WO2019004454A1 - High-strength steel wire - Google Patents
High-strength steel wire Download PDFInfo
- Publication number
- WO2019004454A1 WO2019004454A1 PCT/JP2018/024904 JP2018024904W WO2019004454A1 WO 2019004454 A1 WO2019004454 A1 WO 2019004454A1 JP 2018024904 W JP2018024904 W JP 2018024904W WO 2019004454 A1 WO2019004454 A1 WO 2019004454A1
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- WO
- WIPO (PCT)
- Prior art keywords
- steel wire
- wire
- area ratio
- pearlite structure
- high strength
- Prior art date
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 257
- 239000010959 steel Substances 0.000 title claims abstract description 257
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 119
- 229910001567 cementite Inorganic materials 0.000 claims abstract description 37
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims abstract description 37
- 239000002344 surface layer Substances 0.000 claims abstract description 27
- 239000000203 mixture Substances 0.000 claims abstract description 19
- 239000010410 layer Substances 0.000 claims description 28
- 238000007747 plating Methods 0.000 claims description 12
- 229910052782 aluminium Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 8
- 229910052719 titanium Inorganic materials 0.000 claims description 8
- 229910001297 Zn alloy Inorganic materials 0.000 claims description 7
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052726 zirconium Inorganic materials 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 239000000463 material Substances 0.000 abstract 1
- 238000001816 cooling Methods 0.000 description 44
- 230000000694 effects Effects 0.000 description 28
- 238000000034 method Methods 0.000 description 24
- 238000004519 manufacturing process Methods 0.000 description 23
- 238000005491 wire drawing Methods 0.000 description 22
- 238000010438 heat treatment Methods 0.000 description 16
- 230000009467 reduction Effects 0.000 description 15
- 238000005098 hot rolling Methods 0.000 description 14
- 238000005096 rolling process Methods 0.000 description 14
- 230000032683 aging Effects 0.000 description 13
- 230000009466 transformation Effects 0.000 description 13
- 229910000734 martensite Inorganic materials 0.000 description 12
- 230000007423 decrease Effects 0.000 description 11
- 229910052751 metal Inorganic materials 0.000 description 9
- 239000002184 metal Substances 0.000 description 9
- 229910001563 bainite Inorganic materials 0.000 description 8
- 239000011701 zinc Substances 0.000 description 8
- 239000006104 solid solution Substances 0.000 description 7
- 230000032798 delamination Effects 0.000 description 6
- 235000019362 perlite Nutrition 0.000 description 6
- 239000010451 perlite Substances 0.000 description 6
- 230000008569 process Effects 0.000 description 6
- 238000003303 reheating Methods 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- 230000001965 increasing effect Effects 0.000 description 5
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- 206010052428 Wound Diseases 0.000 description 4
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- 230000015572 biosynthetic process Effects 0.000 description 4
- 239000011247 coating layer Substances 0.000 description 4
- 238000010191 image analysis Methods 0.000 description 4
- 150000004767 nitrides Chemical class 0.000 description 4
- 229920005989 resin Polymers 0.000 description 4
- 239000011347 resin Substances 0.000 description 4
- 150000003839 salts Chemical class 0.000 description 4
- 229910001335 Galvanized steel Inorganic materials 0.000 description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 238000010276 construction Methods 0.000 description 3
- 230000002708 enhancing effect Effects 0.000 description 3
- 239000008397 galvanized steel Substances 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- OXNIZHLAWKMVMX-UHFFFAOYSA-N picric acid Chemical compound OC1=C([N+]([O-])=O)C=C([N+]([O-])=O)C=C1[N+]([O-])=O OXNIZHLAWKMVMX-UHFFFAOYSA-N 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 239000013585 weight reducing agent Substances 0.000 description 3
- 229910052725 zinc Inorganic materials 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 229910052796 boron Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 239000003822 epoxy resin Substances 0.000 description 2
- 230000002431 foraging effect Effects 0.000 description 2
- 238000005246 galvanizing Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 230000014759 maintenance of location Effects 0.000 description 2
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- 229930091051 Arenine Natural products 0.000 description 1
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 208000034656 Contusions Diseases 0.000 description 1
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 230000007935 neutral effect Effects 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
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- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
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Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
- 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
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
- 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
- C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—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
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/38—Wires; Tubes
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Definitions
- the present disclosure relates to high strength steel wire.
- high strength steel wires such as rope steel wires, bridge cable steel wires, PC steel wires etc.
- high carbon steel wire is patented and made into pearlite structure, then wire drawn and aged steel wires It is manufactured using.
- a high strength steel wire having a tensile strength of 1960 MPa or more is required for the purpose of reduction of construction cost or weight reduction of a structure.
- high strength steel wire has a small number of revolutions (breaking value) until fracture in a twisting test, and sometimes vertical cracks called delamination may occur, so it is an issue to have both twisting characteristics and high strength. It has become.
- Patent Document 1 proposes a steel wire in which the hardness in the region of 0.1 d (d is the diameter of the wire) is adjusted from the surface layer in the cross section of the steel wire. It is done.
- Patent Document 2 proposes a high-strength galvanized steel wire having a helical processed structure with two or more turns in the same direction with respect to a length per 100 d (d: wire diameter).
- Patent Document 3 the area ratio of non-pearlite structure is 10% or less in the portion of depth from the surface layer to 50 ⁇ m, the area ratio of non-pearlite structure is 5% or less in the entire cross section, and the plating adhesion amount is on the surface
- a galvanized steel wire plated with zinc of 300 to 500 g / m 2 has been proposed.
- Patent Document 4 proposes a method of manufacturing a steel wire which passes tension between steel wires and passes a plurality of rolls at a bending angle after drawing.
- T (20 + log t) 12 12700 (T: bruising temperature indicated by absolute temperature, t: bruce indicated by time) at a temperature of 430 ° C. or higher
- T bruising temperature indicated by absolute temperature
- t bruce indicated by time
- Patent Document 1 Japanese Patent Application Laid-Open No. 2000-336459
- Patent Document 2 Japanese Patent No. 3130445
- Patent Document 3 Japanese Patent No. 5169839
- Patent Document 4 Japanese Patent No. 3725576
- Patent Document No. 5 Japanese Patent No. 2553612
- Patent Document 5 describes that a twisting characteristic can be improved by performing a predetermined bluing treatment on a steel wire after wire drawing.
- a wire rod obtained by hot rolling and cooling by a usual method is reheated in a usual atmosphere (that is, an atmospheric atmosphere), immersed in a molten lead bath, cooled and drawn.
- a predetermined bluing treatment is performed on the obtained steel wire. Therefore, by decarburization of the surface layer portion in the manufacturing process, the area ratio of pearlite structure of the surface layer portion of the steel wire becomes low, and there is a large room for improvement of the twisting characteristics.
- one aspect of the present disclosure is to provide a high-strength steel wire having high strength and excellent twisting characteristics.
- the component composition is in mass%, C: 0.85 to 1.20%, Si: 0.10 to 2.00%, Mn: 0.20 to 1.00%, P: 0.030% or less, S: 0.030% or less, N: 0.0010 to 0.0080%, B: 0 to 0.0050%, Al: 0 to 0.100%, Ti: 0 to 0.050%, Cr: 0 to 0.60%, V: 0 to 0.10%, Nb: 0 to 0.050%, Zr: 0 to 0.050%, and Ni: 0 to 1.00% Containing the balance Fe and impurities,
- the area ratio of pearlite structure in the steel wire is 90% or more
- the area ratio of pearlite structure in the surface layer of the steel wire is 80% or more
- the area ratio of lamellar pearlite structure having an average length of cementite of 1.0 ⁇ m or more is
- the composition of the steel wire is, in mass%, one or more of B: 0.0001 to 0.0050%, Al: 0.001 to 0.100%, and Ti: 0.001 to 0.050%.
- the high strength steel wire as described in ⁇ 1> containing 2 or more types.
- the composition of the steel wire is, in mass%, Cr: 0.01 to 0.60%, V: 0.01 to 0.10%, Nb: 0.001 to 0.050%, Zr: 0.
- the high strength steel wire according to ⁇ 1> or ⁇ 2> containing one or more of 001 to 0.050% and Ni: 0.01 to 1.00%.
- ⁇ 4> The high-strength steel wire according to any one of ⁇ 1> to ⁇ 3>, wherein the diameter of the steel wire is 1.5 to 8.0 mm.
- ⁇ 5> The high strength steel wire according to any one of ⁇ 1> to ⁇ 4>, wherein a plated layer having any one of a Zn layer and a Zn alloy layer is coated on the surface of the steel wire.
- a high strength steel wire having high strength and excellent twisting characteristics is provided.
- FIG. 1 is a schematic view for explaining an observation area for measuring an area ratio of pearlite structure in an inner portion and a surface portion of a steel wire.
- FIG. 2 is a schematic view for explaining an observation area for measuring the area ratio of the lamellar pearlite structure and the area ratio of the divided pearlite structure.
- a numerical range represented using “to” means a range including numerical values described before and after “to” as the lower limit value and the upper limit value. Further, a numerical range in which “super” or “less than” is added to the numerical values described before and after “to” means a range that does not include these numerical values as the lower limit value or the upper limit value.
- the content of the element of the component composition is expressed as an element amount (for example, an amount of C, an amount of Si, etc.).
- “%” means “mass%” about content of the element of a component composition.
- the term “step” is included in the term if the intended purpose of the step is achieved, even if it can not be distinguished clearly from the other steps, not only an independent step.
- a cross section including the central axis of the steel wire and parallel to the central axis includes the central axis of the steel wire and is cut along the longitudinal direction of the steel wire (that is, the drawing direction) parallel to the central axis It shows a cross section.
- the "central axis” indicates an imaginary line extending in the axial direction, passing through the center point of the cross section orthogonal to the axial direction (longitudinal direction) of the steel wire.
- the length of cementite indicates the length of the long axis of cementite in pearlite structure when a cross section including the central axis of the steel wire and parallel to the central axis is observed.
- the inside of a steel wire shows the area
- the surface layer part of a steel wire shows the area
- the high strength steel wire according to the present embodiment is a high strength steel wire having a predetermined component composition and having a metal structure satisfying the following (1) and (2) and having a tensile strength of 1960 MPa or more. .
- the area ratio of the lamellar pearlite structure having an average length of cementite of 1.0 ⁇ m or more among the structures in the entire steel wire is 30% or more and 65% or less, and the average length of cementite is 0
- the area ratio of the divided perlite structure which is 30 ⁇ m or less is 20% or more and 50% or less.
- the high-strength steel wire according to the present embodiment is a steel wire having high strength and excellent twisting characteristics by the above configuration.
- the high strength steel wire according to the present embodiment was found by the following findings.
- the metallographic structure of the steel wire is pearlite, and the lamellar pearlite structure with a long cementite length and the cementite length It is effective to make a mixed structure of short and divided perlite tissue.
- the pearlite structure has a layered structure of cementite phase and ferrite phase.
- the metallographic structure of the drawn steel wire is pearlite structure with fine layer spacing, pearlite structure with irregularly bent layers, pearlite structure with locally sheared layers, etc. Is a heterogeneous and complex organization.
- the inventors investigated in detail the effects of the component composition and the metal structure of the steel wire on the torsion characteristics.
- the present inventors obtained the following findings.
- the area ratio of the non-pearlite structure of the steel wire is reduced (that is, the area ratio of the pearlite structure of the steel wire is increased) and the cementite has a long lamellar pearlite structure and a long length.
- the pearlite structure is a mixture of a divided pearlite structure having a short cementite length, the twisting characteristics are improved even with a high strength steel wire having a tensile strength of 1960 MPa or more.
- the high-strength steel wire according to the present embodiment is a steel wire having high strength and excellent twisting characteristics.
- the high-strength steel wire according to the present embodiment is a steel wire having a tensile strength of 1960 MPa or more and excellent in torsion characteristics, and can be used, for example, as a steel wire for ropes, steel wire for bridge cables, PC steel wire, etc. . Therefore, the high-strength steel wire according to the present embodiment contributes, for example, to weight reduction of civil engineering and buildings and reduction of construction costs, and is extremely useful in industry.
- composition of the high strength steel wire is, in mass%, C: 0.85 to 1.20%, Si: 0.10 to 2.00%, Mn: 0.20 to 1.00%, P: 0. 030% or less, S: 0.030% or less, N: 0.0010 to 0.0080%, B: 0 to 0.0050%, Al: 0 to 0.100%, Ti: 0 to 0.050%, Cr: 0 to 0.60%, V: 0 to 0.10%, Nb: 0 to 0.050%, Zr: 0 to 0.050%, and Ni: 0 to 1.00% It consists of the balance Fe and impurities. However, B, Al, Ti, Cr, V, Nb, Zr, and Ni are optional elements. That is, these elements may not be contained in the high strength steel wire.
- the amount of C is added to secure the tensile strength of the steel wire. If the amount of C is less than 0.85%, pro-eutectoid ferrite is formed, and it is difficult to secure a predetermined tensile strength. On the other hand, when the amount of C exceeds 1.20%, the amount of proeutectoid cementite increases and the wire drawability deteriorates. Therefore, the amount of C is set to 0.85 to 1.20%.
