EP2447382B1 - High-strength ultra-fine steel wire and manufacturing method therefor - Google Patents

High-strength ultra-fine steel wire and manufacturing method therefor Download PDF

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Publication number
EP2447382B1
EP2447382B1 EP10778818.4A EP10778818A EP2447382B1 EP 2447382 B1 EP2447382 B1 EP 2447382B1 EP 10778818 A EP10778818 A EP 10778818A EP 2447382 B1 EP2447382 B1 EP 2447382B1
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Prior art keywords
steel wire
mass
wire
ferrite phase
concentration
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German (de)
English (en)
French (fr)
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EP2447382A1 (en
EP2447382A4 (en
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Jun Takahashi
Makoto Kosaka
Junichi Kodama
Toshimi Tarui
Tamaki Suzuki
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C22C38/12—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working

Definitions

  • the present invention relates to a high-strength steel wire used for a steel cord for a vehicle tire, a saw wire and the like, and a method of manufacturing the same. More specifically, the present invention relates to an ultrathin steel wire that is strengthened through a wire-drawing working at a cold temperature using a die and that has a wire diameter of 0.04-0.4 mm and the strength of 4500 MPa grade or more.
  • indices for indicating the degree of ductility such as the number of twistings until breakage of a steel wire under a twisting test, and the presence or absence of the occurrence of cracks (delamination) appearing in a longitudinal direction of a steel wire during the twisting test.
  • the increase in strength of the steel wire leads to a decrease in ductility, and it is important to suppress a decrease in ductility.
  • high-strength steel wire deteriorates its properties through aging at room temperature (20-40°C, several days to several years), and hence, it is also important not to substantially decrease favorable ductility through aging.
  • a high-strength steel wire is manufactured such that a wire material having a pearlite structure is subjected to a wire-drawing working using a die. With this working, a distance between pearlite lamellas becomes small, and a large amount of dislocation is introduced into a ferrite phase, whereby the tensile strength increases. Recently, it has been found that the cementite in the pearlite structure is decomposed into fine pieces when strain on the wire excessively increases. However, because of the extremely fine structure, the relationship between mechanical properties and the location and the state in which the carbon exists has not yet been uncovered, and in particular, many unclear points concerning the cause of the deterioration of ductility still exist. In the actual high-strength steel wire, it is believed that the surface region and the central region in the steel wire do not always exhibit the same structure and the same amount of local strain, and this affects the properties of the steel wire.
  • Patent Document 1 Patent Document 2, and Patent Document 3 propose a high-carbon steel wire material for an ultrathin wire having high strength and high ductility, in which chemical components of C, Si, Mn, Cr and the like are defined.
  • the maximum tensile strength of the steel wire is 3500-3600 MPa, and there exists a limitation on highly strengthening the steel wire.
  • Patent Document 4 proposes a highly-strengthened steel and high-toughness steel wire material in which chemical components, structures of non-metallic inclusions, and an area percentage of pro-eutectoid cementite are controlled.
  • Patent Document 5 discloses a method of manufacturing the high-strength steel and high-toughness ultrathin wire steel in which chemical components of steel and area reduction rate at the final die are controlled.
  • Patent Document 6 intends to obtain favorable properties by defining the carbon concentration in the steel wire.
  • Patent Document 7 discloses a method of realizing a favorable carbon condition and obtaining favorable properties by further modifying heat treatment.
  • Patent Document 8 intends to obtain favorable properties by defining the carbon concentration and the distance between lamellas in the steel wire.
  • these Patent Documents do not refer to a carbon condition in an outermost layer (region from a surface to a depth of 2 ⁇ m) of the steel wire. This is because the previous techniques were not able to perform measurement (and control).
  • Patent Document 9 defines variations in the carbon concentration.
  • Patent Document 10 defines a degree of difference in the distance between lamella, which affects the variations of the carbon concentration. However, these Patent Documents only refer to the entire variations, and do not define the carbon concentration at a specific location.
