WO2022259606A1 - Ressort et fil d'acier - Google Patents

Ressort et fil d'acier Download PDF

Info

Publication number
WO2022259606A1
WO2022259606A1 PCT/JP2022/004315 JP2022004315W WO2022259606A1 WO 2022259606 A1 WO2022259606 A1 WO 2022259606A1 JP 2022004315 W JP2022004315 W JP 2022004315W WO 2022259606 A1 WO2022259606 A1 WO 2022259606A1
Authority
WO
WIPO (PCT)
Prior art keywords
mass
steel
steel wire
less
wire
Prior art date
Application number
PCT/JP2022/004315
Other languages
English (en)
Japanese (ja)
Inventor
太一 岡田
隆志 渡邉
貴文 宇和野
和宏 後藤
寛 泉田
Original Assignee
住友電気工業株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority to US17/802,486 priority Critical patent/US20240209481A1/en
Application filed by 住友電気工業株式会社 filed Critical 住友電気工業株式会社
Priority to CN202280002215.XA priority patent/CN115943225A/zh
Priority to JP2022530729A priority patent/JP7173410B1/ja
Priority to KR1020227031927A priority patent/KR20240019005A/ko
Publication of WO2022259606A1 publication Critical patent/WO2022259606A1/fr

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

  • This disclosure relates to steel wires and springs.
  • Patent Document 1 Japanese Patent Application Laid-Open No. 2012-117129
  • the steel wire according to the present disclosure contains 0.5% to 0.7% by weight carbon, 1% to 2.5% by weight silicon, and 0.3% to 1% by weight It is composed of steel containing manganese and 0.5% by mass or more and 2% by mass or less of chromium, with the balance being iron and unavoidable impurities.
  • the wire diameter is 0.5 mm or more and 2 mm or less.
  • Tensile strength is 2000 N/mm 2 or more and 2700 N/mm 2 or less.
  • Steel has a pearlite structure.
  • FIG. 1 is a schematic perspective view showing the structure of a steel wire.
  • FIG. 2 is a schematic cross-sectional view showing the structure in a cross section perpendicular to the longitudinal direction of the steel that constitutes the steel wire.
  • FIG. 3 is a schematic perspective view showing the structure of the spring.
  • FIG. 4 is a flow chart showing an outline of a steel wire and spring manufacturing method.
  • FIG. 5 is a perspective view showing the structure of the raw material wire.
  • FIG. 6 is a diagram showing the relationship between (S+5.8885 ⁇ 10 ⁇ 3 )/T and the twist value.
  • FIG. 7 is a diagram showing the relationship between the ratio of ferrite structure and (S+5.8885 ⁇ 10 ⁇ 3 )/T.
  • the steel wire of the present disclosure contains 0.5% to 0.7% by mass of carbon, 1% to 2.5% by mass of silicon, and 0.3% to 1% by mass of manganese. , 0.5% by mass or more and 2% by mass or less of chromium, and the balance being iron and unavoidable impurities.
  • the wire diameter is 0.5 mm or more and 2 mm or less.
  • Tensile strength is 2000 N/mm 2 or more and 2700 N/mm 2 or less.
  • Steel has a pearlite structure.
  • the "wire diameter” is defined as the circle equivalent diameter of the cross section perpendicular to the longitudinal direction of the steel wire.
  • the equivalent circle diameter means the diameter of a circle when the cross section is circular.
  • the equivalent circle diameter means the diameter of a circle having the same area as the cross-sectional area of the cross-section.
  • the strength of the steel wire can be improved by increasing the workability of the wire rod in the wire drawing process when manufacturing the steel wire.
  • deterioration in toughness occurs due to age hardening.
  • the lattice strain and tensile strength of steel satisfy a specific relationship, deterioration in toughness due to age hardening is less likely to occur, and high strength can be achieved while maintaining toughness. can be done.
  • the value obtained by adding 5.8885 ⁇ 10 -3 to the lattice strain S in steel divided by the tensile strength T (S + 5.8885 ⁇ 10 -3 )/T is 4.8 ⁇ 10 ⁇ 6 or more. Therefore, according to the steel wire of the present disclosure, both high strength and high toughness can be achieved. (S+5.8885 ⁇ 10 ⁇ 3 )/T may be 4.84 ⁇ 10 ⁇ 6 or more. This makes it easy to achieve both high strength and high toughness.
  • the ratio of the ferrite structure in the steel of the steel wire may be 20% or less.
  • the ratio of the ferrite structure is the ratio of the ferrite structure to the sum of the sum of the area of the ferrite structure and the sum of the areas of the pearlite structure in a square area of 200 ⁇ m on a side in the cross section perpendicular to the longitudinal direction of the steel wire. Percentage percentage of total area.
  • the ratio of the ferrite structure may be 15% or less. This makes it easier to ensure sufficient toughness.
  • the steel in the steel wire contains 0.05% by mass or more and 0.5% by mass or less of vanadium, 0.02% by mass or more and 1% by mass or less of cobalt, 0.02% by mass or more and 1% by mass or less of nickel, and 0.02% by mass or more and 1% by mass or less of nickel. It may further contain one or more elements selected from the group consisting of molybdenum in an amount of 05% by mass or more and 0.5% by mass or less.