- the lower limit of the preferable C amount to achieve both high strength and wire drawability is 0.90%.
- the upper limit of the preferable C amount which makes high strength and wire-drawing workability compatible is 1.10%.
- Si has the effect of enhancing tensile strength by solid solution strengthening, as well as enhancing the relaxation characteristics. If the amount of Si is less than 0.10%, these effects are insufficient. When the amount of Si exceeds 2.00%, these effects are saturated and the hot ductility is deteriorated to lower the manufacturability. Therefore, the amount of Si is set to 0.10 to 2.00%.
- the lower limit of the preferred amount of Si is 0.50%. More preferably, the lower limit of the amount of Si may be 1.00%.
- the upper limit of the preferable amount of Si is 1.80%. The upper limit of the amount of Si is more preferably 1.50%.
- Mn has the effect of increasing the tensile strength of the steel after pearlite transformation. If the amount of Mn is less than 0.20%, the effect is insufficient. When the amount of Mn exceeds 1.00%, the effect is saturated. Therefore, the amount of Mn is set to 0.20 to 1.00%.
- the lower limit of the preferable amount of Mn is 0.30%.
- the upper limit of the preferable amount of Mn is 0.90%.
- P and S are contained in the steel wire as impurities. P and S should be suppressed because they deteriorate ductility. Therefore, the upper limit of both P amount and S amount was made into 0.030%.
- the upper limit of preferable P amount and S amount is 0.020%.
- the upper limit of more preferable P amount and S amount is 0.015% or less.
- the lower limit of P amount and S amount is preferably 0% (that is, although it is good not to include), it is more than 0% (or 0.0001% or more) from the viewpoint of reducing de-P cost and desulfurization cost. Good to have.
- N forms nitrides with Al, Ti, Nb, V, etc., and has the effect of refining the grain size and improving the ductility. If the amount of N is less than 0.0010%, these effects are not obtained. If the amount of N exceeds 0.0080%, wire drawability and ductility are deteriorated. Therefore, the N content is set to 0.0010 to 0.0080%.
- the lower limit of the preferable N amount is 0.0020%.
- the upper limit of the preferable N amount is 0.0060%.
- the upper limit of the more preferable N amount is 0.0050%.
- B 0.0001 to 0.0050%
- Al 0.001 to 100% by mass. It may contain one or more of 0.100% and Ti: 0.001 to 0.050%.
- the B is segregated at grain boundaries as solid solution B to suppress the formation of non-pearlite structure, and has an effect of improving twisting characteristics and wire drawability. If the B content exceeds 0.0050%, carbides may be formed at grain boundaries to deteriorate drawability. Therefore, the B content is preferably 0.0001 to 0.0050%.
- the lower limit of the preferable B amount is 0.0005%.
- the upper limit of the preferable B amount is 0.0030%.
- the upper limit of the amount of B is more preferably 0.0020%.
- Al functions as a deoxidizing element.
- Al has the effect of forming AlN to refine crystal grains and improving ductility, the effect of reducing solid solution N and improving ductility, and promoting the formation of solid solution B to form a non-pearlite structure.
- the Al content is preferably 0.001 to 0.100%.
- the lower limit of the preferred amount of Al is 0.010%.
- the lower limit of the amount of Al is more preferably 0.020%.
- the upper limit of the preferable amount of Al is 0.080%.
- the upper limit of the amount of Al is more preferably 0.070%.
- Ti functions as a deoxidizing element.
- Ti precipitates carbides and nitrides to increase tensile strength, reduces grain size to improve ductility, reduces solid solution N, and improves wire drawability, solid There is an effect of promoting the formation of melt B, suppressing the formation of non-pearlite structure, and improving the twist characteristics and wire drawability.
- the amount of Ti is preferably 0.001 to 0.050%.
- the lower limit of the preferred amount of Ti is 0.010%.
- the upper limit of the preferable Ti amount is 0.030%.
- the upper limit of the amount of Ti is more preferably 0.025%.
- the high strength steel wire according to the present embodiment has Cr: 0.01 to 0.60%, V: 0.01 to 0.10%, Nb: 0.001 to 200 for the purpose of improving the characteristics described below. It may contain one or more of 0.050%, Zr: 0.001 to 0.050%, and Ni: 0.01 to 1.00%.
- the Cr has the effect of increasing the tensile strength of the steel after pearlite transformation.
- the amount of Cr exceeds 0.60%, a martensitic structure tends to be formed, which may deteriorate wire drawability and twisting characteristics.
- the amount of Cr is preferably 0.01 to 0.60%.
- the upper limit of the preferable amount of Cr is 0.50%.
- the upper limit of the amount of Cr is more preferably 0.40%.
- V has the effect of precipitating carbide VC and enhancing the tensile strength. If the V content exceeds 0.10%, the alloy cost may increase and the twisting characteristics may be degraded. Therefore, the V content is preferably 0.01 to 0.10%.
- the upper limit of the preferable V amount is 0.08%.
- the upper limit of the more preferable V amount is 0.07%.
- Nb has an effect of precipitating carbides and nitrides to enhance tensile strength, an effect of refining crystal grains to improve ductility, and an effect of reducing solid solution N to improve wire drawability.
- the Nb content is preferably 0.001 to 0.050%.
- the upper limit of the preferable Nb amount is 0.030%.
- the upper limit of the more preferable Nb amount is 0.020%.
- Zr functions as a deoxidizing element. Further, Zr has the effect of reducing the solid solution S by forming a sulfide and improving the ductility. If the Zr content exceeds 0.050%, these effects saturate and coarse oxides may be formed, which may deteriorate wire drawability. Therefore, the amount of Zr is preferably 0.001 to 0.050%. The upper limit of the preferable amount of Zr is 0.030%. The upper limit of the more preferable amount of Zr is 0.020%.
- Ni has the effect of suppressing the penetration of hydrogen and improving the resistance to hydrogen embrittlement.
- the amount of Ni exceeds 1.00%, the alloy cost is increased, and a martensitic structure is easily formed, which may deteriorate wire drawability. Therefore, the amount of Ni is preferably 0.01 to 1.00%.
- the upper limit of the preferable amount of Ni is 0.50%.
- the upper limit of the amount of Ni is more preferably 0.30%.
- the balance is Fe and impurities.
- impurity refers to a component contained in the raw material or a component which is mixed in the process of production and is not intentionally contained. Furthermore, the impurities also include components that are intentionally contained, but in an amount that does not affect the performance of the steel wire.
- O etc. are mentioned, for example. O is unavoidably contained in the steel wire and exists as an oxide such as Al or Ti. When the amount of O is high, coarse oxides are formed, which causes breakage during wire drawing. Therefore, it is preferable to suppress the amount of O to 0.010% or less.
- the area ratio of pearlite structure in the steel wire is 90% or more, and the area ratio of pearlite structure in the surface layer of the steel wire is 80% or more.
- the area ratio of the pearlite structure is an area ratio in a cross section including the central axis of the line and parallel to the central axis.
- the lower limit of the area ratio of pearlite structure is set to 90%.
- the lower limit of the area ratio of the preferred perlite structure is 95%.
- the lower limit of the area ratio of the more preferable pearlite structure is 97%.
- the upper limit of the area ratio of the pearlite structure may be 100% or 99%.
- the remaining structure i.e., non-pearlite structure
- pearlite structure is ferrite, bainite, tempered bainite, martensite, tempered martensite, proeutectoid cementite or the like.
- the lower limit of the area ratio of pearlite structure in the surface layer portion of the steel wire is set to 80%.
- the lower limit of the area ratio of the preferred pearlite structure is 85%.
- the lower limit of the area ratio of the more preferable pearlite structure is 90%.
- the upper limit of the area ratio of the pearlite structure may be 95% or 99%.
- the area ratio of the perlite structure may be 100%.
- a method of setting the area ratio of the pearlite structure of the surface layer portion of the steel wire to 80% or more for example, a method of containing B and further containing at least one of Al and Ti, or hot There is a method of controlling the cooling rate of the wire after rolling. By performing either or both of these methods, it is possible to increase the area ratio of pearlite structure in the surface layer of the steel wire.
- the remaining structure i.e. non-pearlite structure
- pearlite structure is ferrite, bainite, tempered bainite, martensite, tempered martensite, proeutectoid cementite or the like.
- a lamellar pearlite structure having a long cementite length and a divided pearlite structure having a short cementite length are used. It is effective to make the pearlite tissue mixed in an appropriate ratio.
- the steel wire in this embodiment has a non-uniform and complicated structure including the dislocation introduced by wire drawing after wire drawing and before the aging treatment.
- ordinary hot dip galvanizing treatment or equivalent aging treatment with heat treatment
- the microscopic mechanical properties after plating treatment or after aging treatment
- Such a steel wire has a small twist value because it locally deforms when subjected to torsional deformation.
- appropriate aging treatment or plating treatment under appropriate conditions
- the "lamellar pearlite structure” as used herein refers to a pearlite structure in which cementite has a long length and an average length of 1.0 ⁇ m or more.
- the part having a relatively small influence by the aging treatment is a lamellar pearlite structure. If the area ratio of the lamellar pearlite structure is less than 30%, the strength is reduced (that is, it is difficult to obtain a strength of 1960 MPa or more), and if it exceeds 65%, the twisting property is degraded. Therefore, the area ratio of the lamellar pearlite structure is 30% or more and 65% or less.
- the lower limit of the area ratio of the preferred lamellar perlite structure is 40%, more preferably 50%.
- the upper limit of the area ratio of the preferred lamellar pearlite structure is 60%.
- the "divided perlite structure" as used herein refers to a pearlite structure having a short cementite length and an average length of 0.30 ⁇ m or less.
- the strain formed by wire drawing and the structure formed as a result of the cementite in the pearlite being divided by the influence of the aging treatment is a divided pearlite structure.
- the area ratio of the divided pearlite structure is set to 20% or more and 50% or less.
- the lower limit of the area ratio of the preferable split pearlite structure is 25%, and the more preferable lower limit is 30%.
- the upper limit of the area ratio of a preferable divided pearlite structure is 45%, more preferably 40%.
- the method of setting the area ratio of split pearlite structure of steel wire to 20% or more and 50% or less is, for example, 80% or more of area ratio of pearlite structure of surface layer portion after wire drawing at a total reduction ratio of 65 to 95%.
- There is a method of holding the steel wire which is at 500 to 600 ° C. for 1 s or more and 20 s or less, or a method for holding the steel wire at 420 to 480 ° C. for 60 s or more and 600 s or less.
- the measurement method of the organization was as follows.
- the area ratio of the pearlite structure inside the steel wire is determined by the following procedure.
- a cross section including the central axis of the steel wire and parallel to the central axis (hereinafter also referred to as “L cross section”) is etched with picral to reveal a metal structure.
- a metallographic structure in a region of 50 ⁇ m in the radial direction of the steel wire ⁇ 60 ⁇ m in the longitudinal direction of the steel wire is photographed at a magnification of 2000 times by a SEM (scanning electron microscope).
- the location of the SEM photograph of the metallographic structure is a position of a depth of 0.25 D in the radial direction of the steel wire from the surface (that is, the outer peripheral surface) of the steel wire and At a depth of 0.5 D from the surface in the radial direction of the steel wire, three points are provided at intervals of 5 mm in the longitudinal direction of the steel wire, for a total of six places (see FIG. 1).
- OA1 shows the area
- Non-perlite structures structures of ferrite, bainite, tempered bainite, martensite, tempered martensite, and proeutectoid cementite
- the percent area of pearlite tissue is determined by subtracting the area of non-perlite tissue from the entire field of view. And this is measured about two samples, and let the average value of a total of 12 measured be the area ratio of the pearlite structure
- the pearlite structure of the surface layer portion of the steel wire is determined according to the following procedure.
- the L cross section of the steel wire is etched with picral to reveal a metallographic structure.
- the metallographic structure in the region of 50 ⁇ m from the surface in the depth direction (radial direction of the steel wire) and 60 ⁇ m in the longitudinal direction of the steel wire, including the surface of the steel wire, is photographed by SEM at 2000 ⁇ magnification.
- the places where the SEM photograph of the metal structure is taken are six places at intervals of 5 mm in the longitudinal direction of the steel wire (see FIG. 1).
- OA2 shows the area
- Non-perlite structures structures of ferrite, bainite, tempered bainite, martensite, tempered martensite, and proeutectoid cementite
- the area ratio is determined by image analysis.
- the percent area of pearlite tissue is determined by subtracting the area of non-perlite tissue from the entire field of view. And this was measured about two samples, and the average value of a total of 12 measured was made into the area ratio of the pearlite structure of the surface layer part of a steel wire.
- the area ratio of the lamellar pearlite structure and the area ratio of the divided perlite structure are determined according to the following procedure.
- the L cross section of the steel wire is etched with picral to reveal a metallographic structure.
- a metallographic structure in a region of 8 ⁇ m in the radial direction of the steel wire ⁇ 12 ⁇ m in the longitudinal direction of the steel wire is photographed at a magnification of 10000 by SEM.
