WO2017222122A1 - Barre d'armature et son procédé de fabrication - Google Patents

Barre d'armature et son procédé de fabrication Download PDF

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Publication number
WO2017222122A1
WO2017222122A1 PCT/KR2016/013590 KR2016013590W WO2017222122A1 WO 2017222122 A1 WO2017222122 A1 WO 2017222122A1 KR 2016013590 W KR2016013590 W KR 2016013590W WO 2017222122 A1 WO2017222122 A1 WO 2017222122A1
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weight
reinforcing bar
steel
rebar
mpa
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PCT/KR2016/013590
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English (en)
Korean (ko)
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정준호
김원회
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현대제철 주식회사
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Priority claimed from KR1020160149539A external-priority patent/KR101828713B1/ko
Application filed by 현대제철 주식회사 filed Critical 현대제철 주식회사
Publication of WO2017222122A1 publication Critical patent/WO2017222122A1/fr

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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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to reinforcing bars and methods for manufacturing the same, and more particularly, to light steel bars having high strength and high ductility and methods for manufacturing the same.
  • carbon steel has advantages of low cost and easy control of materials by heat treatment.
  • carbon steel is applied throughout an industry such as automobiles and mechanical parts.
  • carbon steel is being applied to the structure for securing the space of human activities.
  • structural steel is widely applied to skyscrapers, long bridges, large marine structures, underground structures, and the like.
  • the carbon steel can be applied to various industries in the form of rebar.
  • rebars applied to a structure, as the structure becomes very high and large, it is required to maintain a relatively light weight while having high strength and high ductility.
  • the present invention provides a lightweight reinforcing bar having high strength and high ductility through alloying components and process control.
  • One embodiment of the present invention is 0.1% to 1.5% by weight of carbon (C), 0.05% to 1.0% by weight of silicon (Si), 0.5% to 16.0% by weight of manganese (Mn), phosphorus (P) greater than 0 0.03 Weight%, Sulfur (S) greater than 0 0.03 weight%, Aluminum (Al) greater than 0 9.0 weight%, Chromium (Cr) 0.2 to 4.0 weight%, Nickel (Ni) 0.1 to 0.5 weight%, Nitrogen (N ) 0.005% to 0.015% by weight, 0.03% to 0.5% by weight of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and an alloy composition containing the remaining iron (Fe) and unavoidable impurities Reheating the billet having at 1100 ° C.
  • Another embodiment of the invention is 0.1% to 1.5% by weight of carbon (C), 0.05% to 1.0% by weight of silicon (Si), 0.5% to 16.0% by weight of manganese (Mn), greater than 0 0.03 Weight%, Sulfur (S) greater than 0 0.03 weight%, Aluminum (Al) greater than 0 9.0 weight%, Chromium (Cr) 0.2 to 4.0 weight%, Nickel (Ni) 0.1 to 0.5 weight%, Nitrogen (N ) 0.005% to 0.015% by weight, 0.03% to 0.5% by weight of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and an alloy composition containing the remaining iron (Fe) and unavoidable impurities
  • the present invention relates to a reinforcing bar having a tensile strength (TS) of 1100 MPa or more and a tensile strength x elongation (TS x EL) of 20000 MPa ⁇ % or more.
  • the reinforcing bar may have a specific gravity of 6.5 gm ⁇ 3 to 7.0 gm ⁇ 3 .
  • the rebar may include a Fe 2 AlC fine grain particles having an average particle diameter of 10nm to 100nm in a dispersed state.
  • the reinforcing bar may have a complex structure of ferrite, austenite and kappa ( ⁇ ) -carbide.
  • the present invention through the dispersion strengthening, by uniformly forming the Fe 3 AlC fine grain particles in the base metal, it is possible to provide a lightweight reinforcing bar having high strength and high ductility.
  • FIG. 1 shows a method for manufacturing rebar of the present invention.
  • Figure 2 shows the microstructure of the reinforcing bar prepared in Example 1 of the present invention.
  • Figure 3 shows the microstructure of the reinforcing bar prepared in Example 3 of the present invention.
  • Figure 4 shows the microstructure of the rebar produced in Comparative Example 1 of the present invention.
  • One embodiment of the present invention is 0.1% to 1.5% by weight of carbon (C), 0.05% to 1.0% by weight of silicon (Si), 0.5% to 16.0% by weight of manganese (Mn), phosphorus (P) greater than 0 0.03 Weight%, Sulfur (S) greater than 0 0.03 weight%, Aluminum (Al) greater than 0 9.0 weight%, Chromium (Cr) 0.2 to 4.0 weight%, Nickel (Ni) 0.1 to 0.5 weight%, Nitrogen (N ) 0.005% to 0.015% by weight, 0.03% to 0.5% by weight of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and an alloy composition containing the remaining iron (Fe) and unavoidable impurities Reheating the billet having at 1100 ° C.