  • the spring of the present disclosure is composed of the steel wire. According to the spring of the present disclosure, it is possible to provide a spring capable of achieving both high strength and high toughness by being composed of the steel wire of the present disclosure.
  • Carbon 0.5% by Mass or More and 0.7% by Mass or Less Carbon is an element that greatly affects the strength of a steel wire having a pearlitic structure. From the viewpoint of obtaining sufficient strength as a steel wire, the carbon content should be 0.5% by mass or more. When the carbon content increases, the toughness decreases, and the workability during processing into a spring shape or wire drawing decreases. From the viewpoint of ensuring sufficient workability, the carbon content should be 0.7% by mass or less. From the viewpoint of further improving the strength, the carbon content is preferably 0.62% by mass or more. From the viewpoint of improving toughness and facilitating processing, the carbon content is preferably 0.68% by mass or less.
  • Silicon 1% by Mass or More and 2.5% by Mass or Less Silicon is an element necessary as a deoxidizing agent during steel smelting.
  • silicon imparts softening resistance, which is a property of suppressing softening due to heating, to steel.
  • the silicon content must be 1% by mass or more.
  • the silicon content is preferably 1.5% by mass or more, more preferably 1.95% by mass or more. If the silicon content increases, the toughness may decrease. From the viewpoint of ensuring sufficient toughness, the silicon content should be 2.5% by mass or less.
  • Manganese 0.3% by Mass or More and 1% by Mass or Less
  • the content of manganese should be 0.3% by mass or more in order to sufficiently achieve the effect as a deoxidizing agent. In order to achieve the effect as a deoxidizing agent more sufficiently, the content of manganese is preferably 0.5% by mass or more.
  • the manganese content should be 1% by mass or less. From the viewpoint of further reducing the formation of martensite structure, the manganese content is preferably 0.8% by mass or less.
  • Chromium 0.5% by Mass to 2% by Mass Chromium contributes to refinement of the steel structure and suppression of softening during heating. From the viewpoint of sufficiently exhibiting such effects, the content of chromium should be 0.5% by mass or more, preferably 0.7% by mass or more. Excessive addition of chromium causes formation of a martensitic structure during cooling after heating when patenting is performed before the wire drawing process. The martensitic structure generated in this manner reduces workability during wire drawing. Also, excessive addition of chromium causes a decrease in toughness. Therefore, the content of chromium should be 2 mass or less. From the viewpoint of reducing the formation of martensite structure and improving the toughness, the chromium content is preferably 1.5% by mass or less.
  • unavoidable impurities such as phosphorus and sulfur are unavoidably mixed into the steel constituting the steel wire.
  • Phosphorus and sulfur when present in excess, cause grain boundary segregation and formation of inclusions, deteriorating the properties of the steel. Therefore, the content of phosphorus and sulfur is preferably 0.025% by mass or less. Also, the total content of unavoidable impurities, including phosphorus and sulfur, is preferably 0.3% by mass or less.
  • Vanadium 0.05% by Mass or More and 0.5% by Mass or Less Vanadium functions as a carbide-forming element in steel and contributes to suppression of softening during heating by forming carbides. From the viewpoint of sufficiently exhibiting such effects, the vanadium content may be 0.05% by mass or more. Excessive addition of vanadium reduces toughness. From the viewpoint of ensuring sufficient toughness, the amount of vanadium added may be 0.5% by mass or less, or even 0.2% by mass or less.
  • Cobalt 0.02% by Mass or More and 1% by Mass or Less Cobalt contributes to improving the heat resistance of steel and suppressing softening during heating. From the viewpoint of sufficiently exhibiting such effects, the content of cobalt may be 0.02% by mass or more, and may be 0.05% by mass or more. Even if the steel contains more than 1% by mass of cobalt, the above effect of cobalt is saturated. Therefore, the content of cobalt is preferably 1% by mass or less. The content of cobalt may be 0.5% by mass or less from the viewpoint of cost reduction.
  • Nickel 0.02 mass % or more and 1 mass % or less
  • the content of nickel may be 0.02% by mass or more, and may be 0.1% by mass. Even if the steel contains more than 1% by mass of nickel, the above effect of nickel is saturated. Moreover, if the above steel contains more than 1% by mass of nickel, which is an expensive element, the manufacturing cost of the steel wire increases. Therefore, the nickel content is preferably 1% by mass or less. The content of nickel may be 0.5% by mass or less from the viewpoint of cost reduction.