- the location of the SEM photograph of the metallographic structure is 50 ⁇ m deep from the surface of the steel wire to the radial direction of the steel wire, and from the surface of the steel wire to the radial direction of the steel wire Three points at a distance of 5 mm in the direction parallel to the longitudinal direction of the steel wire, at a position of depth of 0.25 D and at a position of depth of 0.5 D in the radial direction of the steel wire from the surface of the steel wire There are nine places (see Figure 2). Note that, in FIG. 2, OA indicates an area for taking a SEM photograph.
- the area ratio of the divided perlite structure is also the same procedure as described above, and the SEM photograph of the metal structure is taken, and the length of the long axis of cementite is measured by image analysis in three cementite close to each intersection where the perlite structure exists. Then, the average value of the long axis lengths of cementite (that is, the average length) is determined. Determine the number of intersections where the average value of the major axis lengths of three cementite in the vicinity of the intersection is 0.30 ⁇ m or less, and calculate the percentage of the value divided by the number of all intersections including the intersection where there is no pearlite structure , And the area ratio of the divided perlite structure.
- the tensile strength of the high strength steel wire will be described. If the tensile strength of the steel wire is less than 1960 MPa, for example, when the steel wire is applied to a civil engineering / building structure application, the effects of reduction in construction cost and weight reduction become small. Therefore, the lower limit of the tensile strength of the steel wire is set to 1960 MPa.
- the upper limit of the tensile strength of the steel wire is not particularly limited, but if the tensile strength is too high, the ductility may be reduced and cracking may occur when wire drawing is performed. In this respect, the upper limit of the tensile strength of the steel wire is preferably 3000 MPa (preferably 2800 MPa, more preferably 2500 MPa).
- the high-strength steel wire according to the present embodiment may be a high-strength steel wire used for a rope steel wire, a bridge cable steel wire, a PC steel wire, and the like. Therefore, if the wire diameter (diameter) of the steel wire is less than 1.5 mm, the cost at the time of manufacturing these products increases, and if it exceeds 8.0 mm, the strength and twisting characteristics are easily deteriorated. Therefore, the wire diameter (diameter) of the steel wire is preferably 1.5 mm to 8.0 mm. A more preferable range of the wire diameter (diameter) of the steel wire is 3.0 mm to 7.5 mm.
- a plating layer having any one of a Zn layer and a Zn alloy layer may be coated on the surface of the steel wire.
- the Zn alloy layer include a ZnAl layer, a ZnAlMg alloy layer, and the like.
- the high strength steel wire used for the steel wire for ropes, the steel wire for bridge cables, etc. may use the steel wire by which the surface was plated. And, even if the surface is plated, the high strength steel wire according to this embodiment is a steel wire which is high in strength and excellent in twisting characteristics.
- the surface of the steel wire or the surface of the plated steel wire may be coated with a resin coating layer (for example, an epoxy resin layer).
- Method of manufacturing high strength steel wire An example of the manufacturing method of the high strength steel wire concerning this embodiment is explained.
- a steel piece having the component composition of the high strength steel wire according to the present embodiment is heated to 1000 to 1150 ° C., and thermal rolling is performed at a finish rolling temperature of 850 to 1000 ° C. It has a process of obtaining a wire rod by rolling.
- modes (1) to (6) having the following steps can be mentioned as steps after the step of obtaining a wire rod.
- a steel piece having the component composition of the high strength steel wire according to the present embodiment is heated to 1000 to 1150 ° C.
- the heating temperature is less than 1000 ° C.
- deformation resistance in hot rolling increases and rolling cost increases.
- the heating temperature exceeds 1150 ° C.
- the lower limit of the preferred heating temperature range is 1050.degree.
- the upper limit of the preferred heating temperature range is 1100 ° C.
- the heated billet is hot-rolled at a finish rolling temperature of 850 to 1000 ° C. to obtain a wire rod.
- a finish rolling temperature 850 to 1000 ° C.
- deformation resistance in hot rolling increases and rolling cost increases.
- finish rolling temperature exceeds 1000 ° C.
- the lower limit of the preferred finish rolling temperature range is 870 ° C.
- the upper limit of the preferred finish rolling temperature range is 980 ° C.
- the finish rolling temperature refers to the surface temperature of the wire immediately after finish rolling.
- the wire rod at 850 to 1000 ° C. is cooled to 500 to 600 ° C. at an average cooling rate of 30 to 80 ° C./s from 800 ° C. to 600 ° C. Do.
- the average cooling rate is less than 30 ° C./s, the area ratio of the non-pearlite structure in the surface layer increases, and the wire drawability and the twisting property deteriorate.
- the manufacturing cost increases.
- the lower limit of the preferred average cooling rate range is 40 ° C./s.
- the upper limit of the preferable average cooling rate range is 75 ° C./s.
- an average cooling rate refers to the surface cooling rate of a wire.
- the cooling temperature is less than 500 ° C.
- the pearlite area ratio becomes small, and the twisting characteristics deteriorate.
- the cooling temperature exceeds 600 ° C.
- the strength decreases.
- the lower limit of the preferred cooling temperature range is 530.degree.
- the upper limit of the preferred cooling temperature range is 580 ° C.
- the wire after cooling to 500 to 600 ° C. is subjected to pearlite transformation treatment by holding the wire at 500 to 600 ° C. for 50 seconds or more.
- the holding temperature is less than 500 ° C.
- the pearlite area ratio becomes small, and the twisting characteristics deteriorate.
- the holding temperature exceeds 600 ° C., the strength decreases.
- the lower limit of the preferred holding temperature range is 530 ° C.
- the upper limit of the preferred holding temperature range is 580 ° C. If the holding time is less than 50 s, pearlite transformation is incomplete, martensite is formed, and wire drawability and twisting characteristics deteriorate.
- the upper limit of the holding time is preferably 150 s.
- the lower limit of the preferred holding time range is 60 s.
- the upper limit of the preferred holding time range is 120 s.
- the holding at 500 to 600 ° C. is performed, for example, by a molten salt bath.
- the wire rod at 850 to 1000 ° C. is cooled at an average cooling rate of 700 to 550 ° C. at 1.0 to 5.0 ° C./s
- the cooling is performed by, for example, a blast cooling facility such as Stelmore. If the average cooling rate is less than 1.0 ° C./s, the strength decreases. When the average cooling rate exceeds 5.0 ° C./s, microscopic variations in strength and metallographic structure become large, and the torsion characteristics deteriorate.
- the lower limit of the preferred average cooling rate range is 1.2 ° C./s.
- the upper limit of the preferred average cooling rate range is 3.0 ° C./s.
- the wire rod cooled to room temperature (for example 25 ° C.) is reheated to 800 to 1050 ° C. and held for 20 s or more at 480 to 600 ° C.
- room temperature for example 25 ° C.
- the austenitizing is insufficient and a uniform pearlite structure can not be obtained, and the strength is lowered and the wire drawability is deteriorated.
- the reheating temperature exceeds 1050 ° C., the area ratio of the non-pearlite structure in the surface layer increases, and the wire drawability and the twisting property deteriorate.
- the lower limit of the preferred reheating temperature range is 940 ° C.
- the upper limit of the preferred reheating temperature range is 1020 ° C.
- the holding temperature is less than 480 ° C.
- the area ratio of pearlite structure decreases and the twisting characteristics deteriorate.
- the holding temperature exceeds 600 ° C.
- the lamellar spacing of the perlite structure increases and the strength decreases.
- the lower limit of the preferred holding temperature range is 520 ° C.
- the upper limit of the preferred holding temperature range is 590.degree. If the holding time is less than 20 s, pearlite transformation becomes incomplete, martensite is formed, and wire drawability and twisting characteristics deteriorate.
- the upper limit of the holding time is preferably 120 s.
- the lower limit of the preferred retention time range is 30 s.
- the upper limit of the preferred retention time range is 80 s.
- the atmosphere for the reheat heat treatment is, for example, an inert gas (such as Ar gas), a neutral gas (such as nitrogen gas), or an endothermic modified gas.
- the reheating treatment may be heating for a short time such as induction heating.
- the holding at 480 to 600 ° C. is performed, for example, in a molten lead bath. Instead of the molten lead bath, a molten salt bath, a fluidized bed or the like may be used.
- the wire rod after the above pearlite transformation treatment or after cooling (specifically, the wire rod after cooling to room temperature (for example, 25 ° C.) is drawn at a total reduction of 65 to 95%, and 500 to 600 ° C. Hold for 1 s or more and 20 s or less to obtain a steel wire. By holding at 500 to 600 ° C. for 1 s or more and 20 s or less, the twisting characteristic is improved.
- the heat treatment after wire drawing is also referred to as "aging treatment”. If the total reduction rate is less than 65%, the strength decreases. If the total area reduction rate exceeds 95%, the ductility of the steel wire is reduced, and the wire drawability and twisting characteristics are degraded.
- the preferred total reduction rate is 70 to 90%.
- the total area reduction rate is the difference between the cross-sectional area of the wire before drawing (the area of the surface perpendicular to the longitudinal direction of the wire) and the cross-sectional area of the steel wire after drawing / wire drawing It is a value calculated by cross section area of wire before processing ⁇ 100.
- the holding temperature is less than 500 ° C., there is no effect of improving the twisting characteristics.
- the holding temperature exceeds 600 ° C., the strength decreases.
- the preferred holding temperature range is 510-550.degree. If the holding time is less than 1 s, there is no effect of improving the twisting characteristics. If the holding time exceeds 20 s, the strength decreases.
- the preferred holding temperature range is 2 to 15 s.
- the holding temperature is less than 420 ° C., the twisting characteristic is degraded.
- the preferred holding temperature range is 430-470.degree. If the holding time is less than 60 s, the twisting characteristics deteriorate. If the holding time exceeds 600 s, the manufacturing cost increases.
- the preferred holding temperature range is 100 to 500 s.
- the manufacturing method of the high strength steel wire according to the present embodiment is a step of performing plating treatment at 420 to 480 ° C. for covering the plating layer having any one of Zn layer and Zn alloy layer after the above-mentioned aging treatment May be included.
- Plating treatment for coating a plating layer having a Zn layer and any one layer of Zn alloy layer on the surface of a steel wire is performed under the conditions of 60s to 600s at 420 to 480 ° C, or 1s to 20s at 500 to 600 ° C. You may have the process performed on condition of the following. Also in this case, a similar structure is formed on the steel wire due to the temperature change of the steel wire accompanying the plating process.
- the surface of the steel wire is plated under the conditions of temperature and time corresponding to the above-mentioned aging treatment to provide the structural state of the steel wire according to the present embodiment, and any of the Zn layer and the Zn alloy layer A high strength steel wire coated with a plating layer having one layer is obtained.
- the method for manufacturing a high strength steel wire according to the present embodiment further includes the step of covering the surface of the steel wire or the surface of the plated steel wire with a resin coating layer (for example, an epoxy resin layer). May be Even if the resin coating layer is present, excellent strength and twisting characteristics can be realized as long as the steel wire present inside the resin coating layer has the structure state of the steel wire according to the present embodiment.
- a resin coating layer for example, an epoxy resin layer
- a steel wire was manufactured as follows using the steel pieces of steel types A to S having the component compositions shown in Table 1 under the conditions shown in Tables 2 to 6.
- steel wires of test numbers 1 to 30 shown in Table 2 were manufactured as follows. First, after heating a steel piece, it was hot-rolled, and the obtained wire was wound into a ring and cooled to 500 to 600.degree. Next, the obtained wire was immersed in a molten salt bath at the rear of a hot rolling line to perform patenting (perlite transformation). Thereafter, the wire rod cooled to room temperature (25 ° C.) was drawn to the wire diameter shown in Table 2 (denoted as the wire diameter after wire drawing), and after heating, it was heated and aged. Through these steps, steel wires shown in Test Nos. 1 to 30 were produced.
- the steel wires of test numbers 31 to 34 shown in Table 3 were manufactured as follows. First, after heating a steel piece, it hot-rolled, wound the obtained wire rod like ring shape, and carried out blast cooling. Thereafter, the wire rod cooled to room temperature (25 ° C.) was drawn to the wire diameter shown in Table 3, and after the drawing, it was heated and aged. Through these steps, steel wires shown in Test Nos. 31 to 34 were manufactured.
- steel wires of test numbers 35 to 40 shown in Table 4 were manufactured as follows. After heating the billet, it was hot-rolled, and the obtained wire was wound into a ring, and cooled at an average cooling rate of 2.0 ° C./s. Next, the wire rod cooled to room temperature (25 ° C.) was reheated in a predetermined atmosphere and immersed in a molten lead bath. Thereafter, the wire rod cooled to room temperature (25 ° C.) was subjected to wire drawing to the wire diameter shown in Table 4, and after the wire drawing was heated for aging treatment. Through these steps, steel wires shown in Test Nos. 35 to 40 were manufactured.
- the steel wire of the test number 41 shown in Table 5 was manufactured as follows. First, after heating a steel piece, it was hot-rolled, and the obtained wire was wound into a ring and cooled to 500 to 600.degree. Next, the obtained wire rod was dipped in a molten salt bath after the hot rolling line for patenting treatment. Thereafter, the wire rod cooled to room temperature (25 ° C.) was subjected to wire drawing to the wire diameter shown in Table 5, and after the wire drawing was heated for aging treatment. Thereafter, it was subjected to hot dip galvanization treatment. Through these steps, a steel wire shown in Test No. 41 was manufactured.
