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US20190316238A1 - Steel wire and coated steel wire - Google Patents

Steel wire and coated steel wire Download PDF

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Publication number
US20190316238A1
US20190316238A1 US16/340,619 US201616340619A US2019316238A1 US 20190316238 A1 US20190316238 A1 US 20190316238A1 US 201616340619 A US201616340619 A US 201616340619A US 2019316238 A1 US2019316238 A1 US 2019316238A1
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Prior art keywords
steel wire
less
lamellar
cementite
steel
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Inventor
Toshiyuki Manabe
Toshihiko TESHIMA
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Nippon Steel Corp
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Nippon Steel Corp
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Assigned to NIPPON STEEL CORPORATION reassignment NIPPON STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MANABE, TOSHIYUKI, TESHIMA, Toshihiko
Publication of US20190316238A1 publication Critical patent/US20190316238A1/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • 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
    • C23C2/12—Aluminium or alloys based thereon
    • 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
    • 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
    • C21D2211/003—Cementite
    • 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 invention relates to a steel wire and a coated steel wire.
  • the present invention particularly relates to a steel wire having excellent electrical conductivity and excellent strength which is preferably used for power transmission lines and a coated steel wire having a coating layer formed on the surface of the steel wire.
  • ACSR aluminum conductor steel-reinforced cables
  • the steel wire that is used for the core portion of ACSR plays an important role as a tension member of the aluminum wires.
  • galvanized steel wires obtained by galvanizing drawn pearlitic steels or aluminum clad steel wires obtained by wire drawing aluminum clad wire rods covered with aluminum as a surface layer in order to improve the corrosion resistance of the wires are used.
  • ACSR that is used as power transmission lines is demanded to have strength and a high power transmission efficiency.
  • an increase in the aluminum cross-sectional area by reducing the weight of the core portion, a decrease in the electrical resistance of the steel wire that serves as the core portion, and the like are being studied.
  • Patent Document 1 discloses a method for reducing the specific weight of a power transmission line by using not a steel wire but a composite wire rod of a carbon fiber and aluminum or an aluminum alloy for the core portion for the purpose of reducing the weight of the core portion.
  • Patent Document 2 discloses a method in which the amounts of C, Si, and Mn in a steel wire are limited to minimum necessary amounts for the purpose of decreasing the electrical resistance of the steel wire.
  • Patent Document 1 since a carbon fiber having a higher unit price than steel is used, the cost is increased. In addition, in the technique disclosed by Patent Document 2, the amounts of the alloying elements are decreased, and thus it is difficult for the steel wire to ensure strength suitable for a tension member.
  • Non Patent Document 1 it is reported that, when first wire drawing is performed on a wire rod having a diameter of 5.5 mm in which C content is as high as 0.92% so that a diameter is 1.75 mm, furthermore after patenting is performed, and then cold wire drawing is significantly performed so that the diameter is as ultrafine as 0.26 mm, the electrical conductivity improves most under a condition of a true strain being approximately 1.5.
  • An object of the present invention is to provide a steel wire which has a wire diameter preferable for the use of power transmission lines and has excellent electrical conductivity and tensile strength and a coated steel wire having the above described steel wire and a coating layer which coats the steel wire.
  • the present inventors studied a relationship among the chemical composition of steel, the form of the structure, and the electrical conductivity. As a result, it was found that the electrical conductivity of a wire rod which serves as a material of a steel wire is improved by controlling the chemical composition and the form of cementite. As a result of additionally repeating studies with attention paid to the forms of ferrite and cementite, the present inventors found that the electrical conductivity is further improved by imparting strain to the wire rod and changing the orientations of ferrite and cementite. Furthermore, the present inventors found that a steel wire having not only excellent electrical conductivity and excellent tensile strength but also a wire diameter preferable for the use of power transmission lines can be obtained by devising the conditions of cooling and wire drawing after rolling.
  • the present inventors found that a steel wire having a wire diameter preferable for the use of power transmission lines, excellent electrical conductivity, and high tensile strength can be obtained by wire drawing a wire rod, which has an electrical conductivity increased by cooling under specific conditions after hot rolling and controlling the chemical composition and the structure, under specific conditions.
  • the present invention has been made on the basis of the above described finding, and the gist is as described below.
