WO2018021574A1 - Fil d'acier à haute résistance - Google Patents

Fil d'acier à haute résistance Download PDF

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Publication number
WO2018021574A1
WO2018021574A1 PCT/JP2017/027578 JP2017027578W WO2018021574A1 WO 2018021574 A1 WO2018021574 A1 WO 2018021574A1 JP 2017027578 W JP2017027578 W JP 2017027578W WO 2018021574 A1 WO2018021574 A1 WO 2018021574A1
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Prior art keywords
steel wire
pearlite
aspect ratio
wire
surface layer
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PCT/JP2017/027578
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English (en)
Japanese (ja)
Inventor
真 小此木
直樹 松井
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新日鐵住金株式会社
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Application filed by 新日鐵住金株式会社 filed Critical 新日鐵住金株式会社
Priority to CN201780043855.4A priority Critical patent/CN109563577A/zh
Priority to US16/320,459 priority patent/US20200354810A1/en
Priority to MYPI2019000401A priority patent/MY197958A/en
Priority to BR112019000924-8A priority patent/BR112019000924A2/pt
Priority to KR1020197002093A priority patent/KR20190021379A/ko
Priority to JP2018530444A priority patent/JP6893212B2/ja
Priority to EP17834575.7A priority patent/EP3492616A4/fr
Priority to CA3031185A priority patent/CA3031185A1/fr
Priority to MX2019000974A priority patent/MX2019000974A/es
Publication of WO2018021574A1 publication Critical patent/WO2018021574A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • 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
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C21—METALLURGY OF IRON
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • This disclosure relates to high-strength steel wires.
  • Steel wires are applied to civil engineering and building structures such as rope wires and bridge wires.
  • the wire for a rope and the wire for a bridge are manufactured using, for example, a steel wire that has been subjected to a wire drawing process after a piano wire is patented to a pearlite structure and then subjected to an aging treatment.
  • Patent Document 1 proposes a high-strength steel wire in which the average aspect ratio of plate-like cementite in pearlite is 30 or less in a region having a depth of at least 1 / 10d (d is the radius of the steel wire) of the steel wire surface layer. ing.
  • Patent Document 2 proposes a high-strength steel wire in which the hardness of the region 0.1D from the surface is 1.1 times the internal hardness or less when the wire diameter of the steel wire is D. Yes.
  • Patent Document 1 Japanese Patent Application Laid-Open No. 2004-360005
  • Patent Document 2 Japanese Patent Application Laid-Open No. 2009-280836
  • This disclosure is intended to provide a high-strength steel wire having high strength and excellent hydrogen embrittlement resistance.
  • Means for solving the above problems include the following aspects. (1) By mass%, C: 0.70 to 1.20%, Si: 0.10 to 2.00%, Mn: 0.20 to 1.00%, P: 0.030% or less, S: 0.030% or less, N: 0.0010 to 0.0100%, Al: 0 to 0.100%, Cr: 0 to 2.00%, V: 0 to 0.30%, B: 0 to 0.0.
  • Ti 0 to 0.050%, Nb: 0 to 0.050%, Zr: 0 to 0.050%, Ni: 0 to 2.00%, Cu: 0 to 1.00%, Sn: It has a chemical composition consisting of 0 to 0.50%, Mg: 0 to 0.010%, Ca: 0 to 0.010%, and the balance: Fe and impurities, and the metal structure is 95% or more in area ratio
  • the average aspect ratio R of the pearlite block measured at the surface layer in the cross section in the axial direction including the axis of the steel wire is 2.0 or more.
  • a high-strength steel wire having high strength and excellent hydrogen embrittlement resistance is provided.
  • the metal structure of the steel wire is a pearlite structure, and the pearlite block is in the axial direction of the steel wire (the steel wire It is effective to make the tissue elongated along the longitudinal direction.
  • the pearlite structure has a layered structure of cementite phase and ferrite phase. This layered structure provides hydrogen penetration resistance (hydrogen embrittlement resistance) against crack propagation.