- the steel wire of the test number 42 shown in Table 6 was manufactured like the steel wire of the test number 22 except having changed the order of wiredrawing and aging treatment.
- the steel wires of test numbers 1 to 11, 21 to 25, 30 to 32, 35 to 38, and 41 that satisfy all the requirements specified in the present disclosure have a tensile strength of 1960 MPa or more and a twisting characteristic of It turns out that it is good.
- the area ratio of pearlite structure is less than the lower limit of the present disclosure.
- the area ratio of the divided perlite structure is out of the range of the present disclosure.
- the steel wires of test numbers 18 and 40 the area ratio of pearlite structure in the surface layer portion is lower than the lower limit of the present disclosure.
- the steel wire of test number 40 is an example corresponded to the steel wire of patent document 5.
- the area ratio of the lamellar pearlite structure exceeds the upper limit of the present disclosure.
- the area ratio of the lamellar pearlite structure and the area ratio of the divided perlite structure are out of the scope of the present disclosure.
- the steel wires of test numbers 15 and 34 are any of the area ratio of pearlite structure inside the steel wire, the area ratio of pearlite structure of the surface layer of the steel wire, the area ratio of lamellar pearlite structure, and the area ratio of divided pearlite structure
- the thigh is out of the scope of the present disclosure.
- the test numbers 19, 20 have a C amount outside the scope of the present disclosure.
- any of the steel wires outside the scope of the present disclosure has poor twisting characteristics or insufficient tensile strength of the steel wire.
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Abstract
Description
特許文献2では、100d(d:線径)当たりの長さに対して同一方向に2回転以上のらせん状の加工組織を有する高強度亜鉛めっき鋼線が提案されている。
特許文献3では、表層から50μmまでの深さの部分において非パーライト組織の面積率が10%以下であり、全断面において非パーライト組織の面積率が5%以下であり、表面に、めっき付着量が300~500g/m2の亜鉛めっきが施されためっき鋼線が提案されている。 As a technique for improving the torsion characteristics of high strength steel wires, Patent Document 1 proposes a steel wire in which the hardness in the region of 0.1 d (d is the diameter of the wire) is adjusted from the surface layer in the cross section of the steel wire. It is done.
In Patent Document 3, the area ratio of non-pearlite structure is 10% or less in the portion of depth from the surface layer to 50 μm, the area ratio of non-pearlite structure is 5% or less in the entire cross section, and the plating adhesion amount is on the surface A galvanized steel wire plated with zinc of 300 to 500 g / m 2 has been proposed.
特許文献5では、伸線後、亜鉛めっき前に430℃以上の温度でT(20+log t)≧12700(T:絶対温度で表示されるブルーイング温度、t:時間で表示されるブルーイング時間)なる関係を満足するようにブルーイング処理する亜鉛めっき鋼線の製造方法が提案されている。 Patent Document 4 proposes a method of manufacturing a steel wire which passes tension between steel wires and passes a plurality of rolls at a bending angle after drawing.
In Patent Document 5, after drawing, before zinc plating, T (20 + log t) 12 12700 (T: bruising temperature indicated by absolute temperature, t: bruce indicated by time) at a temperature of 430 ° C. or higher There has been proposed a method of producing a galvanized steel wire which is subjected to a bluing treatment so as to satisfy the following relationship.
特許文献2:特許第3130445号公報
特許文献3:特許第5169839号公報
特許文献4:特許第3725576号公報
特許文献5:特許第2553612号公報 Patent Document 1: Japanese Patent Application Laid-Open No. 2000-336459 Patent Document 2: Japanese Patent No. 3130445 Patent Document 3: Japanese Patent No. 5169839 Patent Document 4: Japanese Patent No. 3725576 Patent Document No. 5: Japanese Patent No. 2553612
ここで、特許文献5では、伸線加工後の鋼線に対して、所定のブルーイング処理を実施することで、捻回特性を向上できることが記載されている。しかし、特許文献5では、通常の方法で熱間圧延、冷却して得られた線材を、通常の雰囲気(つまり、大気雰囲気)で再加熱し、溶融鉛浴浸漬、冷却および伸線加工を経て得られた鋼線に対して、所定のブルーイング処理を実施している。そのため、製造過程での表層部の脱炭によって、鋼線の表層部のパーライト組織の面積率が低くなり、捻回特性の改善の余地が大きい。 However, when the tensile strength of the conventional high strength steel wire is increased, the twisting characteristics become unstable, so that the twisting value can not be improved and the occurrence of delamination can not be sufficiently suppressed. At present, coexistence of twisting characteristics and high strength is an issue.
Here, Patent Document 5 describes that a twisting characteristic can be improved by performing a predetermined bluing treatment on a steel wire after wire drawing. However, in Patent Document 5, a wire rod obtained by hot rolling and cooling by a usual method is reheated in a usual atmosphere (that is, an atmospheric atmosphere), immersed in a molten lead bath, cooled and drawn. A predetermined bluing treatment is performed on the obtained steel wire. Therefore, by decarburization of the surface layer portion in the manufacturing process, the area ratio of pearlite structure of the surface layer portion of the steel wire becomes low, and there is a large room for improvement of the twisting characteristics.
成分組成が、質量%で、
C :0.85~1.20%、
Si:0.10~2.00%、
Mn:0.20~1.00%、
P :0.030%以下、
S :0.030%以下、
N :0.0010~0.0080%、
B :0~0.0050%、
Al:0~0.100%、
Ti:0~0.050%、
Cr:0~0.60%、
V :0~0.10%、
Nb:0~0.050%、
Zr:0~0.050%、および、
Ni:0~1.00%
を含有し、残部Fe及び不純物からなり、
鋼線の中心軸を含み中心軸に平行な断面において、鋼線の内部のパーライト組織の面積率が90%以上であり、鋼線の表層部のパーライト組織の面積率が80%以上であり、
前記鋼線の全体における組織のうち、セメンタイトの平均長さが1.0μm以上であるラメラ状パーライト組織の面積率が30%以上65%以下であり、かつ、セメンタイトの平均長さが0.30μm以下である分断パーライト組織の面積率が20%以上50%以下であり、
かつ、引張強さが1960MPa以上である高強度鋼線。
<2>
鋼線の成分組成が、質量%で、更に、B:0.0001~0.0050%、Al:0.001~0.100%、およびTi:0.001~0.050%の1種または2種以上を含有する<1>に記載の高強度鋼線。
<3>
鋼線の成分組成が、質量%で、更に、Cr:0.01~0.60%、V:0.01~0.10%、Nb:0.001~0.050%、Zr:0.001~0.050%、およびNi:0.01~1.00%の1種または2種以上を含有する<1>又は<2>に記載の高強度鋼線。
<4>
前記鋼線の直径が、1.5~8.0mmである<1>~<3>のいずれか1項に記載の高強度鋼線。
<5>
前記鋼線の表面に、Zn層、およびZn合金層のいずれか1層を有するめっき層が被覆されている<1>~<4>のいずれか1項に記載の高強度鋼線。 <1>
The component composition is in mass%,
C: 0.85 to 1.20%,
Si: 0.10 to 2.00%,
Mn: 0.20 to 1.00%,
P: 0.030% or less,
S: 0.030% or less,
N: 0.0010 to 0.0080%,
B: 0 to 0.0050%,
Al: 0 to 0.100%,
Ti: 0 to 0.050%,
Cr: 0 to 0.60%,
V: 0 to 0.10%,
Nb: 0 to 0.050%,
Zr: 0 to 0.050%, and
Ni: 0 to 1.00%
Containing the balance Fe and impurities,
In a cross section including the central axis of the steel wire and parallel to the central axis, the area ratio of pearlite structure in the steel wire is 90% or more, and the area ratio of pearlite structure in the surface layer of the steel wire is 80% or more,
Among the structures in the entire steel wire, the area ratio of lamellar pearlite structure having an average length of cementite of 1.0 μm or more is 30% to 65%, and the average length of cementite is 0.30 μm The area ratio of the divided perlite structure which is less than or equal to 20% and less than or equal to 50%,
And, a high strength steel wire having a tensile strength of 1960 MPa or more.
<2>
The composition of the steel wire is, in mass%, one or more of B: 0.0001 to 0.0050%, Al: 0.001 to 0.100%, and Ti: 0.001 to 0.050%. The high strength steel wire as described in <1> containing 2 or more types.
<3>
The composition of the steel wire is, in mass%, Cr: 0.01 to 0.60%, V: 0.01 to 0.10%, Nb: 0.001 to 0.050%, Zr: 0. The high strength steel wire according to <1> or <2>, containing one or more of 001 to 0.050% and Ni: 0.01 to 1.00%.
<4>
The high-strength steel wire according to any one of <1> to <3>, wherein the diameter of the steel wire is 1.5 to 8.0 mm.
<5>
The high strength steel wire according to any one of <1> to <4>, wherein a plated layer having any one of a Zn layer and a Zn alloy layer is coated on the surface of the steel wire.
なお、本明細書中において、「~」を用いて表される数値範囲は、「~」の前後に記載される数値を下限値及び上限値として含む範囲を意味する。
また、「~」の前後に記載される数値に「超」または「未満」が付されている場合の数値範囲は、これら数値を下限値または上限値として含まない範囲を意味する。
また、成分組成の元素の含有量は、元素量(例えば、C量、Si量等)と表記する。
また、成分組成の元素の含有量について、「%」は「質量%」を意味する。
また、「工程」との用語は、独立した工程だけではなく、他の工程と明確に区別できない場合であってもその工程の所期の目的が達成されれば、本用語に含まれる。 An embodiment which is an example of the present disclosure will be described.
In the present specification, a numerical range represented using “to” means a range including numerical values described before and after “to” as the lower limit value and the upper limit value.
Further, a numerical range in which “super” or “less than” is added to the numerical values described before and after “to” means a range that does not include these numerical values as the lower limit value or the upper limit value.
Further, the content of the element of the component composition is expressed as an element amount (for example, an amount of C, an amount of Si, etc.).
Moreover, "%" means "mass%" about content of the element of a component composition.
Also, the term "step" is included in the term if the intended purpose of the step is achieved, even if it can not be distinguished clearly from the other steps, not only an independent step.
また、「中心軸」とは、鋼線の軸方向(長手方向)と直交する断面の中心点を通り、軸方向に延びる仮想線を示す。
また、「セメンタイトの長さ」とは、鋼線の中心軸を含み中心軸に平行な断面を観察した場合の、パーライト組織内におけるセメンタイトの長軸の長さを示す。
また、「鋼線の内部」とは、鋼線の表面から、中心軸に向かって(径方向に向かって)、100μmを超えた深さの領域を示す。
また、「鋼線の表層部」とは、鋼線の表面から、中心軸に向かって(径方向に向かって)、100μmまでの深さの領域を示す。
また、「XD」(X=数値)との表記は、鋼線の直径をDとしたとき、鋼線の表面から、中心軸に向かって(径方向に向かって)、直径DのX倍の深さの位置を示す。例えば、「0.25D」は、直径Dの0.25倍の深さの位置を示す。 Also, "a cross section including the central axis of the steel wire and parallel to the central axis" includes the central axis of the steel wire and is cut along the longitudinal direction of the steel wire (that is, the drawing direction) parallel to the central axis It shows a cross section.
The "central axis" indicates an imaginary line extending in the axial direction, passing through the center point of the cross section orthogonal to the axial direction (longitudinal direction) of the steel wire.
Moreover, "the length of cementite" indicates the length of the long axis of cementite in pearlite structure when a cross section including the central axis of the steel wire and parallel to the central axis is observed.
Moreover, "the inside of a steel wire" shows the area | region of the depth which exceeded 100 micrometers toward the central axis (toward the radial direction) from the surface of a steel wire.
Moreover, "the surface layer part of a steel wire" shows the area | region of the depth to 100 micrometers toward the central axis (in the radial direction) from the surface of a steel wire.
In addition, the notation “XD” (X = numerical value) indicates that when the diameter of the steel wire is D, from the surface of the steel wire toward the central axis (in the radial direction), X times the diameter D Indicates the location of depth. For example, “0.25 D” indicates a position at a depth of 0.25 times the diameter D.
(1)鋼線の中心軸を含み中心軸に平行な断面において、鋼線の内部のパーライト組織の面積率が90%以上であり、鋼線の表層部のパーライト組織の面積率が80%以上である。
(2)鋼線の全体における組織のうち、セメンタイトの平均長さが1.0μm以上であるラメラ状パーライト組織の面積率が30%以上65%以下であり、かつ、セメンタイトの平均長さが0.30μm以下である分断パーライト組織の面積率が20%以上50%以下である。 The high strength steel wire according to the present embodiment is a high strength steel wire having a predetermined component composition and having a metal structure satisfying the following (1) and (2) and having a tensile strength of 1960 MPa or more. .
(1) In a cross section including the central axis of the steel wire and parallel to the central axis, the area ratio of pearlite structure in the steel wire is 90% or more, and the area ratio of pearlite structure in the surface layer of the steel wire is 80% or more It is.