  • a steel wire according to an aspect of the present invention includes, as a chemical composition, by mass %, C: 0.40% to 1.10%, Si: 0.005% to 0.350%, Mn: 0.05% to 0.90%, Cr: 0% to 0.70%, Al: 0% to 0.070%, Ti: 0% to 0.050%, V: 0% to 0.10%, Nb: 0% to 0.050%, Mo: 0% to 0.20%, B: 0% to 0.0030%, and a remainder including Fe and impurities; in which a metallographic structure in a cross section includes 80 area % or more of a pearlite structure having a lamellar cementite; an average lamellar spacing which is a spacing between the lamellar cementites is 28 nm to 80 nm; an average length of the lamellar cementite is 22.0 ⁇ m or less; among the pearlite structure, a pearlite structure having the lamellar cementite of which an inclination with respect to a
  • the steel wire according to (1) may include, as the chemical composition, by mass %, one or more selected from the group consisting of Cr: 0.01% to 0.70%, Al: 0.001% to 0.070%, Ti: 0.002% to 0.050%, V: 0.002% to 0.10%, Nb: 0.002% to 0.050%, Mo: 0.02% to 0.20%, and B: 0.0003% to 0.0030%.
  • a coated steel wire according to another aspect of the present invention includes the steel wire according to (1) or (2) and a metal coating layer which coats the steel wire.
  • the metal coating layer may include at least one of the group consisting of zinc, zinc alloy, aluminum, aluminum alloy, copper, copper alloy, nickel, and nickel alloy.
  • the wire diameter of the steel wire that serves as a core material is large, and the electrical conductivity and the tensile strength are excellent. Therefore, the steel wire and the coated steel wire can be preferably used for the use of power transmission lines.
  • FIG. 1 is a view showing a cross section parallel to a longitudinal direction of a steel wire (L cross section) and a schematic view that shows a method for measuring an average length of lamellar cementite in a pearlite structure having lamellar cementite.
  • FIG. 2A is a view that shows a method for measuring an area ratio of a pearlite structure having lamellar cementite of which an inclination with respect to a longitudinal direction of the steel wire (angular difference) is 15° or less and a photograph showing an example of lamellar cementite having an inclination being 15° or less.
  • FIG. 2B is a view that shows the method for measuring the area ratio of the pearlite structure having the lamellar cementite of which the inclination with respect to the longitudinal direction of the steel wire (angular difference) is 15° or less and a photograph showing an example of lamellar cementite having an inclination being not 15° or less.
  • FIG. 3A is a view showing an L cross section of the steel wire and a schematic view showing a TD direction and an RD direction.
  • FIG. 3B is a view showing the L cross section of the steel wire and a schematic view that shows a method for measuring an integration degree of ferrite.
  • a steel wire according to an embodiment of the present invention (the steel wire according to the present embodiment) and a coated steel wire according to an embodiment of the present invention (the coated steel wire according to the present embodiment) will be described below.
  • the steel wire according to the present embodiment has steel composition described below (chemical composition) and includes a pearlite structure having lamellar cementite in a metallographic structure (hereinafter, simply referred to as “the pearlite structure” in some cases).
  • an average lamellar spacing between the lamellar cementites in the pearlite structure is 28 nm to 80 nm
  • an average length of the lamellar cementite is 22.0 ⁇ m or less
  • among the pearlite structure a pearlite structure having the lamellar cementite of which an inclination with respect to a longitudinal direction of the steel wire is 15° or less is 40 area % or more
  • an integration degree of a ⁇ 110 ⁇ plane of ferrite with respect to the longitudinal direction, which is obtained using an X-ray diffraction method, is in a range of 2.0 to 8.0.
  • the steel wire according to the present embodiment has a diameter of 1.4 mm or more.
  • the C has an effect of increasing the pearlite fraction in steel and refining the lamellar spacing in the pearlite structure.
  • the strength is improved.
  • the C content is set to 0.40% or more.
  • the C content is preferably 0.60% or more.
  • the C content is set to 1.10% or less.
  • the C content is preferably 1.05% or less, more preferably 1.00% or less, and still more preferably 0.95% or less.
  • Si is an effective element for increasing the strength of steel by solid solution strengthening and is also an element necessary as a deoxidizing agent.
