0.01% by weight, nitrogen (N): more than 0 and not more than 0.012% by weight, boron (B): more than 0 and less than or equal to 0.003% by weight, nickel (Ni), vanadium (V), niobium (Nb) ) and the sum of at least one of titanium (Ti): 0.01 to 0.5% by weight and the remaining
  • the QST (Quenching & Self-Tempering) treatment step may have a water cooling end temperature and a self-tempering temperature of 765 ⁇ 800 °C.
  • the tensile strength at room temperature of the section steel subjected to step (c) is 490 to 620 MPa, the yield strength is 355 MPa or more, the yield ratio is 0.8 or less, and the high temperature yield strength at 600 ° C. may be 273 MPa or more.
  • the step (b) of the method for manufacturing the section steel may include hot rolling to a rolling start temperature of 1050 to 1100°C.
  • FIG. 1 is a flowchart illustrating a method for manufacturing a section steel according to an embodiment of the present invention.
  • fire-resisting heavy plate materials have been developed, but have not reached commercialization, and there is no development and performance evaluation of fire-resisting steel materials for shaped building structures (H-beams, etc.).
  • H-beams shaped building structures
  • it is intended to provide a high-strength, high-performance section steel having stable fire-resistance/seismic-resistance performance and a manufacturing method thereof.
  • the section steel according to an embodiment of the present invention has carbon (C): 0.08 to 0.17 wt%, manganese (Mn): 0.50 to 1.60 wt%, silicon (Si): 0.10 to 0.50 wt%, chromium (Cr): 0.10 to 0.70 wt%, copper (Cu): more than 0 and 0.5 wt% or less, molybdenum (Mo): 0.30 to 0.70 wt%, phosphorus (P): more than 0, 0.02 wt% or less, sulfur (S): more than 0, 0.01 wt% or less , Nitrogen (N): more than 0 and less than 0.012% by weight, boron (B): more than 0 and less than or equal to 0.003% by weight, nickel (Ni), vanadium (V), niobium (Nb), and titanium (Ti) at least any one or more sum : 0.01 to 0.5% by weight and the remaining iron (Fe) and other unavoidable
  • Carbon (C) is added to secure strength and is the element that has the greatest influence on weldability.
  • carbon reacts with Nb, Ti, etc. to promote the formation of fine carbides, thereby effectively contributing to strength improvement through precipitation strengthening, while preventing dislocation movement at high temperatures, thereby improving high-temperature strength and securing fire resistance performance.
  • the carbon (C) may be added in a content ratio of 0.08 to 0.17 wt% based on the total weight of the section steel according to an embodiment of the present invention. When the content of carbon is less than 0.08% by weight of the total weight, it may be difficult to secure sufficient strength.
  • Manganese (Mn) is a solid solution strengthening element that not only contributes to securing strength, but also improves the hardenability of steel and is an effective element for generating bainite structure.
  • Manganese may be added in a content ratio of 0.50 to 1.60 wt% based on the total weight of the section steel according to an embodiment of the present invention. When the manganese content is less than 0.50% by weight, the effect of solid-solution strengthening cannot be sufficiently exhibited. In addition, when the content of manganese exceeds 1.60% by weight, it may combine with S to generate MnS inclusions or may cause central segregation in the ingot, thereby reducing the ductility of the section steel and lowering the corrosion resistance.
  • Silicon (Si) is added together with aluminum as a deoxidizer to remove oxygen in steel in the steelmaking process.
  • silicon may also have a solid solution strengthening effect.
  • the silicon may be added in a content ratio of 0.10 to 0.50 wt% based on the total weight of the section steel according to an embodiment of the present invention. When the content of silicon is less than 0.10% by weight of the total weight, the effect of adding silicon cannot be properly exhibited. Conversely, when the content of silicon exceeds 0.50% by weight of the total weight, when a large amount is added, the weldability of steel is deteriorated, and a problem may be given to the surface quality by generating a red scale during reheating and hot rolling.
  • Chromium is an element that improves the hardenability of steel and contributes to securing bainite microstructure. When added to C-Mn steel as a ferrite stabilizing element, it delays the diffusion of carbon due to a solute interference effect, thereby affecting grain size refinement.