(2) The area ratio of the lamellar pearlite structure having an average length of cementite of 1.0 μm or more among the structures in the entire steel wire is 30% or more and 65% or less, and the average length of cementite is 0 The area ratio of the divided perlite structure which is 30 μm or less is 20% or more and 50% or less.
パーライト組織の線材を伸線加工すると、伸線後の鋼線の金属組織は、層間隔が微細なパーライト組織、層が不規則に曲がったパーライト組織、局部的に層がせん断変形したパーライト組織などが混在した不均一で複雑な組織となる。この状態の鋼線に、440~460℃の溶融亜鉛浴に30s程度浸漬する通常の溶融亜鉛めっき処理を行うと、微視的な機械的特性が不均一となる。このような不均一な鋼線は、捻じり変形を受けると局部的に変形し、捻回値が小さくなる。
一方、鋼線の微視的な機械的特性を均一にすると、捻じり変形の際の変形が均一になり、捻回値が向上する。 First, in order to improve the twisting characteristics of high strength steel wire with a tensile strength of 1960 MPa or more, the metallographic structure of the steel wire is pearlite, and the lamellar pearlite structure with a long cementite length and the cementite length It is effective to make a mixed structure of short and divided perlite tissue. The pearlite structure has a layered structure of cementite phase and ferrite phase.
When wire drawing of pearlite wire, the metallographic structure of the drawn steel wire is pearlite structure with fine layer spacing, pearlite structure with irregularly bent layers, pearlite structure with locally sheared layers, etc. Is a heterogeneous and complex organization. When ordinary hot-dip galvanizing treatment is performed by immersing the steel wire in this state in a hot-dip zinc bath at 440 to 460 ° C. for about 30 seconds, microscopic mechanical properties become uneven. Such non-uniform steel wires locally deform when subjected to torsional deformation, and the torsion value decreases.
On the other hand, when the microscopic mechanical properties of the steel wire are made uniform, the deformation at the time of torsional deformation becomes uniform, and the torsion value improves.
そして、本実施形態に係る高強度鋼線は、捻回特性に優れた引張強さ1960MPa以上の鋼線であり、例えば、ロープ用鋼線、橋梁ケーブル用鋼線、PC鋼線などに利用できる。そのため、本実施形態に係る高強度鋼線は、例えば、土木・建築物の軽量化や施工コストの低減に寄与し、産業上極めて有用である。 From the above, it has been found that the high-strength steel wire according to the present embodiment is a steel wire having high strength and excellent twisting characteristics.
The high-strength steel wire according to the present embodiment is a steel wire having a tensile strength of 1960 MPa or more and excellent in torsion characteristics, and can be used, for example, as a steel wire for ropes, steel wire for bridge cables, PC steel wire, etc. . Therefore, the high-strength steel wire according to the present embodiment contributes, for example, to weight reduction of civil engineering and buildings and reduction of construction costs, and is extremely useful in industry.
高強度鋼線の成分組成は、質量%で、C:0.85~1.20%、Si:0.10~2.00%、Mn:0.20~1.00%、P:0.030%以下、S :0.030%以下、N :0.0010~0.0080%、B:0~0.0050%、Al:0~0.100%、Ti:0~0.050%、Cr:0~0.60%、V:0~0.10%、Nb:0~0.050%、Zr:0~0.050%、および、Ni:0~1.00%を含有し、残部Fe及び不純物からなる。
ただし、B、Al、Ti、Cr、V、Nb、Zr、およびNiは、任意元素である。つまり、これら元素は、高強度鋼線に含有しなくてもよい。 (Component composition)
The composition of the high strength steel wire is, in mass%, C: 0.85 to 1.20%, Si: 0.10 to 2.00%, Mn: 0.20 to 1.00%, P: 0. 030% or less, S: 0.030% or less, N: 0.0010 to 0.0080%, B: 0 to 0.0050%, Al: 0 to 0.100%, Ti: 0 to 0.050%, Cr: 0 to 0.60%, V: 0 to 0.10%, Nb: 0 to 0.050%, Zr: 0 to 0.050%, and Ni: 0 to 1.00% It consists of the balance Fe and impurities.
However, B, Al, Ti, Cr, V, Nb, Zr, and Ni are optional elements. That is, these elements may not be contained in the high strength steel wire.
ここで、不純物とは、原材料に含まれる成分、または、製造の工程で混入する成分であって、意図的に含有させたものではない成分を指す。さらに、不純物は、意図的に含有させた成分であっても、鋼線の性能に影響を与えない範囲の量で含有する成分も含む。
不純物としては、例えば、O等が挙げられる。Oは鋼線中に不可避的に含有し、Al、Tiなどの酸化物として存在する。O量が高いと粗大な酸化物が形成し、伸線加工時に断線の原因となる。そのため、O量は0.010%以下に抑制することが好ましい。 In the component composition of the high strength steel wire according to the present embodiment, the balance is Fe and impurities.
Here, the term "impurity" refers to a component contained in the raw material or a component which is mixed in the process of production and is not intentionally contained. Furthermore, the impurities also include components that are intentionally contained, but in an amount that does not affect the performance of the steel wire.
As an impurity, O etc. are mentioned, for example. O is unavoidably contained in the steel wire and exists as an oxide such as Al or Ti. When the amount of O is high, coarse oxides are formed, which causes breakage during wire drawing. Therefore, it is preferable to suppress the amount of O to 0.010% or less.
次に、本実施形態に係る高強度鋼線の金属組織の限定理由について述べる。 (Metal structure)
Next, the reason for limitation of the metal structure of the high strength steel wire according to the present embodiment will be described.
なお、パーライト組織の面積率は、線の中心軸を含み中心軸に平行な断面における面積率である。 In the metallographic structure, the area ratio of pearlite structure in the steel wire is 90% or more, and the area ratio of pearlite structure in the surface layer of the steel wire is 80% or more.
The area ratio of the pearlite structure is an area ratio in a cross section including the central axis of the line and parallel to the central axis.
鋼線の表層部のパーライト組織の面積率を80%以上とする方法としては、例えば、Bを含有して、更にAl及びTiの少なくとも1種を含有した成分組成とする方法、または、熱間圧延後の線材の冷却速度を制御する方法がある。これらの方法のいずれか、または両方を実施することで、鋼線の表層部のパーライト組織の面積率を増加できる。 When the area ratio of the pearlite structure in the surface layer portion of the steel wire is less than 80%, the twisting characteristic or the wire drawability deteriorates. Therefore, the lower limit of the area ratio of pearlite structure in the surface layer portion is set to 80%. The lower limit of the area ratio of the preferred pearlite structure is 85%. The lower limit of the area ratio of the more preferable pearlite structure is 90%. The upper limit of the area ratio of the pearlite structure may be 95% or 99%. In addition, the area ratio of the perlite structure may be 100%.
As a method of setting the area ratio of the pearlite structure of the surface layer portion of the steel wire to 80% or more, for example, a method of containing B and further containing at least one of Al and Ti, or hot There is a method of controlling the cooling rate of the wire after rolling. By performing either or both of these methods, it is possible to increase the area ratio of pearlite structure in the surface layer of the steel wire.
そのため、ラメラ状パーライト組織の面積率は、30%以上65%以下とした。好ましいラメラ状パーライト組織の面積率の下限は40%であり、より好ましくは50%である。好ましいラメラ状パーライト組織の面積率の上限は60%である。 The "lamellar pearlite structure" as used herein refers to a pearlite structure in which cementite has a long length and an average length of 1.0 μm or more. Of the perlite that had been present before the aging treatment, the part having a relatively small influence by the aging treatment is a lamellar pearlite structure. If the area ratio of the lamellar pearlite structure is less than 30%, the strength is reduced (that is, it is difficult to obtain a strength of 1960 MPa or more), and if it exceeds 65%, the twisting property is degraded.
Therefore, the area ratio of the lamellar pearlite structure is 30% or more and 65% or less. The lower limit of the area ratio of the preferred lamellar perlite structure is 40%, more preferably 50%. The upper limit of the area ratio of the preferred lamellar pearlite structure is 60%.
そのため、分断パーライト組織の面積率は、20%以上50%以下とした。好ましい分断パーライト組織の面積率の下限は25%であり、より好ましい下限は30%である。一方、好ましい分断パーライト組織の面積率の上限は45%であり、より好ましくは40%である。
鋼線の分断パーライト組織の面積率を20%以上50%以下とする方法は、例えば、総減面率65~95%で伸線加工後の、表層部のパーライト組織の面積率が80%以上である鋼線を、500~600℃で1s以上20s以下保持する方法、または、420~480℃で60s以上600s以下保持する方法がある。
組織の測定方法は、以下とした。 On the other hand, the "divided perlite structure" as used herein refers to a pearlite structure having a short cementite length and an average length of 0.30 μm or less. Among the pearlite that had been present until the aging treatment, the strain formed by wire drawing and the structure formed as a result of the cementite in the pearlite being divided by the influence of the aging treatment is a divided pearlite structure. And, if the area ratio of the divided pearlite structure is less than 20%, the twisting characteristics deteriorate, and if it exceeds 50%, the strength decreases.
Therefore, the area ratio of the divided perlite structure is set to 20% or more and 50% or less. The lower limit of the area ratio of the preferable split pearlite structure is 25%, and the more preferable lower limit is 30%. On the other hand, the upper limit of the area ratio of a preferable divided pearlite structure is 45%, more preferably 40%.
The method of setting the area ratio of split pearlite structure of steel wire to 20% or more and 50% or less is, for example, 80% or more of area ratio of pearlite structure of surface layer portion after wire drawing at a total reduction ratio of 65 to 95%. There is a method of holding the steel wire which is at 500 to 600 ° C. for 1 s or more and 20 s or less, or a method for holding the steel wire at 420 to 480 ° C. for 60 s or more and 600 s or less.
The measurement method of the organization was as follows.
まず、鋼線の中心軸を含み、中心軸に平行な断面(以下、「L断面」とも称する)をピクラールでエッチングし、金属組織を現出させる。次に、SEM(走査型電子顕微鏡)により2000倍の倍率で、鋼線の径方向50μm×鋼線の長手方向60μmの領域の金属組織を写真撮影する。金属組織のSEM写真の撮影の箇所は、鋼線の直径をDとしたとき、鋼線の表面(つまり外周面)から鋼線の径方向に0.25Dの深さの位置、および鋼線の表面から鋼線の径方向に0.5Dの深さの位置において、各々、鋼線の長手方向に5mm間隔で3箇所、計6箇所とする(図1参照)。なお、図1中、OA1は、鋼線の内部における金属組織のSEM写真の撮影の領域を示す。
撮影した金属組織のSEM写真中の非パーライト組織(フェライト、ベイナイト、焼き戻しベイナイト、マルテンサイト、焼き戻しマルテンサイト、初析セメンタイトの各組織)を目視でマーキングし、面積率を画像解析により求める。パーライト組織の面積率は、観察視野全体から非パーライト組織の面積を減じることにより求められる。そして、これを2個のサンプルについて測定し、測定した計12箇所の平均値を鋼線の内部のパーライト組織の面積率とする。 Here, the area ratio of the pearlite structure inside the steel wire is determined by the following procedure.
First, a cross section including the central axis of the steel wire and parallel to the central axis (hereinafter also referred to as “L cross section”) is etched with picral to reveal a metal structure. Next, a metallographic structure in a region of 50 μm in the radial direction of the steel wire × 60 μm in the longitudinal direction of the steel wire is photographed at a magnification of 2000 times by a SEM (scanning electron microscope). Where the diameter of the steel wire is D, the location of the SEM photograph of the metallographic structure is a position of a depth of 0.25 D in the radial direction of the steel wire from the surface (that is, the outer peripheral surface) of the steel wire and At a depth of 0.5 D from the surface in the radial direction of the steel wire, three points are provided at intervals of 5 mm in the longitudinal direction of the steel wire, for a total of six places (see FIG. 1). In addition, OA1 shows the area | region of photography of the SEM photograph of the metallographic structure in the inside of a steel wire in FIG.
Non-perlite structures (structures of ferrite, bainite, tempered bainite, martensite, tempered martensite, and proeutectoid cementite) in the SEM photograph of the metallographic structure taken are visually marked, and the area ratio is determined by image analysis. The percent area of pearlite tissue is determined by subtracting the area of non-perlite tissue from the entire field of view. And this is measured about two samples, and let the average value of a total of 12 measured be the area ratio of the pearlite structure | tissue inside a steel wire.
まず、上記同様に、鋼線のL断面をピクラールでエッチングし、金属組織を現出させる。鋼線の表面を含み、表面から深さ方向(鋼線の径方向)に50μm、鋼線の長手方向に60μmの領域の金属組織を、SEMにより2000倍の倍率で写真撮影する。金属組織のSEM写真の撮影の箇所は、鋼線の長手方向に5mm間隔で6箇所とする(図1参照)。なお、図1中、OA2は、鋼線の表層部における金属組織のSEM写真の撮影の領域を示す。
撮影した金属組織のSEM写真中の非パーライト組織(フェライト、ベイナイト、焼き戻しベイナイト、マルテンサイト、焼き戻しマルテンサイト、初析セメンタイトの各組織)を目視でマーキングし、面積率を画像解析により求める。パーライト組織の面積率は、観察視野全体から非パーライト組織の面積を減じることにより求められる。そして、これを2個のサンプルについて測定し、測定した計12箇所の平均値を鋼線の表層部のパーライト組織の面積率とした。 Next, the pearlite structure of the surface layer portion of the steel wire is determined according to the following procedure.