  • Patent Document 11 describes a steel wire and a method of manufacturing the steel wire for obtaining favorable properties by defining C concentration ratio in the ferrite phase at a surface layer portion of the steel wire and the ferrite phase at a center portion of the steel wire. However, Patent Document 11 only defines a relative value at the center portion and the surface layer portion, and does not define the absolute value to be used as a clear index. Further, the measurement is performed for the inside of the steel wire below 10 ⁇ m or more from the surface of the steel wire, and the C concentration in a region (outermost layer) from the surface to a depth of 2 ⁇ m is not controlled.
  • Patent Document 12 and Patent Document 13 define a range of the residual stress in terms of fatigue and longitudinal crack resistance.
  • Patent Document 12 and Patent Document 13 describe that the residual compressive stress is favorable, an absolute value thereof is small, and the range for keeping an extremely excellent ductility and strength in balance is not defined. Further, there has not existed any example that discloses the relationship with the carbon condition in the outermost layer.
  • Ductility of the ferrite phase plays a main role in the ductility of the high-strength ultrathin steel wire, and thus, the ductility of the high-strength ultrathin steel wire can be secured by maintaining the ductility of the ferrite phase.
  • the cementite is decomposed, C atoms are diffused in the ferrite phase, and the carbon concentration in the ferrite phase increases.
  • Non-Patent Document 1 describes that, in a cold-rolled steel sheet, as the carbon concentration in the ferrite phase increases, a dynamic strain aging in which dislocation in the ferrite phase fixes with carbon occurs during tensile test, which causes a large decrease in the ductility.
  • Non-Patent Document 1 Journal of Japan Institute of Metal, Vol. 45, No. 9, (1981) 942-947
  • the present invention provides a high-strength steel wire, in particular, a high-strength ultrathin steel wire having both high strength of 4500 MPa or more and excellent ductility.
  • the present invention employs the following measures for solving the problems described above.
  • a carbon concentration at a center of a ferrite phase in the outermost surface layer of the steel wire having a pearlite structure is controlled, and the residual compressive stress is added, whereby the steel wire can exhibit the high strength and ductility. Further, it is possible to provide a high-strength steel wire having the sufficient ductility and tensile strength, whereby it is possible to reduce weight of a manufactured product.
  • the present inventors made various analyses on primary factors of ductility of the high-strength steel wire, and found that, in the pearlite structure of heavily drawn wire, the concentration of carbon (hereinafter, referred to as C) in the ferrite phase in the outermost layer of the steel wire and the residual stress in the outermost layer of the steel wire in the longitudinal direction of the steel wire strongly affect the ductility of the steel wire. It is considered that this is because, at the time of bending and twisting, the strong stress is applied to the outermost layer of the steel wire as compared with the inner side thereof, and the outermost layer of the steel wire becomes a starting point of breakage.
  • C concentration of carbon
  • the outermost layer of the steel wire is subjected to heavier working, and receives more considerable temperature changes due to the friction heat and the like, as compared with the inner portion of the steel wire, and hence, it has a structure and state obviously different from the inner portion of the steel wire. Then, cementite is further decomposed, and the ferrite phase in the outermost layer exhibits the higher C concentration than that in the inner portion. Accordingly, the inventors discovered that the steel wire exhibiting an excellent balance between the strength and the ductility can be largely achieved by controlling the structure and the like of the outermost layer because the properties are affected primarily by the outermost layer of the steel wire.
  • the high-strength steel wire is obtained such that a wire material having the pearlite structure is strengthened by applying the high wire-drawing working using a die and the like.
  • high wire-drawing strain is generated at the time of the high wire-drawing working, which leads to occurrence of a phenomenon in which the cementite in the pearlite structure is finely decomposed, and C is dissolved into the ferrite phase.
  • the present inventors combined the three-dimensional atom probe technique (hereinafter, referred to as 3DAP) capable of measuring a local C concentration in the fine region, with a needle-specimen creating technique from the outermost layer of the steel wire which has become available for the first time in the present specification, and investigated in detail the relationship between the C concentration and the strength/ductility of the steel wire in the ferrite phase at every location in the steel wire.