  • the orientation of the layered structure of the pearlite structure becomes uniform, so that the deterioration of the hydrogen embrittlement resistance is suppressed.
  • the metal structure can have excellent hydrogen embrittlement resistance even if the strength of the steel wire is 1800 MPa or more.
  • the metal structure is a pearlite structure having an area ratio of 95% or more.
  • shaft of a steel wire is 2.0 or more.
  • the diameter of the steel wire is D, (average aspect ratio of the pearlite block measured at the surface layer) / (average of the pearlite block measured at the position of 0.25D in the axial section including the axis of the steel wire) (Aspect ratio) is 1.1 or more. Therefore, the high-strength steel wire of the present disclosure is a steel wire that has high strength and excellent hydrogen embrittlement resistance. For example, it is used for rope wires and bridge wires used in civil engineering and building structures. Useful for.
  • FIG. 2 is a schematic diagram showing an axial cross section including the axis of the steel wire.
  • S represents the surface layer
  • Q represents the central axis
  • D represents the diameter of the steel wire.
  • shaft of a steel wire represents the surface cut
  • the “surface layer” indicates a region having a depth of up to 100 ⁇ m from the surface of the steel wire toward the central axis (in the radial direction).
  • “0.25D” means that when the diameter of the steel wire is D, from the surface of the steel wire toward the central axis (in the radial direction), 0.25 times the diameter D Indicates the position of the depth.
  • FIG. 1 is a schematic view showing a cross section orthogonal to the axial direction of the steel wire.
  • S represents the surface layer
  • D represents the diameter of the steel wire
  • 0.25D represents the position of 0.25D. As shown in FIG.
  • the surface layer S is a region having a depth of up to 100 ⁇ m from the surface of the steel wire toward the central axis.
  • 0.25D is a position having a depth of 0.25 times the diameter D from the surface of the steel wire toward the central axis.
  • a numerical range expressed using “to” means a range including numerical values described before and after “to” as a lower limit value and an upper limit value.
  • a numerical range in which “exceeding” or “less than” is added to the numerical values described before and after “to” means a range not including these numerical values as the lower limit value or the upper limit value.
  • “%” indicating the content of a component (element) means “% by mass”.
  • the content of C (carbon) is sometimes referred to as “C amount”.
  • the content of other elements may be expressed in the same manner.
  • the term “process” is not limited to an independent process, and is used in this term if the intended purpose of the process is achieved even when it cannot be clearly distinguished from other processes. included.
  • the chemical composition of the high-strength steel wire of the present disclosure is, in mass%, C: 0.70 to 1.20%, Si: 0.10 to 2.00%, Mn: 0.20 to 1.00%, P : 0.030% or less, S: 0.030% or less, N: 0.0010-0.0100%, Al: 0-0.100%, Cr: 0-2.00%, V: 0-0.
  • B 0 to 0.0050%, Ti: 0 to 0.050%, Nb: 0 to 0.050%, Zr: 0 to 0.050%, Ni: 0 to 2.00%, Cu: It has a chemical composition comprising 0 to 1.00%, Sn: 0 to 0.50%, Mg: 0 to 0.010%, Ca: 0 to 0.010%, and the balance: Fe and impurities.
  • the C content is set to 0.70 to 1.20%.
  • a preferable range of the C content is 0.80 to 1.15%, and a more preferable range is 0.90 to 1.10%.
  • ⁇ Si has the effect of enhancing relaxation properties and increasing tensile strength by solid solution strengthening. If the Si amount is less than 0.10%, these effects are insufficient. On the other hand, if the amount of Si exceeds 2.00%, these effects are saturated and hot ductility deteriorates, resulting in a decrease in manufacturability. Therefore, the Si amount is set to 0.10 to 2.00%. A preferable range of the Si amount is 0.20 to 1.80%, and a more preferable range is 0.50 to 1.50%.
  • Mn has the effect of increasing the tensile strength of steel after pearlite transformation. If the amount of Mn is less than 0.20%, the effect is insufficient. On the other hand, when the amount of Mn exceeds 1.00%, the above effect is saturated. Therefore, the amount of Mn is set to 0.20 to 1.00%. A preferable range of the amount of Mn is 0.30 to 0.90%, and a more preferable range is 0.40 to 0.80%.