  • the Si content is preferably set to 0.010% or more and more preferably set to 0.020% or more.
  • Si is an element that increases the electrical resistivity when distributed in ferrite in the pearlite structure. When the Si content exceeds 0.350%, the electrical resistivity is significantly increased, and thus the Si content is set to 0.350% or less.
  • the Si content is preferably set to 0.250% or less and more preferably set to 0.150% or less.
  • the Si content is preferably set to 0.050% Of more.
  • Mn is a deoxidizing element and an element having an action of preventing hot brittleness by fixing S in steel as MnS.
  • Mn is an element that improves hardenability, decreases the microstructure fraction of ferrite during patenting, and contributes to the improvement of strength.
  • the Mn content is set to 0.05% or more.
  • the Mn content is set to 0.90% or less.
  • the Mn content is preferably 0.75% or less and more preferably 0.60% or less.
  • the steel wire according to the present embodiment basically includes the above described elements and the remainder including Fe and impurities.
  • the amounts of N, P, and S are preferably limited as described below.
  • contents thereof are small and may be 0%.
  • the impurities refer to elements that are inevitably mixed into the steel wire from a raw material or the like or during manufacturing steel.
  • N is an element that degrades ductility by strain aging during cold working and also decreases electrical conductivity. Particularly, when the N content exceeds 0.0100%, the ductility and the electrical conductivity significantly are decreased, and thus the N content is preferably limited to 0.0100% or less.
  • the N content is more preferably 0.0080% or less and still more preferably 0.0050% or less.
  • the P is an element that contributes to the solid solution strengthening of ferrite but significantly degrades ductility. Particularly, when the P content exceeds 0.030%, the degradation in wire drawability during the wire drawing of a wire rod to a steel wire becomes significant. Therefore, the P content is preferably limited to 0.030% or less. The P content is more preferably 0.020% or less and still more preferably 0.012% or less.
  • S is an element that causes red brittleness and degrades ductility.
  • the S content exceeds 0.030%, the degradation in ductility becomes significant. Therefore, the S content is preferably limited to 0.030% or less.
  • the S content is more preferably 0.020% or less and still more preferably 0.010% or less.
  • the steel wire according to the present embodiment basically includes the above described elements and the remainder including Fe and impurities.
  • the steel wire may contain one or more elements selected from the group consisting of Cr, Al, Ti, V, Nb, Mo, and B in a range described below instead of some of Fe. Since it is not necessary that these elements need to be contained, and the lower limits thereof are 0%. In addition, since the properties of the steel wire are not impaired even in a case where these arbitrary elements are contained in an amount less than the range described below, the case is acceptable.
  • the Cr is an element that improves the hardenability of steel and an element that increases the tensile strength by decreasing the lamellar spacing of the lamellar cementite in the pearlite structure.
  • the Cr content is preferably set to 0.01% or more.
  • the Cr content is more preferably 0.02% or more.
  • the upper limit of the Cr content is preferably set to 0.70%.
  • Al is a deoxidizing element and an element that contributes to the refining of austenite grain size by fixing nitrogen as a nitride.
  • the Al content is preferably set to 0.001% or more.
  • Al is an element that decreases the electrical conductivity. Therefore, even in a case where Al is contained, the upper limit of the Al content is preferably set to 0.070%. A more preferred upper limit is 0.050%.
  • Ti is a deoxidizing element and an element that contributes to the refining of austenite grain size by forming a carbonitride.
  • the Ti content is preferably set to 0.002% or more.
  • the upper limit of the Ti content is preferably set to 0.050%. A more preferred Ti content is less than 0.030%.
  • V is an element that improves the hardenability of steel and an element that contributes to the improvement of the strength of steel by being precipitated as a carbonitride.
  • the V content is preferably set to 0.002% or more.
  • the upper limit of the V content is preferably set to 0.10%. A more preferred upper limit is 0.08%.
  • Nb is an element that improves the hardenability of steel and an element that contributes to the refining of austenite grain size by being precipitated as a carbide.
  • the Nb content is preferably set to 0.002% or more.
  • the Nb content exceeds 0.050%, the time until ending the transformation during patenting becomes long. Therefore, even in a case where Nb is contained, the Nb content is preferably set to 0.050% or less.