  • 3DAP three-dimensional atom probe technique
  • the present inventors prepared specimens having a tensile strength of 4500MPa or more through various manufacturing methods, and investigated a relationship between the tensile strength and ductility, the average C concentration at the center portion of the ferrite phase in the pearlite structure in the surface, and the residual stress on the surface.
  • the average C concentration at the center portion of the ferrite phase in the outermost layer of the steel wire was measured using the 3DAP, and the residual stress was investigated using the X-ray diffraction method.
  • the measurement of the tensile strength was made using the tensile strength tester, and the twisting test, which is one of ductility evaluations, was made using the twisting tester.
  • the twisting tester As an index for ductility, the number of twistings until breakage of the steel wire was measured.
  • FIG. 1 shows results obtained by investigating the relationship between the average C concentration at the center portion of the ferrite phase located at a position 1 ⁇ m below the surface of the steel wire, the residual stress in the longitudinal direction of the steel wire in the outermost layer of the steel wire, and, the ductility represented by the number of twistings until breakage of the steel wire under the twisting test.
  • the white circles represent specimens with the twisting number of 20 or more
  • the white squares extreme ductility
  • the black triangles represent specimens with the twisting number of less than 20.
  • the steel wire having the tensile strength of 4500 MPa or more and the favorable ductility was observed only when the average C concentration at the center portion of the ferrite phase in the outermost layer of the steel wire is 0.2 mass% or lower, and at the same time, the residual stress is a large compressive stress of -600MPa or lower. Further, the steel wire having the extremely favorable ductility was observed when the average C concentration at the center portion of the ferrite phase is 0.1 mass% or lower, and at the same time, the residual stress is a strong compressive stress of -600MPa or lower.
  • the average C concentration at the center portion of the ferrite phase in the outermost layer of the steel wire be 0.2 mass% or lower, more preferably, 0.1 mass% or lower, and at the same time, the residual stress in the longitudinal direction of the steel wire be -600 MPa, more preferably, -700 MPA or lower.
  • the lowest value of the average C concentration at the central portion of the ferrite phase in the outermost layer may be set at 0.0001 mass%.
  • the maximum value of the residual compressive stress corresponds to the yield stress in theory, and may be set substantially at -3000 MPa. It is not practical to apply the compressive stress larger than the value above, because it leads to significant increase in cost.
  • the outermost layer of the steel wire means a region from a surface to a depth of 2 ⁇ m excluding a plated layer or other foreign-substance layers on the surface.
  • the central portion of the ferrite phase in the pearlite structure in the outermost layer of the steel wire means a region (region of half of the ferrite phase width) from the central plane of the ferrite phase to a portion located at one-fourth of the width of the ferrite phase toward both sides thereof.
  • a steel wire including C: 0.7-1.2 mass%, Si: 0.05-2.0 mass%, Mn: 0.2-2.0 mass% with a balance including Fe and inevitable impurities.
  • This steel wire having the pearlite structure to which the wire-drawing working is applied is characterized in that the average C concentration at the center portion of the ferrite phase in the outermost layer is 0.2 mass% or lower, and the residual compressive stress in the longitudinal direction of the steel wire in the outermost layer of the steel wire is 600 MPa or more.
  • C is effective in increasing the tensile strength of the wire after the patenting treatment and the hardening rate of the wire at the time of the wire-drawing working. This makes it possible to increase the tensile strength with the smaller strain at the time of the wire-drawing working.
  • the amount of C content is 0.7% or lower, it is difficult to achieve the high-strength steel wire that is the object of the present invention.
  • the amount of C content exceeds 1.2%, pro-eutectoid cementite segregates in the austenite grain boundary at the time of the patenting treatment, and the wire-drawing workability deteriorates, which causes the breakage during the wire-drawing working. Therefore, the amount of C content is specified to be in the range of 0.7-1.2%.
  • Si is an element effective in strengthening the ferrite phase in the pearlite, and in deoxidizing the steel. The effects described above cannot be expected when the amount of Si content is less than 0.05% . On the other hand, when the amount of Si exceeds 2%, hard SiO 2 -based inclusions likely occur, which are harmful to the wire-drawing workability. Therefore, the amount of Si content is specified to be in the range of 0.05-2.0%.