  • the chromium may be added in a content ratio of 0.10 to 0.70 wt% based on the total weight of the section steel according to an embodiment of the present invention. When the content of chromium is less than 0.10% by weight of the total weight, the effect of adding chromium cannot be properly exhibited.
  • Copper (Cu) is an element that exhibits a solid solution strengthening effect by being dissolved in ferrite.
  • bainite transformation supersaturated copper without precipitation is dissolved in the structure at room temperature, and a copper phase is precipitated on dislocations introduced by bainite transformation when heated to a temperature of 600 ° C. increases the strength of the base material.
  • the copper may be added in a content ratio of greater than 0 and 0.5 wt% or less based on the total weight of the section steel according to an embodiment of the present invention. When the copper content exceeds 0.5% by weight of the total weight, hot working is difficult, precipitation strengthening is saturated, toughness is reduced, and problems that cause red hot brittleness occur.
  • Molybdenum can contribute to securing the bainite microstructure by improving the hardenability of steel, and is a very effective element for securing high-temperature strength, and is an effective element for securing the strength of the base material and high-temperature strength.
  • the molybdenum may be added in a content ratio of 0.30 to 0.70 wt % or less based on the total weight of the section steel according to an embodiment of the present invention.
  • Phosphorus (P) may perform a function of increasing the strength of strength by solid solution strengthening and suppressing the formation of carbides.
  • the phosphorus may be added in a content ratio of greater than 0 and 0.020 wt% or less based on the total weight of the section steel according to an embodiment of the present invention. When the phosphorus content exceeds 0.020% by weight, inclusions may be generated as trap elements to decrease ductility of steel, and there is a problem in that the low-temperature impact value is lowered due to precipitation behavior.
  • S can improve processability by forming fine MnS precipitates.
  • the sulfur may be added in a content ratio of greater than 0 to 0.01 wt% or less based on the total weight of the section steel according to an embodiment of the present invention. When the content of sulfur exceeds 0.01% by weight, inclusions may be generated as trap elements, thereby reducing ductility of steel, impairing toughness and weldability, and lowering low-temperature impact values.
  • Nitrogen (N) may contribute to crystal grain refinement by forming nitride-based precipitates such as AlN, and contributing to securing high-temperature strength.
  • the nitrogen may be added in a content ratio of greater than 0 and 0.012% by weight or less based on the total weight of the section steel according to an embodiment of the present invention. When the nitrogen content exceeds 0.012% by weight, the toughness of the weld may be reduced, and the impact value may be reduced.
  • Boron (B) is a strong hardenable element and contributes to the improvement of the strength of steel.
  • boron may be optionally added in an amount greater than 0 and 0.003% by weight or less. If the content of boron exceeds 0.003% by weight of the total weight of the section steel according to an embodiment of the present invention, there is a problem of causing material deviation due to grain boundary segregation.
  • Nickel (Ni) is an element that increases hardenability and improves toughness
  • vanadium (V) has the effect of increasing strength by forming precipitates during rolling.
  • niobium (Nb) is an element that precipitates in the form of NbC or Nb (C,N) to improve the strength of the base material and weld
  • titanium (Ti) suppresses the formation of AlN by forming high-temperature TiN and Ti(C ,N) is an element having the effect of refining the grain size by forming.
  • the section steel according to an embodiment of the present invention contains at least one of nickel (Ni), vanadium (V), niobium (Nb), and titanium (Ti), but the sum of the contents is 0.01 ⁇ It may be added in a content ratio of 0.5% by weight.
  • the sum of the content of at least one of nickel (Ni), vanadium (V), niobium (Nb), and titanium (Ti) contained in the section steel according to an embodiment of the present invention is less than 0.01 wt %, the above-described additive effect cannot be expected, and when it is higher than 0.5% by weight, the manufacturing cost of parts increases, brittle cracks occur, and the carbon content in the matrix decreases, which may cause problems in which the properties of steel are deteriorated.