First, in the same manner as described above, the L cross section of the steel wire is etched with picral to reveal a metallographic structure. The metallographic structure in the region of 50 μm from the surface in the depth direction (radial direction of the steel wire) and 60 μm in the longitudinal direction of the steel wire, including the surface of the steel wire, is photographed by SEM at 2000 × magnification. The places where the SEM photograph of the metal structure is taken are six places at intervals of 5 mm in the longitudinal direction of the steel wire (see FIG. 1). In addition, OA2 shows the area | region of photography of the SEM photograph of the metallographic structure in the surface layer part of a steel wire in FIG.
Non-perlite structures (structures of ferrite, bainite, tempered bainite, martensite, tempered martensite, and proeutectoid cementite) in the SEM photograph of the metallographic structure taken are visually marked, and the area ratio is determined by image analysis. The percent area of pearlite tissue is determined by subtracting the area of non-perlite tissue from the entire field of view. And this was measured about two samples, and the average value of a total of 12 measured was made into the area ratio of the pearlite structure of the surface layer part of a steel wire.
まず、上記同様に、鋼線のL断面をピクラールでエッチングし、金属組織を現出させる。次に、SEMにより10000倍の倍率で、鋼線の径方向8μm×鋼線の長手方向12μmの領域の金属組織を写真撮影する。金属組織のSEM写真の撮影の箇所は、鋼線の直径をDとしたとき、鋼線の表面から鋼線の径方向に50μmの深さの位置、鋼線の表面から鋼線の径方向に0.25Dの深さの位置、および鋼線の表面から鋼線の径方向に0.5Dの深さの位置において、各々、鋼線の長手方向に平行な方向に5mm間隔で3箇所、計9箇所とする(図2参照)。なお、図2中、OAは、SEM写真の撮影の領域を示す。
撮影した金属組織のSEM写真画像上に、鋼線の長手方向に平行な2μm間隔の直線群を描く。さらに、これらの直線群と直角に交差する2μm間隔の直線群を描く。次に、2つの直線群のそれぞれの交点における組織を以下の方法で観察する。パーライト組織が存在する各交点に近接するセメンタイト3個において、セメンタイトの長軸の長さを画像解析により測定し、それらの平均値をセメンタイトの長軸の長さの平均値(つまり、平均長さ)とする。なお、セメンタイトが小さく、10000倍のSEM写真で判別できない場合には、SEM写真の倍率を拡大してもよい。交点に近接する3個のセメンタイトの長軸の長さの平均値が1.0μm以上である交点の数を求め、パーライト組織が存在しない交点も含めた全交点の数(つまり、描いた2つの直線群の全ての交点の数)で除した値の百分率、すなわち、(セメンタイトの長軸の長さの平均値が1.0μm以上である交点の数)/(全交点の数)×100を、ラメラ状パーライト組織の面積率とする。 Next, the area ratio of the lamellar pearlite structure and the area ratio of the divided perlite structure are determined according to the following procedure.
First, in the same manner as described above, the L cross section of the steel wire is etched with picral to reveal a metallographic structure. Next, a metallographic structure in a region of 8 μm in the radial direction of the steel wire × 12 μm in the longitudinal direction of the steel wire is photographed at a magnification of 10000 by SEM. When the diameter of the steel wire is D, the location of the SEM photograph of the metallographic structure is 50 μm deep from the surface of the steel wire to the radial direction of the steel wire, and from the surface of the steel wire to the radial direction of the steel wire Three points at a distance of 5 mm in the direction parallel to the longitudinal direction of the steel wire, at a position of depth of 0.25 D and at a position of depth of 0.5 D in the radial direction of the steel wire from the surface of the steel wire There are nine places (see Figure 2). Note that, in FIG. 2, OA indicates an area for taking a SEM photograph.
On the SEM photograph image of the metallographic structure taken, a straight line group of 2 μm intervals parallel to the longitudinal direction of the steel wire is drawn. Furthermore, draw straight lines at intervals of 2 μm crossing these straight lines at right angles. Next, the tissue at each intersection of the two straight line groups is observed by the following method. The length of the cementite long axis is measured by image analysis in three cementite close to each intersection where the pearlite structure exists, and their average value is an average value of the cementite long axis (that is, the average length And). In addition, when cementite is small and it can not discriminate | determine by a 10000 times SEM photograph, you may expand the magnification of a SEM photograph. Determine the number of intersections where the average length of the major axes of three cementite in the vicinity of the intersection is 1.0 μm or more, and the number of all intersections including the intersection where there is no pearlite structure (that is, the two drawn The percentage of the value divided by the number of all intersections of the straight line group, that is, (the number of intersections in which the average length of the major axis of cementite is 1.0 μm or more) / (the number of all intersections) × 100 , And the area ratio of lamellar pearlite tissue.
次に、本実施形態に係る高強度鋼線の引張強さについて説明する。
鋼線の引張強さが1960MPa未満では、例えば、鋼線を土木・建築構造物の用途に適用した場合、施工コストの低減及び軽量化の効果が小さくなる。そのため、鋼線の引張強さの下限は1960MPaとした。
鋼線の引張強さの上限は、特に限定されるものではないが、引張強さが高すぎると、延性が低下し、伸線加工を施すときに割れが生じる場合がある。この点で、鋼線の引張強さの上限は、引張強さは3000MPa(好ましくは2800MPa、より好ましくは2500MPa)がよい。 (Characteristics of high strength steel wire)
Next, the tensile strength of the high strength steel wire according to the present embodiment will be described.
If the tensile strength of the steel wire is less than 1960 MPa, for example, when the steel wire is applied to a civil engineering / building structure application, the effects of reduction in construction cost and weight reduction become small. Therefore, the lower limit of the tensile strength of the steel wire is set to 1960 MPa.
The upper limit of the tensile strength of the steel wire is not particularly limited, but if the tensile strength is too high, the ductility may be reduced and cracking may occur when wire drawing is performed. In this respect, the upper limit of the tensile strength of the steel wire is preferably 3000 MPa (preferably 2800 MPa, more preferably 2500 MPa).
本実施形態に係る高強度鋼線は、ロープ用鋼線、橋梁ケーブル用鋼線、PC鋼線などに使用される高強度鋼線を対象とすることがよい。そのため、鋼線の線径(直径)が、1.5mm未満では、これらの商品を製造する際のコストが上昇し、8.0mmを超えると強度や捻回特性が劣化しやすくなる。そのため、鋼線の線径(直径)は、1.5mm~8.0mmがよい。より好ましい鋼線の線径(直径)の範囲は、3.0mm~7.5mmである。 Next, the wire diameter of the high strength steel wire according to the present embodiment will be described.
The high-strength steel wire according to the present embodiment may be a high-strength steel wire used for a rope steel wire, a bridge cable steel wire, a PC steel wire, and the like. Therefore, if the wire diameter (diameter) of the steel wire is less than 1.5 mm, the cost at the time of manufacturing these products increases, and if it exceeds 8.0 mm, the strength and twisting characteristics are easily deteriorated. Therefore, the wire diameter (diameter) of the steel wire is preferably 1.5 mm to 8.0 mm. A more preferable range of the wire diameter (diameter) of the steel wire is 3.0 mm to 7.5 mm.
ロープ用鋼線、橋梁ケーブル用鋼線などに使用される高強度鋼線には、表面にめっきが施された鋼線が使用されることがある。そして、表面にめっきが施されていても、本実施形態に係る高強度鋼線は、高強度でかつ捻回特性に優れた鋼線となる。
なお、本実施形態に係る高強度鋼線は、鋼線の表面またはめっきが施された鋼線の表面に、樹脂被覆層(例えばエポキシ樹脂層)が被覆されていてもよい。 Here, in the high-strength steel wire according to the present embodiment, a plating layer having any one of a Zn layer and a Zn alloy layer may be coated on the surface of the steel wire. Examples of the Zn alloy layer include a ZnAl layer, a ZnAlMg alloy layer, and the like.
The high strength steel wire used for the steel wire for ropes, the steel wire for bridge cables, etc. may use the steel wire by which the surface was plated. And, even if the surface is plated, the high strength steel wire according to this embodiment is a steel wire which is high in strength and excellent in twisting characteristics.
In the high-strength steel wire according to the present embodiment, the surface of the steel wire or the surface of the plated steel wire may be coated with a resin coating layer (for example, an epoxy resin layer).
本実施形態に係る高強度鋼線の製造方法の一例について説明する。
本実施形態に係る高強度鋼線の製造方法は、上記本実施形態に係る高強度鋼線の成分組成を有する鋼片を、1000~1150℃に加熱し、仕上げ圧延温度850~1000℃で熱間圧延することにより、線材を得る工程を有する。 (Method of manufacturing high strength steel wire)
An example of the manufacturing method of the high strength steel wire concerning this embodiment is explained.
In the method of manufacturing a high strength steel wire according to the present embodiment, a steel piece having the component composition of the high strength steel wire according to the present embodiment is heated to 1000 to 1150 ° C., and thermal rolling is performed at a finish rolling temperature of 850 to 1000 ° C. It has a process of obtaining a wire rod by rolling.
熱間圧延後、850~1000℃である線材を、800℃から600℃までの平均冷却速度30~80℃/sで、500~600℃まで冷却する工程と、
500~600℃まで冷却後の線材を、500~600℃で50s以上保持することによりパーライト変態処理する工程と、
パーライト変態処理後、室温に冷却した線材を、総減面率65~95%で伸線加工し、500~600℃で1s以上20s以下保持し、鋼線を得る工程と、
を有する高強度鋼線の製造方法。 -Aspect (1)-
Cooling the wire, which is at 850 to 1000 ° C., to 500 to 600 ° C. at an average cooling rate of 30 to 80 ° C./s from 800 ° C. to 600 ° C. after hot rolling;
A pearlite transformation process by holding the wire after cooling to 500 to 600 ° C. for 50 s or more at 500 to 600 ° C .;
After the pearlite transformation treatment, the wire cooled to room temperature is drawn at a total reduction of area of 65 to 95%, held at 500 to 600 ° C. for 1 second to 20 seconds, and obtaining a steel wire;
A method of manufacturing a high strength steel wire having the
熱間圧延後、850~1000℃である線材を、800℃から600℃までの平均冷却速度を30~80℃/sで、500~600℃まで冷却する工程と、
500~600℃まで冷却後の線材を、500~600℃で50秒以上保持することによりパーライト変態処理する工程と、
パーライト変態処理後、室温に冷却した線材を、総減面率65~95%で伸線加工し、420~480℃で60s以上600s以下保持し、鋼線を得る工程と、
を有する高強度鋼線の製造方法。 -Aspect (2)-
Cooling the wire, which is at 850 to 1000 ° C., to 500 to 600 ° C. at an average cooling rate of 800 to 600 ° C. at 30 to 80 ° C./s after hot rolling;
A pearlite transformation process by holding the wire after cooling to 500 to 600 ° C. for 50 seconds or more at 500 to 600 ° C .;
After the pearlite transformation treatment, the wire cooled to room temperature is drawn with a total reduction of area of 65 to 95%, held at 420 to 480 ° C. for 60 s or more and 600 s or less, to obtain a steel wire;
A method of manufacturing a high strength steel wire having the
熱間圧延後、850~1000℃である線材を、700℃から550℃までの平均冷却速度を1.0~5.0℃/sで冷却する工程と、
室温に冷却後の線材を、総減面率65~95%で伸線加工し、500~600℃で1s以上20s以下保持し、鋼線を得る工程と、
を有する高強度鋼線の製造方法。 -Aspect (3)-
Cooling the wire, which is at 850 to 1000 ° C., at an average cooling rate from 700 ° C. to 550 ° C. at 1.0 to 5.0 ° C./s after hot rolling;
Wire drawing after cooling to room temperature with a total reduction in area of 65 to 95% and holding at 500 to 600 ° C. for 1 s or more and 20 s or less to obtain a steel wire;
A method of manufacturing a high strength steel wire having the
熱間圧延後、850~1000℃である線材を、700℃から550℃までの平均冷却速度を1.0~5.0℃/sで冷却する工程と、
室温に冷却後の線材を、総減面率65~95%で伸線加工し、420~480℃で60s以上600s以下保持し、鋼線を得る工程と、
を有する高強度鋼線の製造方法。 -Aspect (4)-
Cooling the wire, which is at 850 to 1000 ° C., at an average cooling rate from 700 ° C. to 550 ° C. at 1.0 to 5.0 ° C./s after hot rolling;
Wire drawing after cooling to room temperature with a total reduction in area of 65 to 95% and holding at 420 to 480 ° C. for 60 seconds or more and 600 seconds or less to obtain a steel wire;
A method of manufacturing a high strength steel wire having the
熱間圧延後、冷却した線材を、800~1050℃に再加熱し、480~600℃で20s以上保持後、冷却する工程と、
室温に冷却後の線材を、総減面率65~95%で伸線加工し、500~600℃で1s以上20s以下保持し、鋼線を得る工程と、
を有する高強度鋼線の製造方法。 -Aspect (5)-
Re-heating the cooled wire rod to 800 to 1050 ° C. after hot rolling and holding it at 480 to 600 ° C. for 20 seconds or more, and then cooling it;
Wire drawing after cooling to room temperature with a total reduction in area of 65 to 95% and holding at 500 to 600 ° C. for 1 s or more and 20 s or less to obtain a steel wire;
A method of manufacturing a high strength steel wire having the
熱間圧延後、冷却した線材を、800~1050℃に再加熱し、480~600℃で20s以上保持後、冷却する工程と、
室温に冷却後の線材を、総減面率65~95%で伸線加工し、420~480℃で60s以上600s以下保持し、鋼線を得る工程と、
を有する高強度鋼線の製造方法。 -Aspect (6)-
Re-heating the cooled wire rod to 800 to 1050 ° C. after hot rolling and holding it at 480 to 600 ° C. for 20 seconds or more, and then cooling it;
Wire drawing after cooling to room temperature with a total reduction in area of 65 to 95% and holding at 420 to 480 ° C. for 60 seconds or more and 600 seconds or less to obtain a steel wire;
A method of manufacturing a high strength steel wire having the
加熱温度が1000℃未満では、熱間圧延の際の変形抵抗が増大し圧延コストが嵩む。加熱温度が1150℃を超えると表層部の非パーライト組織の面積率が増大し、伸線加工性および捻回特性が劣化する。好ましい加熱温度の範囲の下限は、1050℃である。好ましい加熱温度の範囲の上限は、1100℃である。 In the method for manufacturing a high strength steel wire according to the present embodiment, first, a steel piece having the component composition of the high strength steel wire according to the present embodiment is heated to 1000 to 1150 ° C.