  • Mn is an element not only necessary for deoxidation and desulfurization, but also effective in improving hardenability of the steel and increasing the tensile strength after the patenting treatment.
  • the effect described above cannot be obtained when the amount of Mn content is less than 0.2%.
  • the amount of Mn content exceeds 2.0%, the effect described above saturates, and the treatment time for completing the pearlite transformation during the patenting treatment becomes longer, which reduces productivity. Therefore, the amount of Mn content is specified to be in the range of 0.2-2.0%.
  • the steel wire according to the embodiment of the present invention may further include one or more elements of Cr, Ni, V, Nb, Mo, and B for the following reasons.
  • Cr makes distances between the cementite phases in the pearlite finer, increases the tensile strength after the patenting treatment, and improves the hardening rate of the wire at the time of the wire-drawing working.
  • the operation described above has only a smaller effect when the amount of Cr content is less than 0.05%.
  • the amount of Cr content exceeds 1.0%, the time for completing the pearlite transformation at the time of the patenting treatment becomes longer, which deteriorates productivity. For this reason, it is preferable that the amount of Cr content be specified to be in the range of 0.05-1.0%.
  • Ni has an effect that makes the pearlite generated through transformation at the time of the patenting treatment favorable for the wire-drawing workability.
  • the effect cannot be obtained when the amount of Ni content is less than 0.05%, and the effect commensurate with the added amount cannot be obtained when the amount of Ni content exceeds 1.0%.
  • the amount of Ni content be specified to be in the range of 0.05-1.0%.
  • V has an effect that makes the distance between the cementite phases in the pearlite finer and increases the tensile strength at the time of the patenting treatment. This effect is not sufficient when the amount of V content is less than 0.01%, and the effect saturates when the amount of V content exceeds 0.5%. For this reason, it is preferable that the amount of V content be specified to be in the range of 0.01-0.5%.
  • Nb Similar to V, Nb has an effect that makes the distance between the cementite phases in the pearlite finer and increases the tensile strength at the time of patenting treatment. This effect is not sufficient when the amount of Nb content is less than 0.001%, and the effect saturates when the amount of Nb content exceeds 0.1%. For this reason, it is preferable that the amount of Nb content be specified to be in the range of 0.001-0.1%.
  • Mo Similar to V, Mo has an effect that makes the distance between the cementite phases finer, and increases the tensile strength at the time of the patenting treatment. This effect is not sufficient when the amount of Mo content is less than 0.01%, and the effect saturates when the amount of Mo content exceeds 0.1%. For this reason, it is preferable that the amount of Mo content be specified to be in the range of 0.01-0.1%.
  • B has a function and effect of being bound to N to become BN, and prevents deterioration through aging due to N, and it is necessary that the steel contain 0.0001% or more of B in order to sufficiently utilize this effect.
  • the amount of B content exceeds 0.01%, the effect saturates, and adding B exceeding this value is not preferable as it causes the increase in manufacturing cost.
  • the amount of B content be specified to be in the range of 0.0001-0.01%.
  • preferable ranges of elements contained as inevitable impurities are P: 0.015% or lower, S: 0.015% or lower, and N: 0.007% or lower.
  • P 0.015% or lower
  • S 0.015% or lower
  • N 0.007% or lower.
  • a skin pass process is inserted one time, preferably plural times.
  • the skin-pass wire drawing which is one of the important processes, is a method for drawing the wire under an area reduction rate especially smaller than that of the ordinary wire drawing (10% or more). It is preferable for the area reduction rate to be in the range of 1% to 6%, and more preferably, in the range of 2% to 5%. It is difficult to apply the working to the entire surface of the steel wire when the area reduction rate is less than 1%. When the area reduction rate exceeds 7%, the amount of working is too great, which makes it impossible to obtain the preferable residual compressive stress in the surface and carbon concentration in the ferrite phase.
  • the skin-pass wire drawing may be made independently using a single-die type or made using a double-dies type simultaneously with the ordinary wire drawing.
  • the compressive residual stress can be applied to the surface of the steel wire, and at the same time, the lamella structure on the surface can be made further uniform by performing the skin pass process with the area reduction rate of 1%-6% one time, preferably, plural times in the final step.