  • the section steel according to an embodiment of the present invention having the alloy element composition has a tensile strength of 490 to 620 MPa at room temperature, a yield strength of 355 MPa or more, a yield ratio of 0.8 or less, and a high temperature yield strength of 273 MPa or more at 600 ° C.
  • the 0 °C shock absorption energy may be 200J or more.
  • the final microstructure may include bainite.
  • the method for manufacturing a section steel having excellent fire resistance properties according to an embodiment of the present invention includes a reheating step (S100), a hot rolling step (S200), and a Quenching & Self-Tempering (QST) step (S300).
  • the section steel rolling process is manufactured through a reheating process, a hot deformation process, and a cooling process.
  • the reheating process the semi-finished beam blank is reheated to 1200 ⁇ 1250°C.
  • the hot rolling process goes through each of the rolling rolls (RM, IM, FM) and completes the final finishing rolling at 910 ⁇ 950°C, and then STT 765 ⁇ It is characterized in that 800°C is ensured.
  • the steel of the predetermined composition described above is reheated.
  • the steel may be manufactured through a continuous casting process after obtaining molten steel of a desired composition through a steelmaking process.
  • the steel material may be, for example, a billet or a beam blank.
  • the steel is carbon (C): 0.08 to 0.17 wt%, manganese (Mn): 0.50 to 1.60 wt%, silicon (Si): 0.10 to 0.50 wt%, chromium (Cr): 0.10 to 0.70 wt%, copper (Cu) ): greater than 0 and less than or equal to 0.5% by weight, molybdenum (Mo): 0.30 to 0.70% by weight, phosphorus (P): greater than 0 and less than or equal to 0.02% by weight, sulfur (S): greater than 0 and less than or equal to 0.01% by weight, nitrogen (N): 0 More than 0.012% by weight or less, boron (B): greater than 0 and less than or equal to 0.003% by weight, the sum of at least one of nickel (Ni), vanadium (V), niobium (Nb) and titanium (Ti): 0.01 to 0.5% by weight and The remaining iron (Fe) and other unavoidable impurities
  • the steel material may be reheated at a temperature of 1200 ⁇ 1250 °C.
  • the segregated component during the continuous casting process may be re-dissolved.
  • the reheating temperature is lower than 1200° C., the solid solution of various carbides may not be sufficient, and there may be a problem that the segregated components are not sufficiently evenly distributed during the continuous casting process. If the reheating temperature exceeds 1250 °C, very coarse austenite grains are formed, so it may be difficult to secure strength. In addition, when it exceeds 1250° C., heating cost increases and process time is added, which may result in an increase in manufacturing cost and a decrease in productivity.
  • the reheated steel material is hot rolled.
  • the hot rolling may be controlled so that the rolling end temperature is 910 ⁇ 950 °C.
  • the rolling end temperature is less than 910° C.
  • rolling in the non-recrystallized region may be performed, thereby increasing the rolling addition and increasing the yield ratio of the rolled section steel.
  • the hot rolling may be controlled so that the rolling start temperature 1050 ⁇ 1100 °C.
  • the hot-rolled section steel is cooled and self-tempered.
  • a quenching method of spraying cooling water to the section steel is applied.
  • the QST step may be performed in a state where the water cooling end temperature and the self-tempering temperature are controlled to be 765 to 800°C by controlling the feed rate of the section steel or the amount of the sprayed cooling water.
  • the steel manufacturing process described above it is manufactured through a reheating process, a hot deformation process, and a cooling process.
  • the reheating process the semi-finished billet and beam blank are reheated at 1200 ⁇ 1250°C.
  • QST Quenching & Self-Tempering
  • the water cooling end temperature and self-tempering temperature controlled to 765 ⁇ 800 °C processing can be performed.
  • the ingot was first reheated at 1200 ⁇ 1250 °C and then hot rolled to manufacture an H-beam, and the finish rolling temperature was controlled in the range of 910 ⁇ 950 °C. After hot rolling to a thickness of 15 mm based on the flange part of the H-beam, cooling was performed. Water cooling was performed after hot rolling, and water cooling was performed by changing the water cooling end temperature to 765 ⁇ 800°C.
  • chromium (Cr) and some of the conventionally used expensive precipitation hardening alloy elements such as niobium (Nb) or titanium (Ti) are not used or used in a small amount so that strength and toughness can be simultaneously improved.