  • Another embodiment of the invention is 0.1% to 1.5% by weight of carbon (C), 0.05% to 1.0% by weight of silicon (Si), 0.5% to 16.0% by weight of manganese (Mn), greater than 0 0.03 Weight%, Sulfur (S) greater than 0 0.03 weight%, Aluminum (Al) greater than 0 9.0 weight%, Chromium (Cr) 0.2 to 4.0 weight%, Nickel (Ni) 0.1 to 0.5 weight%, Nitrogen (N ) 0.005% to 0.015% by weight, 0.03% to 0.5% by weight of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and an alloy composition containing the remaining iron (Fe) and unavoidable impurities
  • the present invention relates to a reinforcing bar having a tensile strength (TS) of 1100 MPa or more and a tensile strength x elongation (TS x EL) of 20000 MPa ⁇ % or more. This reinforcing
  • the rebar may include a Fe 3 AlC fine grain particles having an average particle diameter of 10nm to 100nm in a dispersed state.
  • the rebar may have a specific gravity of steel of 6.5gm ⁇ 3 to 7.0gm ⁇ 3 .
  • the reinforcing bar may have a complex structure of ferrite, austenite and kappa ( ⁇ ) -carbide.
  • carbon (C) is added to secure the strength and hardness of the steel.
  • Carbon (C) is dissolved in austenite to form martensite structure when quenched.
  • the hardening hardness may be improved, and the deformation potential may be increased during the hardening.
  • the carbon (C) is added in an amount of 0.1% by weight to 1.5% by weight of the total weight. If the carbon content is less than 0.1% by weight, it is difficult to secure sufficient strength. On the contrary, when the content of carbon (C) exceeds 1.5% by weight, the strength of the steel is increased, but the core hardness is reduced, it is difficult to secure sufficient elongation, and the fraction of the pearlite phase in the microstructure is difficult to secure the desired workability.
  • silicon (Si) is added as a deoxidizer for removing oxygen in the steel in the steelmaking process.
  • silicon (Si) is a ferrite stabilizing element having a solid solution strengthening effect, which is effective in inducing ferrite formation and improving toughness and ductility of steel.
  • silicon (Si) also has the effect of increasing the softening resistance phase during tempering.
  • the silicon (Si) is added in an amount of 0.05 wt% to 1.0 wt% of the total weight.
  • the silicon addition effect may not be properly exhibited.
  • the content of silicon (Si) exceeds 1.0% by weight, there is a problem in that oxides are formed on the surface of the steel, thereby reducing ductility, tube structure, and the like.
  • Manganese (Mn) is a substituted element having an atomic diameter similar to iron, which increases the strength and toughness of the steel and increases the hardenability of the steel, but decreases the ductility at the time of increasing the strength more than the addition of carbon (C).
  • manganese (Mn) is a very effective element for solid solution strengthening contributes to the hardenability of the steel, and serves to improve the hardenability of the steel.
  • the manganese (Mn) is added in an amount of 0.5 wt% to 16.0 wt% of the total weight. If the content of manganese (Mn) is less than 0.5% by weight it may not be sufficient to improve the yield strength by strengthening the ferrite solid solution. On the contrary, when the content of manganese (Mn) exceeds 16% by weight, the amount of MnS-based nonmetallic inclusions increases, which may cause defects such as cracking during piping, and may cause hardening cracks, deformation, or hardening ability. Over-improvement increases the likelihood of cold microstructure being expressed in the final tissue.
  • Phosphorus (P) is an element that partially contributes to the strength improvement, but when excessively included, deteriorates the ductility of the steel and causes the final material deviation due to the billet center segregation. P is not a problem if it is uniformly distributed in the steel, but usually forms a harmful compound of Fe 3 P.
  • the Fe 3 P is extremely fragile and segregated so that it does not become homogenized even after annealing, but increases in processing such as forging and rolling.
  • the phosphorus (P) is limited to a content of more than 0 and 0.03% by weight of the total weight. When the content of phosphorus (P) exceeds 0.03% by weight, as well as the center segregation, as well as micro segregation is formed to adversely affect the material, and also may worsen the ductility and tubulation.
  • S is an element that contributes in part to the improvement of workability, but when excessively contained, it inhibits the toughness and ductility of the steel and combines with manganese to form MnS non-metallic inclusions, thereby causing cracks during processing of the steel. Sulfur can combine with iron to form FeS if there is not enough manganese in the steel.
  • the sulfur (S) is limited to a content of more than 0 and 0.03% by weight of the total weight.