  • the amount of locally solid-solved carbon can be easily reduced, and decomposition of the cementite in the outermost layer can be suppressed.
  • A2 Shot peening is performed after the wire drawing.
  • the shot peening is a method of manufacturing a worked layer or strain layer only in the surface region of the steel wire by discharging the spherical shot having a specific size to the entire steel wire under a specific press and for a specific time.
  • the shot peening is performed, for example, such that the air blasting type is used; air pressure is 4-5 ⁇ 10 5 Pa; a period of time is 5-10 seconds; and the size of the shot ball is 10-100 ⁇ m. It is effective to perform sufficient amount of discharge to the entire surface of the steel wire.
  • the compressive residual stress is applied to the surface of the steel wire, and the lamella structure on the surface is made further uniform by performing the shot peening after the wire-drawing working.
  • a wire-drawing speed is set at a low wire-drawing speed of 200 m/min or lower, preferably, 50 m/min or lower.
  • the amount of heat generated during the drawing working due to friction or plastic deformation can be made smaller. This makes it possible to suppress the decomposition of the cementite in the pearlite structure, whereby the amount of carbon diffused in the ferrite phase can be reduced.
  • the die having the small approach angle and small dynamic friction coefficient By employing the die having the small approach angle and small dynamic friction coefficient, the generated heat due to the friction during the wire-drawing working can be suppressed, and an increase in C concentration in the ferrite phase caused by the decomposition of the cementite due to the temperature rise in the outermost layer can be suppressed. This process is effective when employed in the step close to the final step.
  • heating at a temperature of 60-300°C is held for 0.1 minute to 24 hours, more preferably, heating at a temperature of 180-260°C is held for 20 seconds to 15 minutes.
  • the supersaturated carbon dissolved in the ferrite phase due to the decomposition of the cementite during the wire-drawing working is discharged from the ferrite phase, and the carbon concentration in the ferrite phase is decreased.
  • the temperature is too high, the spherical cementite or transition carbide is formed, and on the other hand, when the temperature is too low, the effect is small. It is necessary to set the appropriate temperatures according to types of steel materials, and conditions for wire drawing.
  • the strain of the wire can be introduced uniformly into the wire, and does not exist unbalancedly in the surface. This is effective when performed before the final three steps.
  • the C concentration in the ferrite phase of the steel wire can be accurately measured by the three-dimensional atom probe technique (3DAP).
  • 3DAP three-dimensional atom probe technique
  • the C concentration of the ferrite phase in the pearlite structure of the drawn wire in the outermost layer of the steel wire was not able to be measured.
  • FIB focused ion beam
  • the C concentration in the form of a solid solution may take different values according to the positions in the ferrite phase, and hence attention should be paid to it.
  • the C concentration is high at an interfacial position between the ferrite phase and the cementite phase, and is minimum at the center of the ferrite phase.
  • the average C concentration is defined in the region (region of half of the ferrite phase width) from the center plane of the ferrite phase to a portion located at one-fourth of a width of the ferrite phase toward both ends thereof.
  • the C concentration in the ferrite phase including the interface between the ferrite phase and the cementite phase can be measured.
  • the obtained value can be converted into mass% by multiplying by 12/56.
  • the measurement described above is performed on plural portions in the center portion of the ferrite phase to obtain the average value, and the thus obtained value is defined as the average C concentration at the center portion in the ferrite phase.
  • FIG. 2A through FIG. 2F show a method of preparing a needle specimen for measuring the C concentration at the center portion of the ferrite phase located at a position 1 ⁇ m below the surface of the steel wire
  • FIG. 3 shows the C distribution measured by the 3DAP and the C concentration at the center portion of the ferrite phase using the prepared needle specimen.
  • FIG. 2A To prepare the needle specimen of the region 1 ⁇ m inside from the surface of the steel wire, for example, a rod-like block having the surface of the steel wire on one side thereof is cut out from the surface region of the steel wire using the FIB, as shown in FIG. 2A .