  • the design and process conditions for steel grades with alloying elements are applied.
  • low-temperature toughness may be secured through self-tempering temperature control during cooling.
  • the manufactured section steel may have a tensile strength of 490 to 620 MPa at room temperature, a yield strength of 355 MPa or more, a yield ratio of 0.8 or less, and a high temperature yield strength of 273 MPa or more at 600°C.
  • the final microstructure may include bainite.
  • Table 1 shows the composition of major alloying elements (unit: wt%) of this experimental example
  • Table 2 shows the results of measuring the process conditions for manufacturing the specimen of this experimental example and the mechanical properties of the implemented specimen accordingly.
  • Beam blanks having the composition shown in Table 1 were manufactured using an electric furnace, and then H-beams having a flange portion thickness of 15 mm were manufactured through hot rolling.
  • the components of the composition system 2 of the present invention are carbon (C): 0.08 to 0.17% by weight, manganese (Mn): 0.50 to 1.60% by weight, silicon (Si): 0.10 to 0.50% by weight, chromium (Cr) ): 0.10 to 0.70 wt%, copper (Cu): more than 0 and 0.5 wt% or less, molybdenum (Mo): 0.30 to 0.70 wt%, phosphorus (P): more than 0 and 0.02 wt% or less, sulfur (S): more than 0 0.01 wt % or less, nitrogen (N): greater than 0 and 0.012 wt % or less, boron (B): greater than 0 0.003 wt % or less, nickel (Ni), vanadium (V), niobium (Nb) and titanium (Ti) at least among The sum of any one or more: 0.01 to 0.5% by weight and the remaining iron (C): 0.
  • composition of the composition system 1 of the present invention does not satisfy the composition of phosphorus (P): more than 0 and 0.02% by weight or less, sulfur (S): more than 0 and 0.01% by weight or less, and boron (B): more than 0 and 0.003% by weight or less. can not do it.
  • the specimen according to Example 1 of this experimental example is carbon (C): 0.08 to 0.17 wt%, manganese (Mn): 0.50 to 1.60 wt%, silicon (Si): 0.10 to 0.50 wt%, chromium (Cr): 0.10 to 0.70% by weight, copper (Cu): more than 0 and 0.5% by weight or less, molybdenum (Mo): 0.30 to 0.70% by weight, phosphorus (P): more than 0 to 0.02% by weight or less, sulfur (S): More than 0 and not more than 0.01% by weight, nitrogen (N): greater than 0 and not more than 0.012% by weight, boron (B): greater than 0 and less than or equal to 0.003% by weight, nickel (Ni), vanadium (V), niobium (Nb) and titanium (Ti) The sum of at least any one of: 0.01 to 0.5 wt% and the remaining iron (Fe) satis
  • Example 1 which satisfies these compositions and process conditions, satisfies the requirements of a tensile strength of 490 to 620 MPa at room temperature, a yield strength of 355 MPa or more, a yield ratio of 0.8 or less, and a high temperature yield strength of 273 MPa or more at 600 ° C. .
  • the specimen according to Comparative Example 1 of this experimental example satisfies the composition range of phosphorus (P): more than 0 and 0.02 wt% or less, sulfur (S): more than 0 and 0.01 wt% or less, and boron (B): more than 0 and 0.003 wt% or less
  • the self-tempering temperature does not satisfy the range of 765 ⁇ 800°C.
  • the tensile strength at room temperature does not satisfy the range of 490 to 620 MPa, and the high temperature yield strength at 600° C. does not satisfy 273 MPa or more.
  • the specimen according to Comparative Example 2 of this experimental example satisfies the composition ranges of phosphorus (P): more than 0 and 0.02% by weight or less, sulfur (S): more than 0 and 0.01% by weight or less, and boron (B): more than 0 and 0.003% by weight or less.
  • P phosphorus
  • S sulfur
  • B boron
  • the self-tempering temperature, the recuperation temperature does not satisfy the range of 765 ⁇ 800°C.
  • the tensile strength at room temperature does not satisfy the range of 490 to 620 MPa
  • the high temperature yield strength at 600° C. does not satisfy 273 MPa or more.
  • Comparative Example 3 Comparative Example 4, Comparative Example 5, and Comparative Example 6 of the present experimental example did not satisfy the self-tempering temperature, which is the recuperation temperature, of 765 to 800° C. in the QST (Quenching & Self-Tempering) treatment.
  • the resulting specimens do not satisfy the high temperature yield strength of 273 MPa or more at 600 °C.
  • the specimen according to Comparative Example 7 of the present experimental example did not satisfy the range of 765 ⁇ 800 ° C. Accordingly, the specimen does not satisfy the yield strength at room temperature of 355 MPa or more, and the high temperature yield strength at 600°C does not satisfy 273 MPa or more.