  • the content of sulfur (S) exceeds 0.03% by weight, there is a problem that greatly inhibits the ductility and excessively generates the MnS non-metallic inclusions.
  • Aluminum (Al) serves as a deoxidizer to remove oxygen in the steel.
  • Al is generally used as a deoxidizer, but this patent aims to increase the lattice constant and replace Fe atoms by adding up to 9% by weight in order to maximize the effect of reducing the specific gravity of the steel grade itself. Adding about 7.5% wt has a specific gravity reduction of 10%.
  • the aluminum (Al) is added in an amount of more than 0 9.0 wt% of the total weight. If the content of aluminum (Al) exceeds 9.0% by weight, there is a problem that to form the Al 2 O 3 decreases the toughness.
  • Chromium (Cr) is an effective element added to secure the strength, and can improve the hardenability of the steel and combine with carbon to form carbide to improve the strength. By forming a homogeneous oxide film on the surface of the plate, it is possible to reduce the decarburized portion of the surface layer portion of the plate.
  • Chromium (Cr) is added in an amount of 0.2% to 4.0% by weight of the total weight. If the content of chromium (Cr) is less than 0.2% by weight, it may be difficult to secure the strength even if the carbon (C) content is high. On the contrary, when the content of chromium (Cr) is more than 4.0% by weight, there is a problem of deteriorating ductility or heat affected zone (HAZ) toughness.
  • Nickel (Ni) refines grains and is dissolved in austenite and ferrite to strengthen the matrix and improve hardenability.
  • nickel (Ni) is an element effective in promoting the formation of low-temperature phase microstructure to improve low-temperature impact toughness.
  • chromium or molybdenum When coexisted with chromium or molybdenum, it exhibits excellent hardening ability and facilitates heat treatment of large steels.
  • austenite stabilizing element it is combined with chromium to form austenitic stainless steel and heat resistant steel. It strengthens low temperature toughness of steel and does not harm weldability and malleability. By slowing the diffusion of carbon or nitrogen, it prevents deterioration of heat-resistant steel and improves the expansion rate, stiffness rate, and ceramic rate.
  • the nickel (Ni) is added in an amount of 0.1 wt% to 0.5 wt% of the total weight of the steel sheet according to the present invention. If the content of nickel (Ni) is less than 0.1% by weight, it may be difficult to properly exhibit the effect of adding nickel (Ni). On the contrary, when a large amount of nickel (Ni) is added in excess of 0.5% by weight, red brittleness may be caused.
  • Nitrogen (N) is an unavoidable impurity, and there is a problem of lowering the internal quality of steel by forming inclusions such as AlN and TiN. Nitrogen is added in an amount of 0.005% to 0.015% by weight.
  • the alloy composition may further include one or more of titanium (Ti) niobium (Nb) and vanadium (V) in an amount of 0.03% by weight to 0.5% by weight.
  • titanium (Ti) forms a carbide upon reheating, thereby suppressing austenite grain growth, thereby miniaturizing the structure of the steel and increasing strength.
  • the carbide forming ability of Ti, V, and Nb is stronger than chromium, and is used for improving stainless steel or cutting tool steel because it refines crystal grains.
  • the compound is formed with other metal elements and the precipitation hardening effect is remarkable, it is used for precipitation hardening steel or permanent magnets.
  • the titanium (Ti) may be added in an amount of 0.03% to 0.5% by weight of the total weight. If the content of titanium (Ti) is less than 0.03% by weight, the titanium addition effect may not be properly exhibited. On the contrary, when the content of titanium (Ti) is more than 0.5% by weight, the carbonized precipitates are coarsened, so that the effect of suppressing grain growth is reduced, and it is difficult to secure ductility.
  • Niobium (Nb) combines with carbon (C) and nitrogen (N) at high temperatures to form carbides or nitrides.
  • Niobium-based carbides or nitrides suppress grain growth during rolling to refine grains, thereby improving strength and low temperature toughness of the steel.
  • the niobium (Nb) is added in an amount of 0.03% to 0.5% by weight of the total weight.
  • the content of niobium (Nb) is less than 0.03% by weight, the niobium addition effect cannot be properly exhibited.
  • the content of niobium (Nb) exceeds 0.5% by weight, the ductility of the steel is lowered, and the strength and low temperature toughness according to the increase in niobium content are not improved any more, and are present in solid solution in the ferrite. There is a risk of deterioration.
  • Vanadium (V) combines with carbon (C) and nitrogen (N) at high temperatures to form carbides or nitrides.
  • vanadium (V) serves to improve the strength of the steel through the precipitation strengthening effect by the formation of precipitates.