  • Molybdenum 0.05% by Mass or More and 0.5% by Mass or Less Molybdenum functions as a carbide-forming element in steel and contributes to suppression of softening during heating by forming carbides. From the viewpoint of sufficiently exhibiting such effects, the content of molybdenum may be 0.05% by mass or more. From the viewpoint of ensuring sufficient toughness, the molybdenum content may be 0.5% by mass or less, or 0.25% by mass or less.
  • Fig. 1 is a perspective view showing the structure of the steel wire.
  • a cross section perpendicular to the longitudinal direction Y of the steel wire is also illustrated.
  • steel wire 1 in the present embodiment is a steel wire having a circular cross section perpendicular to longitudinal direction Y and a cylindrical outer peripheral surface 11 .
  • a wire diameter D of the steel wire 1 is 0.5 mm or more and 2 mm or less.
  • the cross section of the steel wire 1 perpendicular to the longitudinal direction Y may be other than circular, and may be elliptical, for example.
  • the steel wire 1 contains 0.5% by mass or more and 0.7% by mass or less of carbon, 1% by mass or more and 2.5% by mass or less of silicon, 0.3% by mass or more and 1% by mass or less of manganese, and 0 .5% by mass or more and 2% by mass or less of chromium, the balance being iron and unavoidable impurities.
  • FIG. 2 is a schematic cross-sectional view showing a part of a cross section perpendicular to the longitudinal direction Y of the steel wire 1.
  • a boundary 21A between the pearlite structures 21 and a boundary 22A between the pearlite structure 21 and the ferrite structure 22 are indicated by solid lines.
  • the steel forming steel wire 1 includes pearlite structure 21 and ferrite structure 22 .
  • the ratio of the pearlite structure 21 in the steel forming the steel wire 1 is 80% or more.
  • the ratio of the pearlite structure 21 is preferably 85% or more, more preferably 90% or more.
  • the ratio of ferrite structure 22 in steel constituting steel wire 1 is 20% or less.
  • the ratio of the ferrite structure 22 is preferably 15% or less, more preferably 10% or less. By setting the ratio of the ferrite structure to 20% or less, the homogeneity of the structure of the steel can be improved, and deterioration of toughness due to age hardening can be made difficult to occur. Therefore, it becomes easy to ensure sufficient toughness.
  • the ratio of pearlite structure 21 and ferrite structure 22 is derived, for example, by the following method. First, a sample is taken from the steel wire 1 . Then, a cross section perpendicular to the longitudinal direction Y of the obtained sample is polished. The polished surface is observed, for example, with an electron microscope. By processing the image obtained by this observation with appropriate software, the ratio of pearlite structure 21 and ferrite structure 22 is derived.
  • the tensile strength T of the steel wire 1 is 2000 N/mm 2 or more and 2700 N/mm 2 or less.
  • the lower limit of tensile strength T of steel wire 1 is preferably 2050 N/mm 2 , more preferably 2100 N/mm 2 .
  • the upper limit of tensile strength T of steel wire 1 is preferably 2600 N/mm 2 , more preferably 2500 N/mm 2 .
  • Tensile strength T is measured based on JIS Z 2241, for example.
  • the value obtained by adding 5.8885 ⁇ 10 -3 to S and dividing it by the tensile strength T is (S + 5.8885 ⁇ 10 -3 ) / T is greater than or equal to 4.8 ⁇ 10 ⁇ 6 .
  • S is 0.005
  • the value obtained by adding 5.8885 ⁇ 10 ⁇ 3 to S is 0.0108885 (10.8885 ⁇ 10 ⁇ 3 ).
  • the tensile strength T is 2230 N/mm 2
  • (S+5.8885 ⁇ 10 ⁇ 3 )/T is 4.88 ⁇ 10 ⁇ 6 . Note that the figures below the third decimal place are rounded off.
  • Lattice strain is derived using, for example, the Williamson-Hall method shown in Equation (1) below.
  • S represents the lattice strain
  • ⁇ represents the half-value width (radian) of the diffraction line
  • ⁇ represents the wavelength of the measured X-ray ( ⁇ 10 ⁇ 1 nm)
  • ⁇ represents the Bragg angle of the diffraction line. (radian)
  • ⁇ which is a dimensionless number, represents a constant.
  • FIG. 3 is a perspective view showing the structure of the spring.
  • spring 2 in the present embodiment is composed of steel wire 1. As shown in FIG. 3,
  • FIG. 5 is a perspective view showing the structure of the raw material wire.
  • a cross section perpendicular to the longitudinal direction Y of the raw material wire 5 is also illustrated.
  • S10 contains 0.5% by mass to 0.7% by mass of carbon, 1% by mass to 2.5% by mass of silicon, 0.3% by mass to 1% by mass of manganese, and 0.5% by mass.
  • a raw wire rod 5 is prepared which is composed of steel containing chromium in an amount of 2% by mass or more and the balance being iron and unavoidable impurities.