Landscapes

  • 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)
PCT/KR2020/007949 2020-06-19 2020-06-19 형강 및 그 제조 방법 WO2021256587A1 (ko)

Priority Applications (5)

Application Number Priority Date Filing Date Title
JP2021564649A JP7297096B2 (ja) 2020-06-19 2020-06-19 形鋼およびその製造方法
US17/609,965 US20220316019A1 (en) 2020-06-19 2020-06-19 Section steel and method for manufacturing same
CN202080034335.9A CN114080461B (zh) 2020-06-19 2020-06-19 型钢及其制造方法
DE112020007334.3T DE112020007334T5 (de) 2020-06-19 2020-06-19 Formstahl und verfahren zur herstellung desselben
PCT/KR2020/007949 WO2021256587A1 (ko) 2020-06-19 2020-06-19 형강 및 그 제조 방법

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/KR2020/007949 WO2021256587A1 (ko) 2020-06-19 2020-06-19 형강 및 그 제조 방법

Publications (1)

Publication Number Publication Date
WO2021256587A1 true WO2021256587A1 (ko) 2021-12-23

Family

ID=79268116

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/KR2020/007949 WO2021256587A1 (ko) 2020-06-19 2020-06-19 형강 및 그 제조 방법

Country Status (5)

Country Link
US (1) US20220316019A1 (ja)
JP (1) JP7297096B2 (ja)
CN (1) CN114080461B (ja)
DE (1) DE112020007334T5 (ja)
WO (1) WO2021256587A1 (ja)

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5928654B2 (ja) * 2013-03-15 2016-06-01 Ｊｆｅスチール株式会社 厚肉高靭性高張力鋼板およびその製造方法
US20160333440A1 (en) * 2014-01-24 2016-11-17 Rautaruukki Oyj Hot-rolled ultrahigh strength steel strip product
KR20180074841A (ko) * 2016-12-23 2018-07-04 현대제철 주식회사 강재 및 그 제조 방법
KR20200012145A (ko) * 2018-07-26 2020-02-05 현대제철 주식회사 형강 및 그 제조 방법
KR20200064125A (ko) * 2017-11-10 2020-06-05 아르셀러미탈 냉간 압연되고 열처리된 강 시트 및 그 제조 방법
KR20200077701A (ko) * 2018-12-21 2020-07-01 현대제철 주식회사 형강 및 그 제조 방법

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4464486B2 (ja) * 1999-06-22 2010-05-19 新日本製鐵株式会社 高強度高靱性圧延形鋼とその製造方法
JP2002003942A (ja) * 2000-06-14 2002-01-09 Nippon Steel Corp 材質偏差の小さい強靭低降伏比鋼の製造方法
JP2002363644A (ja) * 2001-06-11 2002-12-18 Nippon Steel Corp 靭性と疲労強度とに優れた高張力鋼の製造方法
JP2003253331A (ja) * 2002-03-05 2003-09-10 Nippon Steel Corp 高靱性・高延性高張力鋼の製造方法
JP2004060001A (ja) * 2002-07-29 2004-02-26 Sumitomo Metal Ind Ltd 増厚加工を施して用いる建築用鋼材
FI20106275A (fi) * 2010-12-02 2012-06-03 Rautaruukki Oyj Ultraluja rakenneteräs ja menetelmä ultralujan rakenneteräksen valmistamiseksi
JP5838693B2 (ja) * 2011-09-28 2016-01-06 Ｊｆｅスチール株式会社 高温強度に優れる鋼材の製造方法
KR20140056765A (ko) 2012-10-31 2014-05-12 현대제철 주식회사 형강 및 그 제조 방법
SI2789699T1 (sl) * 2013-08-30 2017-06-30 Rautaruukki Oyj Utrjeni vroče valjani jekleni proizvod in metoda za proizvodnjo le-tega
KR101665819B1 (ko) * 2014-12-24 2016-10-13 주식회사 포스코 열처리 강재, 내구특성이 우수한 초고강도 성형품 및 그 제조방법
KR101647230B1 (ko) * 2014-12-24 2016-08-10 주식회사 포스코 저온 인성이 우수한 저항복비 고강도 강재 및 그 제조방법
JP6409598B2 (ja) * 2015-01-30 2018-10-24 新日鐵住金株式会社 靭性に優れた高強度極厚ｈ形鋼及びその製造方法
WO2018115925A1 (en) * 2016-12-19 2018-06-28 Arcelormittal Steel section having a thickness of at least 100mm and method of manufacturing the same