  • the Nb content is more preferably 0.020% or less.
  • Mo is an element that improves the hardenability of steel and decreases the area ratio of ferrite in the structure.
  • the Mo content is preferably set to 0.02% or more.
  • the Mo content is preferably set to 0.20% or less.
  • the Mo content is more preferably 0.10% or less.
  • the B is an element that improves the hardenability of steel and an element that increases the pearlite area ratio by suppressing the generation of ferrite.
  • the B content is preferably set to 0.0003% or more.
  • M 23 (C, B) 6 is precipitated on austenite grain boundaries in a supercooled austenite state during patenting, and ductility is degraded. Therefore, even in a case where B is contained, the B content is preferably set to 0.0030% or less.
  • the B content is more preferably 0.0020% or less.
  • the steel wire according to the present embodiment intends to provide a tensile strength of 1,500 MPa or more, preferably 1,600 MPa or more, and more preferably 2,000 MPa or more in consideration of the application to steel cores of ACSR that constitutes power transmission lines.
  • the steel wire according to the present embodiment needs to include a metallographic structure described below.
  • a cross section refers to a so-called L cross section that is parallel to the longitudinal direction of the steel wire and passes through the longitudinal-direction central axis of the steel wire.
  • the steel wire according to the present embodiment includes 80 area % or more of a pearlite structure having lamellar cementite in the metallographic structure of a cross section.
  • the area ratio of the pearlite structure having lamellar cementite is preferably 95 area % or more, more preferably 97 area % or more, and may be 100 area %.
  • the pearlite structure having lamellar cementite refers to a structure that is derived from pearlite or pseudo pearlite present in a wire rod before wire drawing and a structure in which cementite phase (lamellar cementite) and ferrite phase are alternately repeated and overlaid.
  • the pearlite structure having lamellar cementite in the present embodiment is a structure including cementites that are present linearly, in a curved shape, or fragmentarily and ferrite phase present between the cementites.
  • the steel wire according to the present embodiment may include a ferrite structure in addition to the pearlite structure.
  • the ferrite structure exceeds 20 area %, the area ratio of the pearlite structure is decreased, and the tensile strength is decreased. Therefore, the ferrite structure needs to be limited to 20 area % or less.
  • the ferrite structure mentioned herein is not the ferrite phase that is included in the pearlite structure.
  • the steel wire according to the present embodiment includes a small amount of a bainite structure or a martensite structure in addition to the pearlite structure and the ferrite structure.
  • bainite or martensite that is a diffusionless transformation-type structure is a structure in which the diffusion of a solid solute element is staggered.
  • the bainite structure and the martensite structure are preferably set to less than 3 area % in total.
  • the microstructure fractions in the steel wire are obtained by capturing a metallographic structure photograph from an observation place of the average lamellar spacing on a cut surface of the steel wire described below at a magnification of 2,000 times, marking the regions of the respective structures, and computing the average values of the area ratios of the respective structures by an image analysis.
  • the average lamellar spacing that is a spacing between lamellar cementites adjacent to each other in the pearlite structure is in a range of 28 nm to 80 nm.
  • the average lamellar spacing reaches less than 28 nm, the electrical conductivity of the steel wire is decreased.
  • the average lamellar spacing is more than 80 nm, it is not possible to sufficiently increase the electrical conductivity and the tensile strength.
  • the average lamellar spacing is measured using the following method. That is, the L cross section of the steel wire is implanted into a resin, polished to a mirror surface, and then etched with picral, and digital images of 10 views of arbitrary regions including five or more pearlite blocks are captured using FE-SEM at a magnification of 5,000 times to 10,000 times. From the respective captured photographs, the average lamellar spacings are measured using an image analyzer.
  • the lamellar spacing refers to the distance from the center of a lamellar cementite to the center of the closest lamellar cementite.
  • ⁇ Average Length of Lamellar Cementite is 22.0 ⁇ m or Less>
  • the average length of the lamellar cementite in the pearlite structure is 22.0 ⁇ m or less.
  • the electrical conductivity of the steel wire is decreased.
  • the average length of the lamellar cementite is preferably 12.0 ⁇ m or less and more preferably 10.0 ⁇ m or less.