  • the steel constituting the raw material wire 5 contains 0.05% by mass or more and 0.5% by mass or less of vanadium, 0.02% by mass or more and 1% by mass or less of cobalt, 0.02% by mass or more and 1% by mass or less of nickel, and It may further contain one or more elements selected from the group consisting of molybdenum in an amount of 0.05% by mass or more and 0.5% by mass or less.
  • step S20 the raw material steel wire prepared in step S10 is patented. Specifically, after the raw material steel wire is heated to a temperature range equal to or higher than the temperature at which the steel constituting the steel wire austenites (austenitizing treatment), the temperature is higher than the MS point, which is the temperature at which the steel martensites. A heat treatment is performed in which the material is quenched to a temperature range and held in the temperature range (isothermal transformation treatment). As a result, the metal structure of the raw material steel wire becomes a fine pearlite structure with small lamellar spacing.
  • This step is important for making the value of (S+5.8885 ⁇ 10 ⁇ 3 )/T equal to or greater than 4.8 ⁇ 10 ⁇ 6 .
  • the raw material steel wire is heated to a temperature range of A3 point or higher where the steel becomes an austenite single phase.
  • the austenitizing treatment is preferably carried out just above the A3 point.
  • the austenitizing treatment is preferably performed in a temperature range of A3 point or more and A3 point+20° C. or less.
  • the temperature corresponding to point A3 is, for example, the following formula 910-203 ⁇ [C%] ⁇ 5.2 ⁇ [Ni%]+44.7 ⁇ [Si%]+104 ⁇ [V%]+31.5 ⁇ [Mo %] (°C).
  • [C%], [Ni%], [Si%], [V%] and [Mo%] mean the content (% by mass) of C, Ni, Si, V and Mo, respectively.
  • the austenitizing treatment the raw material steel wire is heated in an inert gas atmosphere from the viewpoint of suppressing the occurrence of decarburization.
  • the isothermal transformation treatment the raw material steel wire is held in a higher temperature range than in the isothermal transformation treatment for a general piano wire or the like.
  • the raw material steel wire is held in a temperature range of 650° C. or higher.
  • the temperature of the isothermal transformation treatment is set to a temperature range higher than that of the isothermal transformation treatment for general piano wires, etc.
  • the lamellar spacing of the obtained pearlite structure becomes slightly larger, but there is a slight presence after the isothermal transformation treatment. It is possible to further reduce the proportion of the ferrite phase in the steel.
  • the value of (S+5.8885 ⁇ 10 ⁇ 3 )/T can be 4.8 ⁇ 10 ⁇ 6 or more.
  • step S30 a wire drawing step is performed as step S30.
  • the raw material steel wire that has been patented in step S20 is drawn.
  • the lower limit of the area reduction rate as the workability of the wire drawing process is 85%.
  • the strength of the steel wire 1 can be improved by setting the area reduction rate to 85% or more.
  • the upper limit of the area reduction rate is 95%.
  • the area reduction rate is the ratio obtained by dividing the difference between V1 and V2 by V1.
  • step S40 a spring processing step for processing into a spring shape is performed as step S40.
  • steel wire 1 is plastically worked into, for example, a helical shape as shown in FIG. 3 to be shaped into a spring.
  • an annealing step is performed as step S50.
  • the steel wire 1 formed into the spring shape at S40 is annealed. Specifically, the strain in the steel wire 1 generated in S40 is reduced by heating the steel wire 1 formed into the shape of the spring.
  • the spring 2 of the present embodiment is completed through the above steps.
  • the lattice strain S and the tensile strength T (unit: N/mm 2 ) of the steel are obtained by adding 5.8885 ⁇ 10 ⁇ 3 to S. (S+5.8885 ⁇ 10 ⁇ 3 )/T, which is the ratio divided by T, is 4.8 ⁇ 10 ⁇ 6 or more. Therefore, according to steel wire 1 and spring 2 of the present embodiment, both high strength and high toughness can be achieved.
  • shot peening may be performed on the steel wire 1 that has been annealed in S50. Shot peening is not an essential step in the method of manufacturing the spring 2 of the present embodiment, but by performing this, a compressive stress is applied to the region including the surface of the spring 2, contributing to improvement in fatigue strength. .
  • the stripping step for removing the decarburized layer in the raw wire rod 5 and the annealing step may be performed before the wire drawing step of S30 is performed.
  • the heating temperature in the annealing step is, for example, 550° C. or higher and 650° C. or lower.
  • the processing time in the annealing step is, for example, 120 minutes or more and 240 minutes or less.
  • the underdrawing step may be performed before the patenting step of S20 is performed. By performing the underdrawing wire drawing process, it becomes easy to adjust the workability in the wire drawing process of S30.