  • P and S are contained as impurities. Since P and S are segregated at the grain boundaries and deteriorate the hydrogen embrittlement resistance, it is better to suppress the amounts of P and S. Therefore, the upper limits of the P amount and the S amount are each 0.030%.
  • the preferable ranges of the P amount and the S amount are each 0.020% or less, and the more preferable range is 0.015% or less.
  • the lower limit values of the P amount and the S amount are not particularly limited, but may be over 0%, for example, 0.0001% or more from the viewpoint of reducing dephosphorization cost and desulfurization cost.
  • the N amount is set to 0.0100% or less.
  • N has an effect of improving relaxation characteristics.
  • N also has the effect of forming nitrides with Al, Ti, Nb, and V, thereby reducing the crystal grain size and improving ductility. If the N content is less than 0.0010%, it is difficult to obtain these effects. Therefore, the N amount is set to 0.0010 to 0.0100%.
  • the N amount is preferably 0.0010 to 0.0080%, more preferably 0.0010 to 0.0050%.
  • the high-strength steel wire of the present disclosure may contain one or more of each element of Al, Cr, V, B, Ti, Nb, Zr, and Ni.
  • Al 0.005-0.100%
  • Cr 0.01-2.00%
  • V 0.01-0. 30%
  • B 0.0001 to 0.0050%
  • Ti 0.001 to 0.050%
  • Nb 0.001 to 0.050%
  • Zr 0.001 to 0.050%
  • Ni One or two or more of 0.01 to 2.00% may be contained.
  • Al is an arbitrary element. Therefore, the Al amount may be 0%. Al functions as a deoxidizing element. Moreover, Al has the effect of forming AlN to refine crystal grains and improving ductility, and the effect of reducing solid solution N and improving hydrogen embrittlement resistance. In this regard, the Al content may be greater than 0%. In order to obtain this effect sufficiently, the Al content is preferably 0.005% or more. Further, the Al content is preferably more than 0.005%, preferably 0.008% or more, preferably 0.010% or more, and preferably 0.020% or more. On the other hand, if the Al content exceeds 0.100%, the above effects are saturated and the productivity may be lowered. Therefore, the Al content is preferably 0.100% or less, and is preferably 0.060 or less. Therefore, when Al is contained, the Al amount is preferably 0.005 to 0.100%, more preferably more than 0.005 to 0.100%, and 0.008 to 0.060%. Also good.
  • the Cr amount may be 0%.
  • Cr has the effect of increasing the tensile strength of steel after pearlite transformation.
  • the Cr content may be greater than 0%.
  • the Cr content is preferably 0.01% or more.
  • the Cr content in the case of containing Cr is preferably 0.01 to 2.00%. A preferred range is 0.10 to 0.50%.
  • V is an arbitrary element. Therefore, the V amount may be 0%. V precipitates the carbide VC to increase the tensile strength and improve the hydrogen embrittlement resistance. In this respect, the V amount may be more than 0%. In order to obtain this effect sufficiently, the V content is preferably 0.01% or more. On the other hand, if the amount of V exceeds 0.30%, the alloy cost increases. Therefore, the amount of V when V is included is preferably 0.01 to 0.30%. A preferred range is 0.02 to 0.10%.
  • the B amount may be 0%.
  • B has the effect of increasing the tensile strength after pearlite transformation and the effect of improving the hydrogen embrittlement resistance.
  • the B amount may be more than 0%.
  • the B content is preferably 0.0001% or more.
  • the B content is preferably 0.0001 to 0.0050%.
  • a preferred range is 0.0005 to 0.0020%.
  • Ti is an arbitrary element. Therefore, the Ti amount may be 0%. Ti functions as a deoxidizing element and has the effect of increasing the tensile strength by precipitating carbides and nitrides and the effect of improving the ductility by refining crystal grains. In this respect, the Ti content may be greater than 0%. In order to sufficiently obtain this effect, the Ti content is preferably 0.001% or more. On the other hand, if the amount of Ti exceeds 0.050%, these effects are saturated, and a coarse oxide may be generated to deteriorate the wire drawing workability. Therefore, when Ti is contained, the Ti amount is preferably 0.001 to 0.050%. A preferred range is 0.005 to 0.020%.