  • the average length of the lamellar cementite is preferably 1.0 ⁇ m or more, more preferably 2.0 ⁇ m or more, and still more preferably 5.0 ⁇ m or more.
  • the average length of the lamellar cementite in the pearlite structure is measured using the following method. That is, a cut surface of the steel wire in the longitudinal direction (wire drawing direction) (the L cross section) is mirror-polished and then etched with picral, the structure is observed using FE-SEM, and the results of the structural observation are analyzed, thereby obtaining the average length of the lamellar cementite. Specifically, as shown in FIG. 1 , on a cross section of the steel wire, a region from the axial-direction central location (D/2) of the steel wire to D/4 locations (D represents the diameter of the steel wire) is set. The set region is a rectangular region in which the lengths of individual sides reach D/2.
  • This rectangular region is further divided into nine equal meshes, and the vertices (16 places) of the respective divided meshes are used as observation locations.
  • capture regions are set at a magnification of 10,000 times so that the wire drawing direction becomes parallel to images, and the surface of the cross section is captured using FE-SEM.
  • the images of the capture regions are analyzed, cementite portions and the other portions (ferrite portions) are binarized, and the lengths of cementite along the long side are obtained.
  • the obtained cementite lengths are averaged, thereby computing the average length of cementite.
  • a pearlite structure having lamellar cementite of which the inclination (angular difference) with respect to the longitudinal direction of the steel wire is 15° or less is 40 area % or more by the area ratio.
  • the area ratio of the pearlite structure having the lamellar cementite of which the inclination is 15° or less is less than 40 area %, the electrical conductivity is decreased.
  • the area ratio of the pearlite structure having the lamellar cementite of which the inclination with respect to the longitudinal direction of the steel wire is 15° or less is preferably 55 area % or more and more preferably 60 area % or more.
  • the proportion of the lamellar cementite of which the inclination with respect to the longitudinal direction of the steel wire is 15° or less is high from the viewpoint of the electrical conductivity, and thus the upper limit of the area ratio of the pearlite structure having the lamellar cementite of which the inclination is 15° or less is 100 area %.
  • the area ratio of the pearlite structure having the lamellar cementite of which the inclination with respect to the longitudinal direction of the steel wire is 15° or less is measured using the following method. That is, each of the images captured in the measurement of the average length of the lamellar cementite is used, in a region of a drawn pearlite structure in which the orientations of lamellar cementites in the image central part (pearlite colony) are equal to one another, both terminals of one lamellar cementite are connected with a line segment, the angular difference from the horizontal direction is measured, and whether or not the angular difference is 15° or less is confirmed.
  • the region is determined as the pearlite structure having lamellar cementite of which the inclination with respect to the longitudinal direction of the steel wire is 15° or less.
  • the lamellar cementite is determined as lamellar cementite of which the inclination is not 15° or less, and the region is not included as “the pearlite structure in which the inclination of lamellar cementite with respect to the longitudinal direction of the steel wire is 15° or less”.
  • FIG. 2A is an example of an image showing a pearlite structure in which the inclination is in a range of 15° or less in the region of the drawn pearlite structure in which the orientations of lamellar cementites in the central part are equal to one another
  • FIG. 2B is an example of an image showing a pearlite structure in which the inclination is not 15° or less.
  • the integration degree of a ⁇ 110 ⁇ plane of ferrite with respect to the longitudinal direction of the steel wire is in a range of 2.0 to 8.0. In a case where the integration degree of the ⁇ 110 ⁇ plane of ferrite is less than 2.0 or more than 8.0, the electrical conductivity of the steel wire is decreased, which is not preferable. Meanwhile, from the viewpoint of the electrical conductivity and the tensile strength, the integration degree of the ⁇ 110 ⁇ plane of ferrite is preferably 2.2 to 5.5 and more preferably 3.0 to 4.5.
  • the integration degree of ferrite is measured using the following method. That is, in a region from the central part to D/4 (D represents the diameter of the steel wire) in a radial direction of a cut surface in the longitudinal direction (the wire drawing direction) of the steel wire shown in FIG. 3B , a ⁇ 110 ⁇ pole figure is produced using an X-ray diffraction method, and the absolute maximum value of the pole densities (ratios to a random orientation) of spots observed in an RD direction (the longitudinal direction of the steel wire) is considered as the integration degree of the ⁇ 110 ⁇ plane of ferrite.