  • a sample of the steel wire 1 of the present disclosure was produced and evaluated to confirm the effect of achieving both high strength and high toughness.
  • the evaluation procedure is as follows.
  • a sample I was produced in the same procedure as the method for producing the steel wire 1 described in the above embodiment.
  • Table 1 shows the chemical composition of the steel in sample I.
  • the holding time (austenitizing treatment) in the temperature range of A3 or higher in the patenting process of sample I was set to 60 seconds.
  • the temperature of isothermal transformation treatment in the patenting process of sample I was set to 650°C.
  • Samples II to VI were produced in the same manner as Sample I, except that the chemical composition of the steel was changed as shown in Table 1.
  • Samples VII to VIII were produced in the same manner as Sample I, except that the chemical composition of the steel was changed as shown in Table 1 and the temperature of the isothermal transformation treatment was set to 600°C.
  • Samples IX and X were produced in the same manner as Sample I, except that the chemical composition of the steel was changed as shown in Table 1, and the austenitizing temperature in the patenting process was set to below the A3 point.
  • the numerical values in Table 1 represent the content of each element in % by mass. Components other than the chemical composition of steel shown in Table 1 are iron and unavoidable impurities.
  • Tensile strength T, lattice strain S, ratio of ferrite structure 22 and torsion value in samples I to X were measured.
  • Tensile strength T, lattice strain S, and ratio of ferrite structure 22 were measured two weeks after samples IX were produced.
  • the lattice strain S was measured as follows.
  • the strain value was calculated by plotting data based on the Williamson-Hall method for the data obtained using X-ray diffraction measurement.
  • monochromatic X-rays were used using a silicon double-crystal spectroscope. Specifically, diffraction was caused on the (111) plane of the silicon single crystal, and the X-ray wavelength was adjusted to 0.0689 nm. Since the intensity of X-rays is large and easily attenuated in a double-crystal spectroscope, an X-ray source of a synchrotron radiation facility that can obtain high intensity was used. Specifically, BL16 of Kyushu Synchrotron Light Research Center (SAGA-LS) was used.
  • BL16B2 of SPring-8 for example, BL16B2 of SPring-8, BL16XU of SPring-8, BL19B2 of SPring-8, BL46XU of SPring-8, BL5S1 of Aichi-SR, SAGA- Similar measurements are possible using other equipment such as BL15 from LS.
  • Diffraction measurement was performed so that two diffraction lines from iron contained in the steel wire could be observed. Specifically, the (110) diffraction line of iron and the (220) diffraction line of iron are observed. The shape of the obtained diffraction line was analyzed, and the half width, wavelength, and Bragg angle of the diffraction line were determined, and the lattice strain S was calculated by substituting them into the Williamson-Hall equation of formula (1).
  • Torsion values were measured as follows. One end of the sample was fixed, the other end of the sample was twisted, and the number of twists until the sample broke was measured as the twist value. The gauge length was 100 ⁇ D and the twisting speed was 60 rpm. A first torsion value immediately after preparation of the sample and a second torsion value two weeks after preparation of the sample were measured in order to confirm the influence of age hardening on toughness. Those having both the first twist value and the second twist value of 20 times or more were regarded as acceptable.
  • Samples I to X had a first twist value of 20 or more. With reference to Table 2, sample I to sample X have a tensile strength T of 2000 N/mm 2 or more and 2700 N/mm 2 or less. Therefore, Samples I-X have high intensities. Samples VII and VIII are thought to have high ferrite area ratios because the temperature of the isothermal transformation treatment was set low. Sample IX and sample X are thought to have high ferrite area ratios due to the fact that the austenitizing temperature was set low. The ferrite area ratio also varies depending on the cooling rate from the austenitizing treatment temperature to the isothermal transformation treatment temperature in the patenting process. Referring to FIG.
  • the second twist value was 20 times or more in samples I to VI having (S+5.8885 ⁇ 10 ⁇ 3 )/T of 4.8 ⁇ 10 ⁇ 6 or more. That is, Samples I to VI are less susceptible to deterioration in toughness due to age hardening, and maintain high toughness. Samples VII through X with (S+5.8885 ⁇ 10 ⁇ 3 )/T less than 4.8 ⁇ 10 ⁇ 6 had second twist values of less than 20 turns. In other words, samples VII to X are age-hardened and their toughness is reduced. Therefore, it can be said that Samples I to VI have both high strength and high toughness. Referring to FIG.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