When the heating temperature is less than 1000 ° C., deformation resistance in hot rolling increases and rolling cost increases. When the heating temperature exceeds 1150 ° C., the area ratio of the non-pearlite structure in the surface layer increases, and the wire drawability and twisting characteristics deteriorate. The lower limit of the preferred heating temperature range is 1050.degree. The upper limit of the preferred heating temperature range is 1100 ° C.
仕上げ圧延温度が850℃未満では、熱間圧延の際の変形抵抗が増大し圧延コストが嵩む。仕上げ圧延温度が1000℃を超えると、金属組織が粗大になり、伸線加工性が劣化する。好ましい仕上げ圧延温度の範囲の下限は、870℃である。好ましい仕上げ圧延温度の範囲の上限は、980℃である。
なお、仕上げ圧延温度とは、仕上げ圧延直後の線材の表面温度を指す。 Next, the heated billet is hot-rolled at a finish rolling temperature of 850 to 1000 ° C. to obtain a wire rod.
When the finish rolling temperature is less than 850 ° C., deformation resistance in hot rolling increases and rolling cost increases. When the finish rolling temperature exceeds 1000 ° C., the metal structure becomes coarse and wire drawability deteriorates. The lower limit of the preferred finish rolling temperature range is 870 ° C. The upper limit of the preferred finish rolling temperature range is 980 ° C.
The finish rolling temperature refers to the surface temperature of the wire immediately after finish rolling.
平均冷却速度が30℃/s未満では、表層部の非パーライト組織の面積率が増大し、伸線加工性と捻回特性が劣化する。平均冷却速度が80℃/s以上とするには製造コストが嵩む。好ましい平均冷却速度の範囲の下限は、40℃/sである。好ましい平均冷却速度の範囲の上限は、75℃/sである。なお、平均冷却速度とは、線材の表面冷却速度を指す。
冷却温度が500℃未満では、パーライト面積率が小さくなり、捻回特性が劣化する。冷却温度が600℃を超えると、強度が低下する。好ましい冷却温度の範囲の下限は、530℃である。好ましい冷却温度の範囲の上限は、580℃である。 Next, after hot rolling (specifically, after finish rolling), the wire rod at 850 to 1000 ° C. is cooled to 500 to 600 ° C. at an average cooling rate of 30 to 80 ° C./s from 800 ° C. to 600 ° C. Do.
When the average cooling rate is less than 30 ° C./s, the area ratio of the non-pearlite structure in the surface layer increases, and the wire drawability and the twisting property deteriorate. In order to make the average cooling rate 80 ° C./s or more, the manufacturing cost increases. The lower limit of the preferred average cooling rate range is 40 ° C./s. The upper limit of the preferable average cooling rate range is 75 ° C./s. In addition, an average cooling rate refers to the surface cooling rate of a wire.
When the cooling temperature is less than 500 ° C., the pearlite area ratio becomes small, and the twisting characteristics deteriorate. When the cooling temperature exceeds 600 ° C., the strength decreases. The lower limit of the preferred cooling temperature range is 530.degree. The upper limit of the preferred cooling temperature range is 580 ° C.
保持温度が500℃未満では、パーライト面積率が小さくなり、捻回特性が劣化する。保持温度が600℃を超えると強度が低下する。好ましい保持温度の範囲の下限は、530℃である。好ましい保持温度の範囲の上限は、580℃である。
保持時間が50s未満では、パーライト変態が未完となり、マルテンサイトが生成し、伸線加工性と捻回特性が劣化する。ただし、製造コストの観点から、保持時間の上限は、150sがよい。好ましい保持時間の範囲の下限は、60sである。好ましい保持時間の範囲の上限は、120sである。500~600℃の保持は、例えば、溶融塩浴槽により実施する。 Next, the wire after cooling to 500 to 600 ° C. is subjected to pearlite transformation treatment by holding the wire at 500 to 600 ° C. for 50 seconds or more.
When the holding temperature is less than 500 ° C., the pearlite area ratio becomes small, and the twisting characteristics deteriorate. When the holding temperature exceeds 600 ° C., the strength decreases. The lower limit of the preferred holding temperature range is 530 ° C. The upper limit of the preferred holding temperature range is 580 ° C.
If the holding time is less than 50 s, pearlite transformation is incomplete, martensite is formed, and wire drawability and twisting characteristics deteriorate. However, from the viewpoint of manufacturing cost, the upper limit of the holding time is preferably 150 s. The lower limit of the preferred holding time range is 60 s. The upper limit of the preferred holding time range is 120 s. The holding at 500 to 600 ° C. is performed, for example, by a molten salt bath.
平均冷却速度が1.0℃/s未満では強度が低下する。平均冷却速度が5.0℃/sを超えると、微視的な強度および金属組織のばらつきが大きくなり捻回特性が劣化する。好ましい平均冷却速度の範囲の下限は、1.2℃/sである。好ましい平均冷却速度の範囲の上限は、3.0℃/sである。 Here, in place of the above cooling and pearlite transformation treatment, after hot rolling, the wire rod at 850 to 1000 ° C. is cooled at an average cooling rate of 700 to 550 ° C. at 1.0 to 5.0 ° C./s You may The cooling is performed by, for example, a blast cooling facility such as Stelmore.
If the average cooling rate is less than 1.0 ° C./s, the strength decreases. When the average cooling rate exceeds 5.0 ° C./s, microscopic variations in strength and metallographic structure become large, and the torsion characteristics deteriorate. The lower limit of the preferred average cooling rate range is 1.2 ° C./s. The upper limit of the preferred average cooling rate range is 3.0 ° C./s.
再加熱温度が800℃未満では、オーステナイト化が不十分で均一なパーライト組織が得られず、強度が低下するとともに、伸線加工性が劣化する。再加熱温度が1050℃を超えると表層部の非パーライト組織の面積率が増大し、伸線加工性と捻回特性が劣化する。好ましい再加熱温度の範囲の下限は、940℃である。好ましい再加熱温度の範囲の上限は、1020℃である。
保持温度が480℃未満では、パーライト組織の面積率が低下し、捻回特性が劣化する。保持温度が600℃を超えるとパーライト組織のラメラ間隔が大きくなり強度が低下する。好ましい保持温度の範囲の下限は、520℃である。好ましい保持温度の範囲の上限は、590℃である。
保持時間が20s未満では、パーライト変態が未完となり、マルテンサイトが生成し、伸線加工性と捻回特性が劣化する。ただし、製造コストの観点から、保持時間の上限は、120sがよい。好ましい保持時間の範囲の下限は、30sである。好ましい保持時間の範囲の上限は、80sである。
再加熱処理を酸化性雰囲気で行うと、鋼線の表層部のパーライト組織の面積率が低下し、伸線加工性と捻回特性が劣化する場合がある。そのため、再加熱熱処理の雰囲気は、例えば、不活性ガス(Arガス等)、中性ガス(窒素ガス等)、又は吸熱型変性ガスとする。また、再加熱処理は、誘導加熱などの短時間加熱でもよい。
なお、480~600℃の保持は、例えば、溶融鉛浴で実施する。溶融鉛浴に代えて、溶融塩浴、流動層等を用いてもよい。 Also, instead of the above cooling treatment and pearlite transformation treatment, after hot rolling, the wire rod cooled to room temperature (for example 25 ° C.) is reheated to 800 to 1050 ° C. and held for 20 s or more at 480 to 600 ° C. cooling You may
When the reheating temperature is less than 800 ° C., the austenitizing is insufficient and a uniform pearlite structure can not be obtained, and the strength is lowered and the wire drawability is deteriorated. When the reheating temperature exceeds 1050 ° C., the area ratio of the non-pearlite structure in the surface layer increases, and the wire drawability and the twisting property deteriorate. The lower limit of the preferred reheating temperature range is 940 ° C. The upper limit of the preferred reheating temperature range is 1020 ° C.
When the holding temperature is less than 480 ° C., the area ratio of pearlite structure decreases and the twisting characteristics deteriorate. When the holding temperature exceeds 600 ° C., the lamellar spacing of the perlite structure increases and the strength decreases. The lower limit of the preferred holding temperature range is 520 ° C. The upper limit of the preferred holding temperature range is 590.degree.
If the holding time is less than 20 s, pearlite transformation becomes incomplete, martensite is formed, and wire drawability and twisting characteristics deteriorate. However, from the viewpoint of manufacturing cost, the upper limit of the holding time is preferably 120 s. The lower limit of the preferred retention time range is 30 s. The upper limit of the preferred retention time range is 80 s.
When the reheating treatment is performed in an oxidizing atmosphere, the area ratio of pearlite structure in the surface layer portion of the steel wire may be reduced, and the wire drawability and the twisting property may be deteriorated. Therefore, the atmosphere for the reheat heat treatment is, for example, an inert gas (such as Ar gas), a neutral gas (such as nitrogen gas), or an endothermic modified gas. Further, the reheating treatment may be heating for a short time such as induction heating.
The holding at 480 to 600 ° C. is performed, for example, in a molten lead bath. Instead of the molten lead bath, a molten salt bath, a fluidized bed or the like may be used.
総減面率が65%未満では強度が低下する。総減面率が95%を超えると、鋼線の延性が低下し、伸線加工性や捻回特性が劣化する。好ましい総減面率の範囲は、70~90%である。なお、総減面率とは、式:(伸線加工前の線材の断面積(線材の長手方向に垂直な面の面積)と伸線加工後の鋼線の断面積との差分/伸線加工前の線材の断面積)×100で算出される値である。
保持温度が500℃未満では、捻回特性の向上効果がない。保持温度が600℃を超えると強度が低下する。好ましい保持温度の範囲は、510~550℃である。
保持時間が1s未満では、捻回特性の向上効果がない。保持時間が20sを超えると強度が低下する。好ましい保持温度の範囲は、2~15sである。 Then, the wire rod after the above pearlite transformation treatment or after cooling (specifically, the wire rod after cooling to room temperature (for example, 25 ° C.) is drawn at a total reduction of 65 to 95%, and 500 to 600 ° C. Hold for 1 s or more and 20 s or less to obtain a steel wire. By holding at 500 to 600 ° C. for 1 s or more and 20 s or less, the twisting characteristic is improved. The heat treatment after wire drawing is also referred to as "aging treatment".
If the total reduction rate is less than 65%, the strength decreases. If the total area reduction rate exceeds 95%, the ductility of the steel wire is reduced, and the wire drawability and twisting characteristics are degraded. The preferred total reduction rate is 70 to 90%. The total area reduction rate is the difference between the cross-sectional area of the wire before drawing (the area of the surface perpendicular to the longitudinal direction of the wire) and the cross-sectional area of the steel wire after drawing / wire drawing It is a value calculated by cross section area of wire before processing × 100.
When the holding temperature is less than 500 ° C., there is no effect of improving the twisting characteristics. When the holding temperature exceeds 600 ° C., the strength decreases. The preferred holding temperature range is 510-550.degree.
If the holding time is less than 1 s, there is no effect of improving the twisting characteristics. If the holding time exceeds 20 s, the strength decreases. The preferred holding temperature range is 2 to 15 s.
保持温度が420℃未満では捻回特性が低下する。保持温度が480℃を超えると強度が低下する。好ましい保持温度の範囲は、430~470℃である。
保持時間が60s未満では捻回特性が低下する。保持時間600sを超えると製造コストが嵩む。好ましい保持温度の範囲は、100~500sである。 Here, after wire drawing, instead of holding at 500 to 600 ° C. for 1 s or more and 20 s or less, it may be held at 420 to 480 ° C. for 60 s or more and 600 s or less.