  • the integration degree of the ⁇ 110 ⁇ plane of ferrite that is obtained by X-ray diffraction refers to the integration degree being computed from information obtained from both ferrite phase included in the pearlite structure and ferrite that is not the pearlite structure.
  • the measurement conditions of the X-ray diffraction in the present embodiment are as described below.
  • the steel wire according to the present embodiment has a wire diameter of 1.4 mm or more.
  • the wire diameter is 1.4 mm or more, the wire drawing of wire rods and the manufacturing of coated steel wires having a metal coating layer of aluminum, zinc, or the like formed around the steel wire are easy. Therefore, the steel wire according to the present embodiment is also excellent in views of the drawnability and the manufacturing costs in addition to the electrical conductivity and the tensile strength.
  • the diameter of the steel wire according to the present embodiment is preferably 1.5 mm or more and more preferably 1.6 mm or more.
  • the diameter of the steel wire is preferably 4.2 mm or less and more preferably 4.0 mm or less.
  • the steel wire according to the present embodiment is excellent for both the electrical conductivity and the tensile strength.
  • the electrical resistivity that is an index of the electrical conductivity is preferably less than 19.0 ⁇ cm, more preferably less than 18.0 ⁇ cm, and still more preferably less than 17.0 ⁇ cm.
  • the tensile strength of the steel wire according to the present embodiment is preferably 1,500 MPa or more, more preferably 1,600 MPa or more, and still more preferably 2,000 MPa or more.
  • a coated steel wire according to the present embodiment includes the steel wire according to the present embodiment and a metal coating layer that coats the steel wire. That is, the coated steel wire according to the present embodiment is a metal-coated steel wire.
  • the metal coating layer includes, for example, at least one of the group consisting of zinc, a zinc alloy, aluminum, an aluminum alloy, copper, a copper alloy, nickel, and a nickel alloy.
  • the metal coating layer may be a plated layer or a clad layer.
  • the plated layer may be an electroplated layer or a hot-dipped layer.
  • an alloying layer is formed in the interface between the steel wire and the metal coating layer.
  • As the alloying layer a ZnFe alloying layer, an AlFe alloying layer, a NiFe alloying layer, and a CuFe alloying layer can be exemplified.
  • the coated steel wire has the metal coating layer, it is possible to increase the electrical conductivity of the entire coated steel wire.
  • the manufacturing method described below is an example, and the method for manufacturing the steel wire according to the present embodiment and the coated steel wire according to the present embodiment is not limited to manufacturing conditions described below as long as steel wires or coated steel wires satisfying the scope of the present invention can be obtained.
  • a steel piece (billet) is manufactured by continuous casting or the like, and hot rolling is carried out. After the casting, blooming may be carried out.
  • hot rolling it is preferable that the steel piece is heated so that the central part of the steel piece is reached 1,000° C. to 1,100° C., hot rolling in which the finish temperature is set to 900° C. to 1,000° C. is carried out, and thus a wire rod is obtained.
  • cooling is carried out by water cooling, air cooling, furnace cooling, and/or immersion in a melting bath.
  • the cooling pattern is preferably set depending on the C content.
  • the wire rod is cooled to a temperature range of 800° C. to 920° C. at an average cooling rate of 20° C./s or more (first cooling), then, cooled so that the average cooling rate in a temperature range of 800° C. to 600° C. reaches 5° C./s to 20° C./s (second cooling), and then cooled so that the average cooling rate in a temperature range of 600° C. to 500° C. reaches 5° C./s or less (third cooling).
  • the cooling rate of the first cooling is less than 20° C./s, proeutectoid ferrite is likely to be generated, and the microstructure fraction of pearlite is decreased.
  • the first cooling stop temperature is less than 800° C., austenite grain size are refined, and sufficient hardenability cannot be obtained.
  • the first cooling stop temperature is more than 920° C., proeutectoid ferrite is likely to be generated in the subsequent cooling, and the microstructure fraction of pearlite is decreased.
  • the cooling rate of the second cooling is less than 5° C./s
  • the microstructure fraction of pearlite is likely to be decreased by the generation of proeutectoid ferrite.