Le fil d'acier selon la présente invention est formé d'un acier contenant 0,5 à 0,7 % en masse de carbone, 1 à 2,5 % en masse de silicium, 0,3 à 1 % en masse de manganèse, et 0,5 à 2 % en masse de chrome, la partie restante étant du fer et des impuretés inévitables. Le fil d'acier a un diamètre de fil de 0,5 à 2 mm. Le fil d'acier a une résistance à la traction de 2 000 à 2700 N/mm2 <sp />. L'acier présente une structure de perlite. La valeur de (S + 5,8885 × 10-3)/T qui est obtenue en divisant, par la résistance à la traction T, une valeur obtenue par addition de 5,8885 × 10-3 à la contrainte de réseau S de l'acier est égale ou supérieure à 4,8 × 10-6. Ici, l'unité de la résistance à la traction est le N/mm2.
PCT/JP2022/004315 2021-06-08 2022-02-03 Ressort et fil d'acier WO2022259606A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
US17/802,486 US20240209481A1 (en) 2021-06-08 2002-02-03 Steel wire and spring
CN202280002215.XA CN115943225A (zh) 2021-06-08 2022-02-03 钢线和弹簧
JP2022530729A JP7173410B1 (ja) 2021-06-08 2022-02-03 鋼線およびばね
KR1020227031927A KR20240019005A (ko) 2021-06-08 2022-02-03 강선 및 스프링