  • This block is fixed on a needle mount as shown in FIG. 2B through vapor deposition (deposition) using, for example, tungsten.
  • This fixed block is processed using FIB so as to have a thin top end position as shown in FIG. 2C .
  • FIG. 2D is a diagram showing the processed block as viewed from above, and from FIG. 2D , it can be understood that the top end portion is the rod-like block having the surface of the steel wire.
  • FIG. 2F is a diagram showing the thus prepared needle specimen as viewed from the side.
  • the needle top end is prepared such that the position thereof corresponds to 1 ⁇ m inside from the surface of the steel wire.
  • the needle specimen in the outermost layer of the steel wire can be prepared.
  • a thick-colored portion indicates that the C concentration is high, and a thin-colored portion indicates that the C concentration is low. Therefore, the thick-colored band-like regions indicate the cementite phase having been subjected to the wire-drawing working, and the thin-colored region between the thick-colored band-like regions indicates the ferrite phase having been subjected to the wire-drawing working.
  • FIG. 3 shows that C is solid-solved in the ferrite phase.
  • the carbon concentration at the center portion of the ferrite phase can be estimated such that the box is cut out from the center of the ferrite phase as shown in FIG. 3 , and the number of C atoms contained in the box is divided by the total number of atoms. In this example, the C concentration is 0.18 mass%.
  • the center portion of the ferrite phase is located at the midway point between two cementite phases, and corresponds to the region (region of half of the ferrite phase width) from the center plane of the ferrite phase to a portion located at one-fourth of a width of the ferrite phase toward both ends thereof.
  • the width of the ferrite phase is not necessarily constant and depends on the amount of working or position in the specimen, and there exists a region having a width as narrow as 10 nm or lower. If the box contains the cementite region, the resulting value may be higher than the actual C concentration in the ferrite phase. For this reason, the box position to be analyzed is set at the center portion of the ferrite phase, and the box width is half of the width of the ferrite phase. Further, the average C concentration is an average of five or more, preferably, ten or more different values of the C concentration measured at the center portion of the ferrite phase.
  • the residual stress in the outermost layer of the steel wire can be measured accurately, for example, using the X-ray diffraction method.
  • the measurement can be made accurately, in particular, through debye-ring fitting method using the micro-region X-ray diffractometer that can measure the local region. This method is performed by a fitting operation using the reflection of the crystal grain of the steel wire as the debye ring, and investigating the size and orientation of the residual stress on the basis of distortion of the debye ring.
  • the depth-region including the surface is determined from the depth of penetration of X-rays. For example, when Cr is used as the X-ray source, the integrated value of several ⁇ m depth below the surface is obtained.
  • Another method of investigating the residual stress at the surface of the steel wire is a method of dissolving as needed (Heyn method).
  • Heyn method is a method for measuring the difference in length of the steel wire before and after the outermost layer to be investigated is dissolved, and investigating the residual stress in the longitudinal direction of the steel wire.
  • a high-strength ultrathin steel wire with brass plate having the wire diameter of 0.04-0.40 mm and having a pearlite structure was prepared such that a sample material having chemical components shown in Table 1 is processed to be a predetermined wire diameter through hot rolling; then patenting treatment is applied using a lead bath; and, the wire-drawing working are performed to make the wire have the tensile strength of 4500 MPa or more.
  • the brass plating was performed after the final patenting treatment was performed and the acid cleaning was performed.
  • Table 2 shows: the real strain of the ultrathin steel wire at the time of wire-drawing working; manufacturing method; wire diameter; average C concentration at the center portion of the ferrite phase in the outermost layer of the steel wire; residual stress in the outermost layer of the steel wire; tensile strength; and, twisting number until break at the time of twisting test.
  • the manufacturing method is represented by characters indicating contents described above.
  • the twisting test the test specimen was fixed at a holding interval 100 times larger than the wire diameter at both ends of the test specimen, and the number of twistings until breakage was investigated.
  • the evaluation was made such that the ductility is favorable when the tensile strength is 4500 MPa or more and the twisting number is 20 or more, and the ductility is extremely favorable when the twisting number is 25 or more.