  • the cooling rate of the second cooling is more than 20° C./s
  • pearlitic transformation and the distribution of alloying elements become insufficient throughout the second and third cooling.
  • the cooling rate of the third cooling is more than 5° C./s, the distribution of the alloying element does not easily occur, and thus the electrical conductivity is decreased.
  • the wire rod may be heated again to a temperature range of 600° C. to 400° C.
  • the wire rod is cooled to 800° C. to 920° C. at an average cooling rate of 20° C./s or more and immersed in a molten salt of 500° C. to 600° C. for 30 seconds or more, and thus pearlitic transformation is caused.
  • the finish temperature of rolling refers to the surface temperature of the wire rod immediately after the finish rolling
  • the average cooling rate in the cooling after the finish rolling refers to the cooling rate of the central part of the wire rod.
  • the wire rod obtained through the above described manufacturing process for example, 80% or more of the metallographic structure in a cross section is a pearlite structure, the average lamellar spacing of the pearlite structure is 50 nm to 170 nm, and the average length of lamellar cementite in the pearlite structure becomes 1.5 ⁇ m or less.
  • the wire diameter of the wire rod manufactured by the above described manufacturing process is preferably 3.0 mm to 14.0 mm
  • wire drawing is performed on the wire rod, so that a steel wire is obtained.
  • the wire drawing it is preferable that the wire drawing is performed on the wire rod as to impart a true strain of 1.5 to 2.4.
  • the true strain is preferably 1.7 to 2.1.
  • the electrical resistivity of the steel wire after the wire drawing is decreased by approximately 1.0 ⁇ cm to 1.5 ⁇ cm relative to the wire rod before the wire drawing (that is, the electrical conductivity is increased).
  • steel wires having a low electrical resistivity and a high tensile strength can be obtained even when the true strain is less than 1.5 or more than 2.4.
  • a true strain of 1.5 to 2.4 is imparted to the above described kind of steel, it is easy to obtain steel wires having a high tensile strength and an electrical resistivity that is suppressed to be lower.
  • the average lamellar spacing is decreased, the average length of lamellar cementites is increased, the inclination of lamellar cementite with respect to the longitudinal direction is decreased, the proportion of the pearlite structure having cementite of which the angular difference is 15° or less is increased, and the integration degree of the ⁇ 110 ⁇ plane of ferrite is increased.
  • the proportion of cementite of which the angular difference is 15° or less is insufficient, and the electrical conductivity is decreased.
  • the wire drawing is carried out under a condition in which the true strain exceeds 2.4, the amount of solid solute C in ferrite is increased, and thus the electrical conductivity is decreased.
  • the steel wire according to the present embodiment is manufactured.
  • a method for forming the metal coating layer may be any of an electroplating method, a hot dipping method, and a cladding method.
  • the thickness of the metal coating layer at this time is preferably as thick as approximately 0.7% to 20% of the diameter of the wire rod or the steel wire.
  • the coated steel wire according to the present embodiment is manufactured.
  • the coating may be carried out between the cooling and the wire drawing. That is, the coated steel wire according to the present embodiment can be obtained even when the wire drawing is carried out after forming the metal coating layer on the wire rod.
  • Molten steel melted to chemical composition shown in Table 1 (here, the remainder was Fe and impurities) in a 50 kg vacuum melting furnace was cast to ingots.
  • the respective ingots were heated at 1,250° C. for one hour and then hot-forged so as to become bar wire rods having a diameter of 15 mm so that the finish temperature was 950° C. or more, and then cooled in the air to room temperature.
  • These hot-forged materials were machined to a diameter of 10 mm and cut to a length of 1,500 mm.
  • These machined materials were heated in a nitrogen atmosphere at 1,050° C. for 15 minutes and then hot-rolled so that the finish temperature was 900° C. or more, thereby obtaining rolled materials having a diameter of 7 mm.
  • metal coating layers were formed using a hot dip galvanizing method or an aluminum cladding method.
  • wire drawing was performed on the wire rods so as to impart true strains shown in Table 3 to steel portions included in the wire rods, thereby obtaining steel wires or coated steel wires in which the diameters of the steel portions were 2.0 mm to 3.5 mm.