  • the vanadium is added in an amount of 0.03% to 0.5% by weight of the total weight. If the content of vanadium is less than 0.03% by weight, it may be difficult to properly exhibit the effect of adding vanadium. On the contrary, when the amount of vanadium is added in excess of 0.5% by weight, the low temperature impact toughness may be reduced.
  • the remainder is made of iron (Fe) and impurities that are inevitably included in the steelmaking process.
  • the method of manufacturing the rebar includes a reheating step S100, a hot rolling step S200, a cooling step S300, and a reheating step S400.
  • the reheating step (S100) is not necessarily to be performed, but is carried out in order to derive the effect, such as re-use of the precipitate.
  • the steel of the semi-finished state which is the target of the hot rolling process has the alloy composition described above.
  • the semi-finished steel may for example be a billet.
  • the billet of the alloy composition described above is reheated to 1100 ° C to 1200 ° C.
  • Steel having the alloy composition may be obtained through a continuous casting process after obtaining a molten steel of a desired composition through a steelmaking process. By reheating these steels, the segregated components can be reclaimed during casting.
  • the reheating step (S100) when the reheating temperature is less than 1100 ° C, the segregated components during casting may not be sufficiently reusable, and there is a problem that a rolling load is caused during hot rolling.
  • titanium is not sufficiently reusable in the alloy component, coarsening of precipitates occurs, and it is difficult to secure sufficient strength.
  • the reheating temperature when the reheating temperature is higher than 1200 ° C., the austenite grain size may be increased, thereby making it difficult to secure the strength. Due to the excessive heating process, only the steel manufacturing cost may increase.
  • the reheated steel is hot rolled to a finish rolling temperature of Ac1 to 1000 °C.
  • grains may be refined due to repetition of recovery and recrystallization during rolling.
  • finish rolling temperature (FRT) is less than Ac1
  • the mixed structure is generated by the abnormal region rolling, which makes it difficult to secure the workability of the steel sheet and may cause a load in the rolling process.
  • finish rolling temperature (FRT) is higher than 1000 ° C.
  • the quality of the steel sheet due to the generation of surface scale of the steel sheet is deteriorated, and the size of grains due to the high temperature rolling is increased, thereby making it impossible to secure the strength.
  • Finish rolling temperature (FRT) in the hot rolling step (S200), for example, may be 850 ⁇ 1000 °C.
  • the hot rolled steel is cooled to a temperature of Ms-100 (° C) to Ms (° C) via a temp core.
  • the effect of suppressing coarse grain growth to the maximum in the cooling temperature range is excellent.
  • the cooled rolled material is regenerated to 500 ° C to 600 ° C. It is possible to secure a microstructure having ferrite, austenite and kappa ( ⁇ ) -carbide in the recuperation temperature range. If the recuperation temperature is less than 550 ° C., it is difficult to secure workability due to an increase in strength and a decrease in ductility due to grain refinement. On the contrary, when the coiling temperature exceeds 600 °C ductility is secured but the strength is lowered.
  • the rebar according to an embodiment of the present invention may have a tensile strength (TS) of 1100 MPa or more, and a tensile strength x elongation (TS ⁇ EL) value of 20000 MPa ⁇ or more.
  • TS tensile strength
  • TS ⁇ EL tensile strength x elongation
  • the billets were hot-rolled under the conditions shown in Table 2 to prepare specimens of Examples 1 to 3 and Comparative Examples 1 and 2.
  • Table 3 shows the mechanical property evaluation results for the specimens prepared according to Examples 1 to 3 and Comparative Examples 1 and 2. The physical property evaluation was shown by measuring the tensile strength (TS), yield strength (YS) and elongation (EL).
  • Example 1 992 1,133 24.8 28098.4 ⁇ + ⁇ + ⁇
  • Example 2 1,185 1,285 29 37265 ⁇ + ⁇ + ⁇
  • Example 3 1,094 1,179 19.8 23344.2 ⁇ + ⁇ + ⁇
  • Comparative Example 1 651 832 14.3 11897.6 ⁇ + Fe 3 C Comparative Example 2 600 770 10.1 7,777 ⁇ + ⁇
  • the specimens of Comparative Examples 1 and 2 had a tensile strength (TS) of less than 1000 MPa and a tensile strength x elongation (TS ⁇ EL) of less than 20000 MPa ⁇ %.
  • TS tensile strength
  • TS ⁇ EL tensile strength x elongation
  • Example 2 to 4 show the microstructure cross sections of Example 2, Example 3 and Comparative Example 1 specimens, respectively.
  • Example 2 In the case of the specimens of Example 2 and Example 3, the composite structure of ferrite, austenite and kappa ( ⁇ ) -carbide was shown, and in the comparative example 1 specimen, the composite structure of ferrite and cementite was shown.