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2021095849 2021-06-08
JP2021-095849 2021-06-08

Publications (1)

Publication Number Publication Date
WO2022259606A1 true WO2022259606A1 (fr) 2022-12-15

Family

ID=84425645

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2022/004315 WO2022259606A1 (fr) 2021-06-08 2022-02-03 Ressort et fil d'acier

Country Status (1)

Country Link
WO (1) WO2022259606A1 (fr)

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002146479A (ja) * 2000-11-06 2002-05-22 Kobe Steel Ltd 捻回特性に優れた伸線加工用線材およびその製造方法
JP2012117129A (ja) * 2010-12-02 2012-06-21 Sumitomo Electric Ind Ltd 硬引き線、ばね、及び硬引き線の製造方法
WO2018179597A1 (fr) * 2017-03-28 2018-10-04 住友電工スチールワイヤー株式会社 Fil d'acier et ressort
WO2018230717A1 (fr) * 2017-06-15 2018-12-20 新日鐵住金株式会社 Fil laminé pour acier à ressort
JP2020535313A (ja) * 2017-09-29 2020-12-03 ポスコＰｏｓｃｏ 耐腐食疲労特性に優れたばね用線材、鋼線及びこれらの製造方法
JP2021183716A (ja) * 2020-05-22 2021-12-02 住友電気工業株式会社 鋼線およびばね

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002146479A (ja) * 2000-11-06 2002-05-22 Kobe Steel Ltd 捻回特性に優れた伸線加工用線材およびその製造方法
JP2012117129A (ja) * 2010-12-02 2012-06-21 Sumitomo Electric Ind Ltd 硬引き線、ばね、及び硬引き線の製造方法
WO2018179597A1 (fr) * 2017-03-28 2018-10-04 住友電工スチールワイヤー株式会社 Fil d'acier et ressort
WO2018230717A1 (fr) * 2017-06-15 2018-12-20 新日鐵住金株式会社 Fil laminé pour acier à ressort
JP2020535313A (ja) * 2017-09-29 2020-12-03 ポスコＰｏｓｃｏ 耐腐食疲労特性に優れたばね用線材、鋼線及びこれらの製造方法
JP2021183716A (ja) * 2020-05-22 2021-12-02 住友電気工業株式会社 鋼線およびばね

Similar Documents

Publication Publication Date Title
CN102066599B (zh) 高强度极细钢线及其制造方法
WO2013094475A1 (fr) Acier pour structure mécanique pour l&#39;écrouissage froide et son procédé de fabrication
JP2017043835A (ja) 冷間加工用機械構造用鋼、およびその製造方法
WO2016002413A1 (fr) Matériau de fil pour fil d&#39;acier, et fil d&#39;acier
US10570478B2 (en) Steel for mechanical structure for cold working, and method for producing same
JP2010163689A (ja) オイルテンパー線とその製造方法、及びばね
WO2018021574A1 (fr) Fil d&#39;acier à haute résistance
JP2013204133A (ja) 線材及びこれを用いた鋼線
JP5711539B2 (ja) 腐食疲労強度に優れるばね
EP3115478B1 (fr) Fil d&#39;acier à teneur élevée en carbone présentant d&#39;excellentes propriétés d&#39;étirage de fil et son procédé de production
JP5655627B2 (ja) 耐水素脆化特性に優れた高強度ばね用鋼
JP4980172B2 (ja) 強度延性バランスに優れた高強度極細鋼線の製造方法
WO2022259606A1 (fr) Ressort et fil d&#39;acier
JP7173410B1 (ja) 鋼線およびばね
JP2021183716A (ja) 鋼線およびばね
JP4464511B2 (ja) 延性及び疲労特性の優れた高強度極細鋼線の製造方法
JP2018024909A (ja) 冷間加工用機械構造用鋼およびその製造方法
WO2015152063A1 (fr) Matériau en acier à haute résistance présentant d&#39;excellentes caractéristiques de fatigue
JP5594521B2 (ja) ベルト式ｃｖｔのエレメント用鋼及びこれを用いたエレメント
JP2001247934A (ja) ばね用鋼線およびその製造方法ならびにばね
JP2015017288A (ja) コイルばね、およびその製造方法
WO2004055226A1 (fr) Fil d&#39;acier pour ressort
WO2023162615A1 (fr) Fil d&#39;acier
JP2018162523A (ja) 鋼線用線材および鋼線
JP3641056B2 (ja) 高強度極細鋼線

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2022530729

Country of ref document: JP

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 17802486

Country of ref document: US

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 22819797

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 22819797

Country of ref document: EP

Kind code of ref document: A1