  • Nb is an arbitrary element. Therefore, the Nb amount may be 0%. Nb has the effect of increasing the tensile strength by precipitating carbides and nitrides, and the effect of improving the ductility by refining crystal grains. In this respect, the Nb amount may be more than 0%. In order to sufficiently obtain these effects, the Nb content is preferably 0.001% or more. On the other hand, if the Nb amount exceeds 0.050%, the above effects are saturated and the twisting characteristics may be deteriorated. Therefore, the amount of Nb when Nb is included is preferably 0.001 to 0.050%. A preferred range is 0.005 to 0.020%.
  • the Zr amount may be 0%.
  • Zr functions as a deoxidizing element.
  • Zr also has the effect of reducing the solid solution S by forming sulfides and improving the resistance to hydrogen embrittlement.
  • the amount of Zr may be more than 0%.
  • the Zr content is preferably 0.001% or more.
  • the amount of Zr is preferably 0.001 to 0.050%.
  • a preferred range is 0.002 to 0.020%.
  • Ni is an arbitrary element. Therefore, the Ni amount may be 0%. Ni has an effect of suppressing intrusion of hydrogen. In this regard, the Ni content may be greater than 0%. In order to obtain this effect sufficiently, the Ni content is preferably 0.01% or more. On the other hand, when the Ni content exceeds 2.00%, the alloy cost increases. Furthermore, a martensite structure is likely to be generated, and the wire drawing workability and hydrogen embrittlement resistance may be deteriorated. Therefore, when Ni is included, the amount of Ni is preferably 0.01 to 2.00%. A preferred range is 0.05 to 0.50%.
  • each element of Cu, Sn, Mg, and Ca may be 1 type, or 2 or more types of each element of Cu, Sn, Mg, and Ca as an arbitrary component. Therefore, the content of these elements may be 0% by mass.
  • Cu more than 0 to 1.00%
  • Sn more than 0 to 0.50%
  • Mg more than 0 to 0.010%
  • Ca more than 0 to 0.010% It may be.
  • the balance is Fe and impurities.
  • the balance excluding the above-described elements is Fe and impurities.
  • the impurity refers to a component contained in the raw material or a component mixed in the manufacturing process and not intentionally contained in the steel.
  • the impurity include O (oxygen).
  • O is contained as an impurity in the steel and exists as an oxide such as Al or Ti. If the amount of O is high, a coarse oxide is formed, which causes disconnection when wire drawing is performed. For this reason, the O content is preferably suppressed to 0.01% or less.
  • the lower limit of the amount of O is not particularly limited, but may be, for example, over 0% or 0.001% or more.
  • the steel wire having the above components is the above-described specific metal structure. Next, the reason for limiting the metal structure will be described.
  • the lower limit of the area ratio of the pearlite structure was set to 95%.
  • the area ratio of the pearlite structure may be 96% or more.
  • the upper limit of the area ratio of the pearlite structure may be 100% or less, or 99% or less.
  • the region that defines the average aspect ratio R of the pearlite block is a position (surface layer) at a depth of 100 ⁇ m from the surface of the steel wire.
  • the ratio of the average aspect ratio of the pearlite block measured at the surface layer to the average aspect ratio of the pearlite block measured at a position of 0.25D is defined.
  • the pearlite structure has a layered structure of a cementite phase and a ferrite phase. This layered structure provides resistance to hydrogen intrusion from the surface layer (hydrogen embrittlement resistance).
  • the pearlite block on the surface layer of the steel wire extends along the wire drawing direction (longitudinal direction of the steel wire), the direction of the layered structure of the pearlite structure on the surface layer of the steel wire becomes uniform.
  • this average aspect ratio R is 2.0 or more. Preferably it is 2.5 or more, More preferably, it is 3.0 or more.