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Abstract

Selon un mode de réalisation, cette invention concerne un procédé de fabrication d'une barre d'armature, comprenant les étapes de : réchauffage d'une billette ayant une composition d'alliage prédéterminée à une température de 1100 °C à 1200 °C ; laminage à chaud la billette réchauffée à une température de laminage de finition du point Ac1 à 1000 °C ; refroidissement de l'acier laminé à chaud à une température de surface de Ms-100 (°C) à Ms (°C) à l'aide d'un procédé Tempcore ; et le fait de soumettre l'acier refroidi à un chauffage à récupération à une température de 500 °C à 600 °C.
PCT/KR2016/013590 2016-06-21 2016-11-24 Barre d'armature et son procédé de fabrication WO2017222122A1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
KR10-2016-0077466 2016-06-21
KR20160077466 2016-06-21
KR1020160149539A KR101828713B1 (ko) 2016-06-21 2016-11-10 철근 및 이의 제조 방법
KR10-2016-0149539 2016-11-10

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111485174A (zh) * 2020-04-13 2020-08-04 攀钢集团攀枝花钢铁研究院有限公司 地铁用钢轨及其制备方法
WO2021057218A1 (fr) * 2019-09-27 2021-04-01 南京钢铁股份有限公司 Procédé de commande d'un réseau de carbure pour tige en fil d'acier portant du gcr15 coulé en continu

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WO2014034070A1 (fr) * 2012-08-31 2014-03-06 Ｊｆｅスチール株式会社 Acier pour barres d'armature, et barre d'armature
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KR20150013246A (ko) * 2012-06-08 2015-02-04 신닛테츠스미킨 카부시키카이샤 강선재 또는 막대강
KR20160025183A (ko) * 2014-08-27 2016-03-08 현대제철 주식회사 고강도 강판 및 그 제조 방법

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* Cited by examiner, † Cited by third party
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KR20150013246A (ko) * 2012-06-08 2015-02-04 신닛테츠스미킨 카부시키카이샤 강선재 또는 막대강
WO2014034070A1 (fr) * 2012-08-31 2014-03-06 Ｊｆｅスチール株式会社 Acier pour barres d'armature, et barre d'armature
KR20130064760A (ko) * 2013-04-30 2013-06-18 현대제철 주식회사 고강도 강판 및 그 제조방법
KR20150001535A (ko) * 2013-06-27 2015-01-06 현대제철 주식회사 고강도 냉연강판 및 그 제조 방법
KR20160025183A (ko) * 2014-08-27 2016-03-08 현대제철 주식회사 고강도 강판 및 그 제조 방법

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2021057218A1 (fr) * 2019-09-27 2021-04-01 南京钢铁股份有限公司 Procédé de commande d'un réseau de carbure pour tige en fil d'acier portant du gcr15 coulé en continu
CN111485174A (zh) * 2020-04-13 2020-08-04 攀钢集团攀枝花钢铁研究院有限公司 地铁用钢轨及其制备方法

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