  • the C concentration in the ferrite phase in the outermost layer of the steel wire was measured at a position 1 ⁇ m below the surface of the steel wire by the method described above using the 3DAP.
  • the residual stress in the outermost layer of the steel wire in the longitudinal direction of the steel wire was measured using the debye-ring fitting method described above. The compressive stress is indicated when the residual stress is negative, and the tensile stress is indicated when the residual stress is positive.
  • test Nos. 1-6 are the present invention examples, and the other test examples are comparative examples. As shown in Table 2, all the present invention examples exhibit the tensile strength of 4500 MPa or more, the average C concentration at the center portion of the ferrite phase in the outermost layer of 0.2 mass% or lower, and the residual stress of -600MPa or lower (residual compressive stress of 600 MPa or more). As a result, the ultrathin steel wire having the large twisting number and sufficient ductility can be realized. In particular, test Nos. 1-2 exhibit the twisting number of 25 or more, and are extremely favorable.
  • test Nos. 7-20 are comparative examples, and exhibit the tensile strength of 4500 MPa or more but an insufficient twisting number.
  • Nos. 7-9 are comparative examples whose components in the steel wire are outside the range according to the present invention. As for No. 7, as the C concentration of the steel wire is too low or the amount of strain of the steel wire is made higher, the C concentration at the center portion of the ferrite phase becomes the specified value or more, which results in the decrease in ductility.
  • No. 8 and No. 9 are comparative examples, in which the amount of Si in the steel wire and the amount of of C in the steel wire are higher than the range according to the present invention, respectively. In those comparative examples, although the residual stress and the C concentration at the center portion of the ferrite phase are within the specified range, the ductility deteriorates.
  • Nos. 10-13 are comparative examples, in which components in the steel wire and the residual stress are within the range according to the present invention, but the C concentration is the specified value or more. In these comparative examples, the ductility deteriorates.
  • Nos. 14-16 are comparative examples, in which components in the steel wire and the C concentration at the center portion of the ferrite phase are within the range according to the present invention, but the residual stress is outside the range. In these comparative examples, the ductility deteriorates.
  • Nos. 17-20 are comparative examples, in which the C concentration at the center portion of the ferrite phase in the outermost layer and the residual stress are outside the range. In these comparative examples, the ductility deteriorates.

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Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008069409A (ja) * 2006-09-14 2008-03-27 Bridgestone Corp 高強度高炭素鋼線およびその製造方法
KR101316198B1 (ko) * 2011-11-15 2013-10-08 주식회사 포스코 고연성 선재, 강재 및 그 제조방법