  • the upper limit of the average aspect ratio R is not particularly limited, but may be 15 or less, 12 or less, or 10 or less in terms of productivity.
  • the ratio of the average aspect ratio of the above formula is small (less than 1.1) (ie, the extension of the surface pearlite block to the internal pearlite block is the same, or When it is small), the strain of the surface layer is the same as that of the internal layer, or the internal layer is subjected to higher strain than the surface layer. Therefore, the surface layer may not be given sufficient strain to the inside.
  • the surface layer is not sufficiently strained and the internal strain is high, the ductility of the steel wire is lowered and cracking is likely to occur, so that the hydrogen embrittlement resistance deteriorates. Therefore, strain is concentrated on the surface layer, and the ratio of the average aspect ratio of the above formula is 1.1 or more.
  • the total area reduction rate in the wire drawing is increased.
  • the ratio of the average aspect ratio of the above formula is less than 1.1, and the ductility of the steel wire and cracking are likely to occur.
  • the ratio of the average aspect ratio represented by the above formula is preferably 1.2 or more, more preferably 1.3 or more, from the viewpoint of further suppressing the deterioration of the hydrogen embrittlement resistance.
  • the upper limit of the ratio of the average aspect ratio is not particularly limited, but may be 5 or less, 3 or less, or 2 or less in terms of productivity.
  • the measurement method of the metal structure was as follows.
  • the area ratio of the pearlite structure of the steel wire was determined by the following procedure. First, a cross section perpendicular to the axis of the steel wire (hereinafter also referred to as “C cross section”) is etched using picral to reveal a metal structure. Next, when the diameter of the steel wire is D, the center structure of the surface layer (the position where the depth from the surface of the steel wire is 50 ⁇ m) and the metal structure at the position where the depth is 0.25D are observed. The observation of the metal structure is performed by taking photographs using SEM at four places rotated at intervals of 90 ° around the axis of the steel wire, one place at the center, and a total of nine places.
  • an area of 120 ⁇ m in the circumferential direction and 90 ⁇ m in the central direction is performed at a magnification of 1000 times.
  • the locations where the area ratio of the pearlite structure of the steel wire is measured are the center positions of the four surface layers S (the positions where the depth from the steel wire surface is 50 ⁇ m), the four 0. There are a total of nine positions, 25D positions and one central part C.
  • the non-pearlite structure (ferrite, bainite, martensite, and pro-eutectoid cementite structure) in the photographed structure photograph is visually marked, and the area ratio of each structure is obtained by image analysis.
  • the area ratio of the pearlite structure is determined by subtracting the area of the non-pearlite structure from the entire observation field. This is measured about two samples, the average value thereof is obtained, and the pearlite area ratio of the entire steel wire is obtained.
  • the average aspect ratio of the pearlite block on the surface layer was determined by the following procedure.
  • a pearlite block grain boundary is detected using an EBSD (Electron Back Scattering Diffraction Pattern) device for an axial cross section (hereinafter also referred to as an L cross section) including the axis of the steel wire.
  • EBSD Electro Back Scattering Diffraction Pattern
  • the measurement step is set to 0.3 ⁇ m and bcc at each measurement point. Measure the crystal orientation of -Fe and determine the boundary where the orientation difference is 9 degrees or more.
  • a region surrounded by the boundary is defined as a pearlite block grain.
  • 20 pearlite blocks are selected from the pearlite block group in the measurement region in order from the largest circle equivalent diameter.
  • the aspect ratio of each of the 20 selected pearlite blocks (the ratio of the major axis to the minor axis of the pearlite block, that is, the major axis / minor axis) is obtained, and the average value of the aspect ratios of the twenty pearlite blocks is obtained.
  • the pearlite block was investigated for 2 samples on both sides per L cross section and all 4 samples taken from different parts of the steel wire, and the average value of the average aspect ratio of all 8 locations was the average of the pearlite block in the surface layer. Aspect ratio.