  • the metal coating layers were removed from the coated steel wires obtained in the above described manner using hydrochloric acid, sodium hydroxide, or the like to take out steel wires, and the tensile strengths and the electrical conductivities of these steel wires were evaluated.
  • Three tensile test pieces having a length of 350 mm were sampled in a wire form from the steel wire.
  • a tensile test was carried out at normal temperature on these tensile test pieces with an inter-chuck distance of 200 mm at a tensile rate of 10 mm/min, tensile strengths (TS) were measured, and the average value thereof was considered as the tensile strength of this test specimen.
  • TS tensile strengths
  • test piece for electrical conductivity measurement having a length of 60 mm was cut out from the steel wire, and the electrical resistivity was measured at a temperature of 20° C. using a four-terminal method.
  • the L cross section was implanted into a resin, polished to a mirror surface, and then etched with picral, and digital images of 10 views of arbitrary regions including five or more pearlite blocks were captured using FE-SEM at a magnification of 5,000 times to 10,000 times. From the respective photographs, the average lamellar spacings were measured using an image analyzer.
  • a metallographic structure photograph was captured at a magnification of 2,000 times at the observation place of the average lamellar spacing of the cut surface of each of the steel wires, the regions of individual structures were marked, and the average values of the area ratios of the individual structures were computed by an image analysis. Meanwhile, Table 3 shows the area ratios of a pearlite structure and a ferrite structure; however, for steel wires in which the total of these structures was not 100%, a bainite structure and/or a martensite structure were observed as other structures.
  • the average length of lamellar cementite in the pearlite structure was obtained by using the sample provided for the measurement of the average lamellar spacing, carrying out structural observation using FE-SEM, and analyzing the results of the structural observation.
  • a region from the axial-direction central location (D/2) of the steel wire to D/4 locations (D represents the diameter of the steel wire) was set.
  • the set region was a rectangular region in which the lengths of individual sides reached D/2. This rectangular region was further divided into nine equal meshes, and the vertices of the respective divided meshes were used as observation locations.
  • capture regions were set at a magnification of 10,000 times so that the wire drawing direction became parallel to images, and the surface of the cross section was captured using FE-SEM.
  • the images of the capture regions were analyzed, cementite portions and the other portions (ferrite portions) were binarized, and the lengths of cementite along the long side were obtained.
  • the obtained cementite lengths were averaged, thereby computing the average length of cementite.
  • each of the images captured in the measurement of the average length of the lamellar cementite was used, in a region of a drawn pearlite structure in which the orientations of lamellar cementites in the image central part were equal to one another, both terminals of one lamellar cementite were connected with a line segment, the angular difference from the horizontal direction was measured, and whether or not the angular difference is 15° or less was confirmed.
  • the integration degree of a ⁇ 110 ⁇ plane of ferrite was measured as described below.
  • D represents the diameter of the steel wire
  • RD direction wire drawing direction
  • a ⁇ 110 ⁇ pole figure was produced using an X-ray diffraction method, and the maximum value of the pole densities (ratios to a random orientation) of spots observed in the RD direction was considered as the integration degree of the ⁇ 110 ⁇ plane of ferrite.
  • the measurement conditions of the X-ray diffraction are as described above.
  • Table 3 shows that, in the case of the test numbers 19 to 22 and 28 to 30 not satisfying the conditions regulated by the present invention, at least one of the above described properties failed to reach the target values (tensile strength: 1,500 MPa or more, electrical resistivity: less than 19.0 ⁇ cm, and diameter: 1.4 mm or more). In contrast, in the test numbers 3 to 18, 23, 26, 27, 31, and 32 satisfying all of the conditions regulated by the present invention, all of the above described properties reached the target values. Meanwhile, for all of the test numbers 11 to 14, 26, 27, and 32, a kind of steel K was used; however, in the test number 11 to 14 and 32 in which the true strain during the wire drawing was 1.5 to 2.4, particularly, the electrical resistivity was suppressed to be low.
  • a steel wire which has a wire diameter preferable for the use of power transmission lines and is excellent for electrical conductivity and tensile strength and a coated steel wire having the above described steel wire and a coating layer that coats the steel wire.
  • the steel wire and the coated steel wire of the present invention have a large wire diameter and is excellent for the electrical conductivity and the tensile strength and thus can be preferably used for the use of power transmission lines.

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