CN102965546A (zh) * 2012-11-20 2013-03-13 无锡康柏斯机械科技有限公司 一种帘线机
DK2993246T3 (da) * 2013-04-30 2019-05-13 Nippon Steel & Sumitomo Metal Corp Flad stålwire
CN105960477B (zh) * 2014-02-06 2018-11-06 新日铁住金株式会社 钢线
CN105960478B (zh) 2014-02-06 2018-10-09 新日铁住金株式会社 单丝
JP6229792B2 (ja) * 2014-04-24 2017-11-15 新日鐵住金株式会社 高強度スチールコード用線材
EP3144404A4 (en) * 2014-04-24 2018-01-17 Nippon Steel & Sumitomo Metal Corporation Filament for high strength steel cord
WO2016024635A1 (ja) * 2014-08-15 2016-02-18 新日鐵住金株式会社 伸線加工用鋼線
CN105063508B (zh) * 2015-08-26 2017-01-18 武汉钢铁(集团)公司 含硼高端帘线钢及其生产方法
CN108138285B (zh) * 2015-10-23 2020-02-21 日本制铁株式会社 拉丝加工用钢丝材
JP6724400B2 (ja) * 2016-02-10 2020-07-15 日本製鉄株式会社 強度と延性のバランスに優れた高強度極細鋼線及びその製造方法
KR101830537B1 (ko) 2016-11-07 2018-02-20 주식회사 포스코 피로 저항성이 우수한 고강도 강선 및 이의 제조방법
JP6520985B2 (ja) * 2017-05-02 2019-05-29 横浜ゴム株式会社 ビードリング及びその製造方法
WO2018212327A1 (ja) * 2017-05-18 2018-11-22 新日鐵住金株式会社 線材、鋼線、及び鋼線の製造方法
CN109811565A (zh) * 2017-11-21 2019-05-28 江苏法尔胜技术开发中心有限公司 压实喷丸面股耐磨钢丝绳及其生产方法
CN110238235A (zh) * 2019-06-11 2019-09-17 安徽环新集团有限公司 用于汽车发动机的卡簧线材生产线及生产方法
CN112223569A (zh) * 2020-09-28 2021-01-15 王佩 一种耐磨线切割复合线材及其制备方法
CN113699438B (zh) * 2021-07-20 2022-07-08 武汉钢铁有限公司 一种86级低成本帘线钢及其制备工艺
CN113913681B (zh) * 2021-08-26 2022-03-25 武汉钢铁有限公司 一种高强度低断丝率的帘线钢、轧制方法及其用途
JP7436964B1 (ja) 2022-07-29 2024-02-22 住友電気工業株式会社 鋼線、及び鋼線の製造方法

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS60204865A (ja) 1984-03-28 1985-10-16 Kobe Steel Ltd 高強度で高靭延性の極細線用高炭素鋼線材
JPS6324046A (ja) 1986-07-16 1988-02-01 Kobe Steel Ltd 高靭性高延性極細線用線材
JPH0323674A (ja) 1989-06-21 1991-01-31 Mitsubishi Electric Corp 半導体装置
JPH06145895A (ja) 1992-10-30 1994-05-27 Kobe Steel Ltd 高強度高靭性鋼線材、該鋼線材を用いた極細鋼線およびその製法並びに撚り鋼線
JPH07113119A (ja) 1993-10-15 1995-05-02 Kobe Steel Ltd 高強度高靭延性極細鋼線の製法
JPH08232046A (ja) * 1995-02-23 1996-09-10 Nippon Steel Corp 耐捻回割れ性に優れた高強度鋼線
JPH11199979A (ja) * 1998-01-16 1999-07-27 Nippon Steel Corp 疲労特性の優れた高強度極細鋼線およびその製造方法
JP3814070B2 (ja) * 1998-01-20 2006-08-23 新日本製鐵株式会社 高強度極細鋼線およびその製造方法
WO2000049186A1 (fr) * 1999-02-19 2000-08-24 Suncall Corporation Ressort presentant d'excellentes caracteristiques de resistance a la fatigue et procede de traitement de surface destine a sa fabrication
JP4464511B2 (ja) 2000-02-08 2010-05-19 新日本製鐵株式会社 延性及び疲労特性の優れた高強度極細鋼線の製造方法
JP2001279381A (ja) * 2000-03-29 2001-10-10 Kobe Steel Ltd 耐縦割れ性に優れた高強度高靭性極細鋼線及びその製造方法
JP2001279380A (ja) * 2000-03-29 2001-10-10 Sumitomo Electric Ind Ltd 高靭性鋼線およびその製造方法
US6949149B2 (en) * 2002-12-18 2005-09-27 The Goodyear Tire & Rubber Company High strength, high carbon steel wire
JP3777166B2 (ja) 2003-03-31 2006-05-24 新日本製鐵株式会社 高強度極細鋼線の製造方法
JP4555711B2 (ja) * 2005-03-14 2010-10-06 新日本製鐵株式会社 延性に優れた高強度極細鋼線
JP4593504B2 (ja) 2006-03-28 2010-12-08 新日本製鐵株式会社 延性に優れた高強度極細鋼線
JP4980172B2 (ja) 2007-01-30 2012-07-18 新日本製鐵株式会社 強度延性バランスに優れた高強度極細鋼線の製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

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KR101260598B1 (ko) 2013-05-03
EP2447382A1 (en) 2012-05-02
TW201102443A (en) 2011-01-16
CN102066599B (zh) 2013-11-06
CN102066599A (zh) 2011-05-18
EP2447382A4 (en) 2017-08-02
US20110168302A1 (en) 2011-07-14
TWI412608B (zh) 2013-10-21

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