  • the portion where the aspect ratio is measured is a region of the surface layer S that is 100 ⁇ m from the surface in the central axis direction of the steel wire and 500 ⁇ m in the longitudinal direction of the steel wire. Further, at 0.25D, 100 ⁇ m in the central axis direction centered on the position of the depth of 0.25D (from 0.25D to 50 ⁇ m in the surface direction centered on the position of the depth of 0.25D, and 0. 25D to 50 ⁇ m in the central axis direction) and a 500 ⁇ m region in the longitudinal direction of the steel wire. As shown in FIG. 2, the measurement is performed on the surface layer on both sides and 0.25D on both sides with respect to the central axis Q in the L cross section.
  • the tensile strength of the steel wire When the tensile strength of the steel wire is less than 1800 MPa, for example, when applied to civil engineering / building structures, the effects of reduction in construction cost and weight reduction are reduced. Therefore, in the high strength steel wire of the present disclosure, the lower limit of the tensile strength is set to 1800 MPa.
  • the upper limit of tensile strength is not specifically limited, If tensile strength is too high, ductility will fall and a crack may arise when performing a wire drawing process. In this respect, the tensile strength may be 3000 MPa or less, or 2800 MPa or less.
  • the high-strength steel wire of the present disclosure has a steel wire diameter (wire diameter) of 2.5 mm to 9.5 mm from the viewpoint of manufacturing the steel wire having the above-described metal structure and tensile strength and from the viewpoint of the above-described application. It may be 3.0 mm to 9.0 mm, or 3.5 mm to 8.5 mm.
  • the diameter of a steel wire represents the same meaning as the wire diameter of a steel wire.
  • a step of heating a steel slab having a specific chemical composition to 1000 to 1150 ° C. and a step of obtaining a wire by hot rolling the steel slab at a finish rolling temperature of 800 to 950 ° C.
  • pearlite transformation treatment by directly immersing the wire at 800 to 950 ° C. in a molten salt bath at 500 to 600 ° C. for 50 seconds or more, and further water cooling from 400 ° C. to 300 ° C.
  • a step of drawing the wire after the pearlite transformation treatment at a total area reduction of 70 to 95% and a step of aging the drawn wire at 450 ° C. or less.
  • a step of heating a steel slab having a specific chemical composition to 1000 to 1150 ° C. and a step of obtaining a wire by hot rolling the steel slab at a finish rolling temperature of 800 to 950 ° C. Cooling the wire at 800 to 950 ° C., reheating the cooled wire to a temperature range of 950 ° C. or higher, and immersing the reheated wire in a Pb bath or a molten salt bath.
  • Pearlite transformation treatment by holding at 500 to 600 ° C, wire drawing after pearlite transformation treatment with a total area reduction of 70 to 95%, and wire drawing after drawing to 450 ° C or less
  • an aging treatment by holding at 500 to 600 ° C, wire drawing after pearlite transformation treatment with a total area reduction of 70 to 95%, and wire drawing after drawing to 450 ° C or less.
  • the wire drawing is performed as follows. Use a die with an approach half angle of 10 degrees or more (preferably 20 degrees or less) when drawing at least in the final pass in a range where the total area reduction ratio is 70 to 95%, and the area reduction rate is 12% or less. Strength is imparted as (preferably 3% or more and 9% or less). That is, this condition may be adopted not only for the final path but also for a plurality of paths including the final path and the final path.
  • the chemical composition of the steel slab is the same as the chemical composition of the high-strength steel wire described above.
  • the chemical composition of the billet is shown below.
  • the chemical composition of the billet is: C: 0.70 to 1.20%, Si: 0.10 to 2.00%, Mn: 0.20 to 1.00%, P: 0.030% or less, S: 0.030% or less, N: 0.0010 to 0.0100%, Al: 0 to 0.100%, Cr: 0 to 2.00%, V: 0 to 0.30%, B: 0 to 0.0.
  • the above embodiment has been described as an example as a preferable method for producing the high-strength steel wire of the present disclosure. According to the above aspect, a steel wire having high strength and excellent hydrogen embrittlement resistance can be easily produced.