If the holding temperature is less than 420 ° C., the twisting characteristic is degraded. When the holding temperature exceeds 480 ° C., the strength decreases. The preferred holding temperature range is 430-470.degree.
If the holding time is less than 60 s, the twisting characteristics deteriorate. If the holding time exceeds 600 s, the manufacturing cost increases. The preferred holding temperature range is 100 to 500 s.
鋼線の表面に、Zn層、およびZn合金層のいずれか1層を有するめっき層を被覆するめっき処理を、420~480℃で60s以上600s以下の条件、もしくは500~600℃で1s以上20s以下の条件で行う工程を有してもよい。この場合も、めっき処理に伴う鋼線の温度変化によって、鋼線に同様の組織が形成される。
つまり、鋼線の表面に、上記時効処理に対応する温度および時間の条件でめっき処理を施すことにより、本実施形態に係る鋼線の組織状態を備え、かつZn層、およびZn合金層のいずれか1層を有するめっき層が被覆されている高強度鋼線が得られる。 In addition, the manufacturing method of the high strength steel wire which concerns on this embodiment is replaced with said aging treatment,
Plating treatment for coating a plating layer having a Zn layer and any one layer of Zn alloy layer on the surface of a steel wire is performed under the conditions of 60s to 600s at 420 to 480 ° C, or 1s to 20s at 500 to 600 ° C. You may have the process performed on condition of the following. Also in this case, a similar structure is formed on the steel wire due to the temperature change of the steel wire accompanying the plating process.
That is, the surface of the steel wire is plated under the conditions of temperature and time corresponding to the above-mentioned aging treatment to provide the structural state of the steel wire according to the present embodiment, and any of the Zn layer and the Zn alloy layer A high strength steel wire coated with a plating layer having one layer is obtained.
まず、鋼片を加熱した後、熱間圧延して、得られた線材をリング状に巻取り、500~600℃まで冷却した。次に、得られた線材を熱間圧延ライン後方の溶融塩浴に浸漬してパテンティング処理(パーライト変態処理)した。その後、室温(25℃)まで冷却した線材を表2に示す線径(伸線後の線径と表記)まで伸線加工し、伸線後に加熱して時効処理した。これらの工程を経て、試験番号1~30に示す鋼線を製造した。 Specifically, steel wires of test numbers 1 to 30 shown in Table 2 were manufactured as follows.
First, after heating a steel piece, it was hot-rolled, and the obtained wire was wound into a ring and cooled to 500 to 600.degree. Next, the obtained wire was immersed in a molten salt bath at the rear of a hot rolling line to perform patenting (perlite transformation). Thereafter, the wire rod cooled to room temperature (25 ° C.) was drawn to the wire diameter shown in Table 2 (denoted as the wire diameter after wire drawing), and after heating, it was heated and aged. Through these steps, steel wires shown in Test Nos. 1 to 30 were produced.
まず、鋼片を加熱した後、熱間圧延して、得られた線材をリング状に巻き取り、衝風冷却した。その後、室温(25℃)まで冷却した線材を表3に示す線径まで伸線加工し、伸線後に加熱して時効処理した。これらの工程を経て、試験番号31~34に示す鋼線を製造した。 The steel wires of test numbers 31 to 34 shown in Table 3 were manufactured as follows.
First, after heating a steel piece, it hot-rolled, wound the obtained wire rod like ring shape, and carried out blast cooling. Thereafter, the wire rod cooled to room temperature (25 ° C.) was drawn to the wire diameter shown in Table 3, and after the drawing, it was heated and aged. Through these steps, steel wires shown in Test Nos. 31 to 34 were manufactured.
鋼片を加熱した後、熱間圧延して、得られた線材をリング状に巻取り、平均冷却速度2.0℃/sで冷却した。次に、室温(25℃)まで冷却した線材を、所定の雰囲気下で再加熱し、溶融鉛浴に浸漬した。その後、室温(25℃)まで冷却した線材を表4に示す線径まで伸線加工し、伸線後に加熱して時効処理した。これらの工程を経て、試験番号35~40に示す鋼線を製造した。 In addition, steel wires of test numbers 35 to 40 shown in Table 4 were manufactured as follows.
After heating the billet, it was hot-rolled, and the obtained wire was wound into a ring, and cooled at an average cooling rate of 2.0 ° C./s. Next, the wire rod cooled to room temperature (25 ° C.) was reheated in a predetermined atmosphere and immersed in a molten lead bath. Thereafter, the wire rod cooled to room temperature (25 ° C.) was subjected to wire drawing to the wire diameter shown in Table 4, and after the wire drawing was heated for aging treatment. Through these steps, steel wires shown in Test Nos. 35 to 40 were manufactured.
まず、鋼片を加熱した後、熱間圧延して、得られた線材をリング状に巻取り、500~600℃まで冷却した。次に、得られた線材を熱間圧延ライン後方の溶融塩浴に浸漬してパテンティング処理した。その後、室温(25℃)まで冷却した線材を表5に示す線径まで伸線加工し、伸線後に加熱して時効処理した。その後、溶融亜鉛めっき処理した。これらの工程を経て、試験番号41に示す鋼線を製造した。 Moreover, the steel wire of the test number 41 shown in Table 5 was manufactured as follows.
First, after heating a steel piece, it was hot-rolled, and the obtained wire was wound into a ring and cooled to 500 to 600.degree. Next, the obtained wire rod was dipped in a molten salt bath after the hot rolling line for patenting treatment. Thereafter, the wire rod cooled to room temperature (25 ° C.) was subjected to wire drawing to the wire diameter shown in Table 5, and after the wire drawing was heated for aging treatment. Thereafter, it was subjected to hot dip galvanization treatment. Through these steps, a steel wire shown in Test No. 41 was manufactured.
試験番号13、17、27、39、42の鋼線は、分断パーライト組織の面積率が本開示の範囲を外れる。
試験番号18と40の鋼線は、表層部のパーライト組織の面積率が本開示の下限を下回る。なお、試験番号40の鋼線は、特許文献5の鋼線に相当する例である。 On the other hand, in the steel wire of test No. 12, the area ratio of pearlite structure is less than the lower limit of the present disclosure.
In the steel wires of test numbers 13, 17, 27, 39, 42, the area ratio of the divided perlite structure is out of the range of the present disclosure.
In the steel wires of test numbers 18 and 40, the area ratio of pearlite structure in the surface layer portion is lower than the lower limit of the present disclosure. In addition, the steel wire of test number 40 is an example corresponded to the steel wire of patent document 5. FIG.
試験番号14、16、26、29の鋼線は、ラメラ状パーライト組織の面積率と分断パーライト組織の面積率が本開示の範囲を外れる。 In the steel wires of test numbers 28 and 33, the area ratio of the lamellar pearlite structure exceeds the upper limit of the present disclosure.
In the steel wires of test numbers 14, 16, 26, and 29, the area ratio of the lamellar pearlite structure and the area ratio of the divided perlite structure are out of the scope of the present disclosure.
試験番号19、20は、C量が本開示の範囲を外れる。 The steel wires of test numbers 15 and 34 are any of the area ratio of pearlite structure inside the steel wire, the area ratio of pearlite structure of the surface layer of the steel wire, the area ratio of lamellar pearlite structure, and the area ratio of divided pearlite structure The thigh is out of the scope of the present disclosure.
The test numbers 19, 20 have a C amount outside the scope of the present disclosure.
本明細書に記載された全ての文献、特許出願、および技術規格は、個々の文献、特許出願、および技術規格が参照により取り込まれることが具体的かつ個々に記された場合と同程度に、本明細書中に参照により取り込まれる。 The disclosure of Japanese Patent Application No. 2017-128871 is incorporated herein by reference in its entirety.
All documents, patent applications, and technical standards described herein are as specific and individually as individual documents, patent applications, and technical standards are incorporated by reference. Incorporated herein by reference.
Claims (5)
- 成分組成が、質量%で、
C :0.85~1.20%、
Si:0.10~2.00%、
Mn:0.20~1.00%、
P :0.030%以下、
S :0.030%以下、
N :0.0010~0.0080%、
B :0~0.0050%、
Al:0~0.100%、
Ti:0~0.050%、
Cr:0~0.60%、
V :0~0.10%、
Nb:0~0.050%、
Zr:0~0.050%、および、
Ni:0~1.00%
を含有し、残部Fe及び不純物からなり、
鋼線の中心軸を含み中心軸に平行な断面において、鋼線の内部のパーライト組織の面積率が90%以上であり、鋼線の表層部のパーライト組織の面積率が80%以上であり、
前記鋼線の全体における組織のうち、セメンタイトの平均長さが1.0μm以上であるラメラ状パーライト組織の面積率が30%以上65%以下であり、かつ、セメンタイトの平均長さが0.30μm以下である分断パーライト組織の面積率が20%以上50%以下であり、
かつ、引張強さが1960MPa以上である高強度鋼線。 The component composition is in mass%,
C: 0.85 to 1.20%,
Si: 0.10 to 2.00%,
Mn: 0.20 to 1.00%,
P: 0.030% or less,
S: 0.030% or less,
N: 0.0010 to 0.0080%,
B: 0 to 0.0050%,
Al: 0 to 0.100%,
Ti: 0 to 0.050%,
Cr: 0 to 0.60%,
V: 0 to 0.10%,
Nb: 0 to 0.050%,
Zr: 0 to 0.050%, and
Ni: 0 to 1.00%
Containing the balance Fe and impurities,
In a cross section including the central axis of the steel wire and parallel to the central axis, the area ratio of pearlite structure in the steel wire is 90% or more, and the area ratio of pearlite structure in the surface layer of the steel wire is 80% or more,
Among the structures in the entire steel wire, the area ratio of lamellar pearlite structure having an average length of cementite of 1.0 μm or more is 30% to 65%, and the average length of cementite is 0.30 μm The area ratio of the divided perlite structure which is less than or equal to 20% and less than or equal to 50%,
And, a high strength steel wire having a tensile strength of 1960 MPa or more. - 鋼線の成分組成が、質量%で、更に、B:0.0001~0.0050%、Al:0.001~0.100%、およびTi:0.001~0.050%の1種または2種以上を含有する請求項1に記載の高強度鋼線。 The composition of the steel wire is, in mass%, one or more of B: 0.0001 to 0.0050%, Al: 0.001 to 0.100%, and Ti: 0.001 to 0.050%. The high strength steel wire according to claim 1 containing two or more kinds.
- 鋼線の成分組成が、質量%で、更に、Cr:0.01~0.60%、V:0.01~0.10%、Nb:0.001~0.050%、Zr:0.001~0.050%、およびNi:0.01~1.00%の1種または2種以上を含有する請求項1又は請求項2に記載の高強度鋼線。 The composition of the steel wire is, in mass%, Cr: 0.01 to 0.60%, V: 0.01 to 0.10%, Nb: 0.001 to 0.050%, Zr: 0. The high strength steel wire according to claim 1 or 2, containing one or more of 001 to 0.050% and Ni: 0.01 to 1.00%.
- 前記鋼線の直径が、1.5~8.0mmである請求項1~請求項3のいずれか1項に記載の高強度鋼線。 The high strength steel wire according to any one of claims 1 to 3, wherein a diameter of the steel wire is 1.5 to 8.0 mm.
- 前記鋼線の表面に、Zn層、およびZn合金層のいずれか1層を有するめっき層が被覆されている請求項1~請求項4のいずれか1項に記載の高強度鋼線。 The high strength steel wire according to any one of claims 1 to 4, wherein a plating layer having any one of a Zn layer and a Zn alloy layer is coated on the surface of the steel wire.
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- 2018-06-29 KR KR1020197038563A patent/KR20200016289A/en not_active Application Discontinuation
- 2018-06-29 WO PCT/JP2018/024904 patent/WO2019004454A1/en active Application Filing
- 2018-06-29 CN CN201880042600.0A patent/CN110832096A/en active Pending
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JP2021161451A (en) * | 2020-03-30 | 2021-10-11 | 日本製鉄株式会社 | Steel wire material for wire drawing |
JP2021161445A (en) * | 2020-03-30 | 2021-10-11 | 日本製鉄株式会社 | Steel wire material |
JP2021161444A (en) * | 2020-03-30 | 2021-10-11 | 日本製鉄株式会社 | Steel wire material for wire drawing |
JP2021161443A (en) * | 2020-03-30 | 2021-10-11 | 日本製鉄株式会社 | Wire and steel wire |
JP7440758B2 (en) | 2020-03-30 | 2024-02-29 | 日本製鉄株式会社 | wire rod and steel wire |
CN112458356A (en) * | 2020-10-15 | 2021-03-09 | 中天钢铁集团有限公司 | Phi 14mm wire rod for 1860MPa bridge cable galvanized steel wire and preparation method |
Also Published As
Publication number | Publication date |
---|---|
EP3647446A1 (en) | 2020-05-06 |
EP3647446A4 (en) | 2021-02-17 |
KR20200016289A (en) | 2020-02-14 |
JP6485612B1 (en) | 2019-03-20 |
JPWO2019004454A1 (en) | 2019-06-27 |
CN110832096A (en) | 2020-02-21 |
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