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5928654B2 (ja) * 2013-03-15 2016-06-01 Ｊｆｅスチール株式会社 厚肉高靭性高張力鋼板およびその製造方法
US20160333440A1 (en) * 2014-01-24 2016-11-17 Rautaruukki Oyj Hot-rolled ultrahigh strength steel strip product
KR20180074841A (ko) * 2016-12-23 2018-07-04 현대제철 주식회사 강재 및 그 제조 방법
KR20200064125A (ko) * 2017-11-10 2020-06-05 아르셀러미탈 냉간 압연되고 열처리된 강 시트 및 그 제조 방법
KR20200012145A (ko) * 2018-07-26 2020-02-05 현대제철 주식회사 형강 및 그 제조 방법
KR20200077701A (ko) * 2018-12-21 2020-07-01 현대제철 주식회사 형강 및 그 제조 방법

Also Published As

Publication number Publication date
CN114080461B (zh) 2023-04-14
DE112020007334T5 (de) 2023-03-30
US20220316019A1 (en) 2022-10-06
JP2022541704A (ja) 2022-09-27
CN114080461A (zh) 2022-02-22
JP7297096B2 (ja) 2023-06-23

Similar Documents

Publication Publication Date Title
CA2106616C (en) Shape steel material having high strength, high toughness and excellent fire resistance and process for producing rolled shape steel of said material
WO2006022053A1 (ja) 溶接性および靭性に優れた引張り強さ５５０MPa級以上の高張力鋼材およびその製造方法
KR100799822B1 (ko) 저항복비 내화 강재
JP5114743B2 (ja) 耐火用高強度圧延鋼材およびその製造方法
US20090087335A1 (en) Fire resistant steel and method of production of same
KR102089167B1 (ko) 형강 및 그 제조 방법
WO2020111867A2 (ko) 우수한 저항복비 및 저온인성 특성을 가지는 구조용강 및 그 제조방법
WO2021256587A1 (ko) 형강 및 그 제조 방법
WO2021256590A1 (ko) 철근 및 그 제조방법
KR102155431B1 (ko) 형강 및 그 제조 방법
WO2017222122A1 (ko) 철근 및 이의 제조 방법
JP3397271B2 (ja) 耐火用圧延形鋼およびその製造方法
JPH10204572A (ja) ７００℃耐火圧延形鋼およびその製造方法
JPH0832945B2 (ja) 耐火強度の優れた建築構造用鋼材およびその製造方法
JP3285732B2 (ja) 耐火用圧延形鋼およびその製造方法
JP3181448B2 (ja) 含酸化物分散鋳片及びその鋳片による靱性の優れた圧延形鋼の製造方法
JP3472017B2 (ja) 耐火圧延形鋼およびその製造方法
JP3241199B2 (ja) 酸化物粒子分散鋳片及びその鋳片を素材とする靭性の優れた圧延形鋼の製造方法
JP3426425B2 (ja) 耐火圧延形鋼用鋳片およびそれを素材とする耐火用圧延形鋼の製造方法
JPH05279735A (ja) 大入熱溶接熱影響部靱性の優れた建築用耐火鋼板の製造法
JP3107698B2 (ja) 強度・靱性および耐火性の優れたフランジを有する形鋼の製造方法
KR20240059874A (ko) 형강 및 형강 제조 방법
JPH0737648B2 (ja) 靭性の優れた建築用耐火鋼板の製造法
KR20000019209A (ko) 고온 강도가 우수한 저항복비형 열연강판의 제조방법
JP3107696B2 (ja) 強度・靱性および耐火性の優れたフランジを有する形鋼の製造方法

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2021564649

Country of ref document: JP

Kind code of ref document: A

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

Ref document number: 20941437

Country of ref document: EP

Kind code of ref document: A1

122 Ep: pct application non-entry in european phase

Ref document number: 20941437

Country of ref document: EP

Kind code of ref document: A1