  • Steel types A to L having the chemical composition shown in Table 1 are heated under the conditions shown in Table 2, hot rolled, wound into a ring shape, and molten salt bath at the back of the hot rolling line at the temperature shown in Table 2
  • a wire rod was manufactured by performing a patenting treatment by dipping in a wire. Moreover, about one part, it changed into performing a patenting process by immersing in a molten salt tank, and manufactured the wire by performing blast cooling. Thereafter, the obtained wire was drawn to the wire diameter after drawing as shown in Table 3, heated after aging and subjected to aging treatment, and steel wires shown in Test Nos. 1 to 22 were produced.
  • the wire rod cooled after hot rolling was reheated under the conditions shown in Table 4, and immersed in a Pb bath at the temperature shown in Table 4 to perform a patenting treatment to produce a wire rod. Thereafter, the obtained wire was drawn to the wire diameter after drawing shown in Table 5, heated after aging and subjected to aging treatment, and steel wires shown in Test Nos. 23 to 25 were produced.
  • the area ratio of the metal structure, the average aspect ratio R of the pearlite block measured on the surface layer, and the ratio of the average aspect ratio of the pearlite block measured on the surface layer to the average aspect ratio at the 0.25D position from the surface layer (perlite measured on the surface layer) was obtained as described above.
  • the results are shown in Tables 3 and 5.
  • the hydrogen embrittlement resistance was evaluated by the FIP test. Specifically, the steel wires of test numbers 1 to 25 were immersed in a 20% strength NH 4 SCN solution at 50 ° C., a load that was 0.8 times the breaking load was applied, and the breaking time was evaluated. The specific liquid volume (solution volume / test specimen surface area) was 12 cc / cm 2 . In the FIP test, 12 wires were evaluated for each steel wire, and the average value was defined as the hydrogen embrittlement time. Those having a hydrogen embrittlement time of 10 hours or more were judged to have good hydrogen embrittlement resistance (denoted as G in each table). Further, those not corresponding to the above conditions were judged to have poor hydrogen embrittlement resistance (denoted as NG in each table). The results are shown in Tables 3 and 5.
  • Steel wires with test numbers 1 to 11 and 20 to 25 that satisfy all the requirements of the high strength steel wire of the present disclosure have a tensile strength of 1800 MPa or more and good resistance to hydrogen embrittlement.
  • the steel wire of test number 12 has good resistance to hydrogen embrittlement but has low tensile strength.
  • the area ratio of the pearlite structure, the average aspect ratio R of the pearlite block measured on the surface layer, and the average aspect ratio of the pearlite block measured on the surface layer / Are outside the scope of this disclosure.
  • the average aspect ratio R of the pearlite block measured on the surface layer is less than the lower limit of the present disclosure, and the hydrogen embrittlement resistance is poor.
  • the steel wire of Test No. 14 has an area ratio of the pearlite structure that is less than the lower limit of the present disclosure, and has poor hydrogen embrittlement resistance.
  • the steel wire of Test No. 16 has an area ratio of the pearlite structure and an average aspect ratio R of the pearlite block measured on the surface layer, which is less than the lower limit of the present disclosure, and has poor hydrogen embrittlement resistance.
  • the steel wire of test number 17 has an average aspect ratio R of the pearlite block measured on the surface layer, and an average aspect ratio of the pearlite block measured on the surface layer / (an average aspect ratio of the pearlite block measured at a position of 0.25D). Is less than the lower limit of the present disclosure, and the hydrogen embrittlement resistance is poor.
  • the steel wire of test number 18 has good hydrogen embrittlement resistance, but the tensile strength is less than the lower limit of the present disclosure. Furthermore, the area ratio of the pearlite structure and (average aspect ratio of the pearlite block measured at the surface layer) / (average aspect ratio of the pearlite block measured at the position of 0.25D) are less than the lower limit of the present disclosure.
  • the steel wire of Test No. 19 has (average aspect ratio of pearlite block measured at the surface layer) / (average aspect ratio of pearlite block measured at a position of 0.25D) below the lower limit of the present disclosure, and hydrogen embrittlement resistance The characteristic is bad.

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Abstract

Cette invention concerne un fil d'acier à haute résistance ayant une composition chimique spécifiée, dans lequel : la structure métallique présente au moins 95 % en superficie de structure de perlite ; le rapport d'aspect moyen R des blocs de perlite mesurés dans la couche de surface dans des sections transversales dans la direction axiale qui comprennent l'axe du fil d'acier est d'au moins 2,0 ; lorsque le diamètre du fil d'acier est D, (rapport d'aspect moyen mesuré dans la couche de surface)/(rapport d'aspect moyen mesuré à la position de 0,25 D) dans des sections transversales dans la direction axiale qui comprennent l'axe du fil d'acier est d'au moins 1,1 ; et la résistance à la traction est d'au moins 1800 MPa.
PCT/JP2017/027578 2016-07-29 2017-07-28 Fil d'acier à haute résistance WO2018021574A1 (fr)

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CN201780043855.4A CN109563577A (zh) 2016-07-29 2017-07-28 高强度钢线
US16/320,459 US20200354810A1 (en) 2016-07-29 2017-07-28 High-strength steel wire
MYPI2019000401A MY197958A (en) 2016-07-29 2017-07-28 High strength steel wire
BR112019000924-8A BR112019000924A2 (pt) 2016-07-29 2017-07-28 arame de aço de alta resistência
KR1020197002093A KR20190021379A (ko) 2016-07-29 2017-07-28 고강도 강선
JP2018530444A JP6893212B2 (ja) 2016-07-29 2017-07-28 高強度鋼線
EP17834575.7A EP3492616A4 (fr) 2016-07-29 2017-07-28 Fil d'acier à haute résistance
CA3031185A CA3031185A1 (fr) 2016-07-29 2017-07-28 Fil d'acier a haute resistance
MX2019000974A MX2019000974A (es) 2016-07-29 2017-07-28 Alambre de acero de alta resistencia.

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WO2020256140A1 (fr) 2019-06-19 2020-12-24 日本製鉄株式会社 Fil machine
WO2021255776A1 (fr) * 2020-06-15 2021-12-23 住友電気工業株式会社 Fil d'acier pour un ressort
US11807923B2 (en) 2020-06-17 2023-11-07 Sumitomo Electric Industries, Ltd. Spring steel wire
JP7469642B2 (ja) 2020-05-21 2024-04-17 日本製鉄株式会社 高強度鋼線

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JP5521885B2 (ja) * 2010-08-17 2014-06-18 新日鐵住金株式会社 高強度かつ耐水素脆化特性に優れた機械部品用鋼線、および機械部品とその製造方法
CN114075639A (zh) * 2020-08-20 2022-02-22 宝山钢铁股份有限公司 一种高强度高疲劳寿命缆索用钢、盘条及其制备方法
CN112458356B (zh) * 2020-10-15 2022-02-01 中天钢铁集团有限公司 一种1860MPa级桥梁缆索镀锌钢丝用φ14mm盘条及制备方法

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WO2020256140A1 (fr) 2019-06-19 2020-12-24 日本製鉄株式会社 Fil machine
JP7469642B2 (ja) 2020-05-21 2024-04-17 日本製鉄株式会社 高強度鋼線
WO2021255776A1 (fr) * 2020-06-15 2021-12-23 住友電気工業株式会社 Fil d'acier pour un ressort
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US11892048B2 (en) 2020-06-15 2024-02-06 Sumitomo Electric Industries, Ltd. Spring steel wire
US11807923B2 (en) 2020-06-17 2023-11-07 Sumitomo Electric Industries, Ltd. Spring steel wire

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US20200354810A1 (en) 2020-11-12
EP3492616A1 (fr) 2019-06-05
CN109563577A (zh) 2019-04-02
CA3031185A1 (fr) 2018-02-01
JPWO2018021574A1 (ja) 2019-05-23
MY197958A (en) 2023-07-25
EP3492616A4 (fr) 2020-01-08
MX2019000974A (es) 2019-07-04
KR20190021379A (ko) 2019-03-05
JP6893212B2 (ja) 2021-06-23

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