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WO2018179597A1 - Fil d'acier et ressort - Google Patents

Fil d'acier et ressort Download PDF

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Publication number
WO2018179597A1
WO2018179597A1 PCT/JP2017/043632 JP2017043632W WO2018179597A1 WO 2018179597 A1 WO2018179597 A1 WO 2018179597A1 JP 2017043632 W JP2017043632 W JP 2017043632W WO 2018179597 A1 WO2018179597 A1 WO 2018179597A1
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WO
WIPO (PCT)
Prior art keywords
steel wire
less
mass
spring
wire
Prior art date
Legal status (The legal status 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 status listed.)
Ceased
Application number
PCT/JP2017/043632
Other languages
English (en)
Japanese (ja)
Inventor
隆志 渡邉
善郎 藤野
松本　断
文男 山本
拓也 小口
高橋　文雄
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
NHK Spring Co Ltd
Sumitomo SEI Steel Wire Corp
Original Assignee
NHK Spring Co Ltd
Sumitomo SEI Steel Wire Corp
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=63674975&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=WO2018179597(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by NHK Spring Co Ltd, Sumitomo SEI Steel Wire Corp filed Critical NHK Spring Co Ltd
Priority to CN202411201433.3A priority Critical patent/CN119194244A/zh
Priority to CN201780089135.1A priority patent/CN110573638A/zh
Priority to JP2019508557A priority patent/JP6884852B2/ja
Publication of WO2018179597A1 publication Critical patent/WO2018179597A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16F—SPRINGS; SHOCK-ABSORBERS; MEANS FOR DAMPING VIBRATION
    • F16F1/00—Springs
    • F16F1/02—Springs made of steel or other material having low internal friction; Wound, torsion, leaf, cup, ring or the like springs, the material of the spring not being relevant
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16F—SPRINGS; SHOCK-ABSORBERS; MEANS FOR DAMPING VIBRATION
    • F16F1/00—Springs
    • F16F1/02—Springs made of steel or other material having low internal friction; Wound, torsion, leaf, cup, ring or the like springs, the material of the spring not being relevant
    • F16F1/04—Wound springs
    • F16F1/06—Wound springs with turns lying in cylindrical surfaces
    • 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
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like
    • 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
    • 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

Definitions

  • the present invention relates to a steel wire and a spring, and more specifically to a steel wire suitable for manufacturing a spring and a spring made of the steel wire.
  • the steel wire according to the present invention has carbon of 0.7 mass% or more and 1.0 mass% or less, silicon of 0.12 mass% or more and 0.32 mass% or less, and 0.3 mass% or more and 0.9 mass% or less. It is composed of steel containing up to mass% manganese and the balance being iron and inevitable impurities.
  • the total decarburized layer depth in the cross section perpendicular to the longitudinal direction is 0.5% or less of the diameter. In a cross section perpendicular to the longitudinal direction, the difference between the maximum value and the minimum value of hardness on a straight line passing through the center of gravity is 50 HV or less.
  • FIG. 1 is a schematic cross-sectional view showing a cross section perpendicular to the longitudinal direction of a steel wire.
  • FIG. 2 is a schematic cross-sectional view showing the vicinity of the surface of a cross section perpendicular to the longitudinal direction of the steel wire.
  • FIG. 3 is a schematic perspective view showing the structure of the spring.
  • FIG. 4 is a flowchart showing an outline of a steel wire manufacturing method.
  • FIG. 5 is a schematic cross-sectional view showing a cross section perpendicular to the longitudinal direction of the raw material wire.
  • FIG. 6 is a schematic cross-sectional view for explaining the wire drawing process.
  • FIG. 7 is a schematic diagram for explaining a test method for sag resistance.
  • FIG. 1 is a schematic cross-sectional view showing a cross section perpendicular to the longitudinal direction of a steel wire.
  • FIG. 2 is a schematic cross-sectional view showing the vicinity of the surface of a cross section perpendicular to the longitudinal direction of the
  • FIG. 8 is a schematic diagram for explaining a test method for sag resistance.
  • FIG. 9 is a schematic diagram for explaining a test method for sag resistance.
  • FIG. 10 is a diagram showing the results of a sag resistance test.
  • FIG. 11 is a diagram showing the distribution of hardness in a cross section perpendicular to the longitudinal direction of the steel wire.
  • FIG. 12 is a diagram showing the results of a sag resistance test.
  • FIG. 13 is a diagram showing the relationship between the total decarburized layer depth and the surface hardness.
  • the steel wire of the present application includes carbon (C) of 0.7% by mass or more and 1.0% by mass or less, silicon (Si) of 0.12% by mass or more and 0.32% by mass or less, and 0.3% by mass or more.
  • the steel is made of steel containing 0.9% by mass or less of manganese (Mn), the balance being iron (Fe) and inevitable impurities.
  • Mn manganese
  • the total decarburized layer depth in the cross section perpendicular to the longitudinal direction is 0.5% or less of the diameter. In a cross section perpendicular to the longitudinal direction, the difference between the maximum value and the minimum value of hardness on a straight line passing through the center of gravity is 50 HV or less.
  • the appropriate component composition is selected, the decarburized layer depth is suppressed to an extremely small level as compared with the conventional one, and the variation in the hardness in the radial direction is suppressed. And strength can be improved.
  • steel having a component composition capable of ensuring the strength required for the spring is employed.
  • the total decarburized layer depth is suppressed to an extremely small level of 0.5% or less of the diameter, and the maximum hardness in the depth direction (radial direction) The difference from the minimum value is suppressed to 50 HV or less.
  • phosphorus (P) which is an inevitable impurity
  • sulfur (S) is 0.025% by mass or less
  • copper (Cu) is preferably 0.2% by mass or less.
  • the diameter of the cross section perpendicular to the longitudinal direction may be not less than 0.5 mm and not more than 7 mm.
  • the steel wire of the present application is particularly suitable for a steel wire having a diameter in this range.
  • “a diameter in a cross section perpendicular to the longitudinal direction” means a diameter of a circle circumscribing the cross section when the cross section perpendicular to the longitudinal direction is other than a circle.
  • the tensile strength may be 1900 MPa to 2450 MPa. By setting the tensile strength to 1900 MPa or more, sufficient strength can be ensured. By setting the tensile strength to 2450 MPa or less, it becomes easy to ensure sufficient toughness.
  • the drawing value in the tensile test may be 40% or more and 60% or less.
  • the aperture value By setting the aperture value to 40% or more, the workability to the spring and the fatigue strength of the spring after processing can be improved.
  • the aperture value By setting the aperture value to 60% or less, it becomes easy to ensure sufficient strength.
  • the residual shear strain in the sag resistance test is preferably 0.2% or less.
  • the area reduction rate at the time of wire drawing may be 80% or more and 90% or less. By doing so, excellent sag resistance and strength can be obtained more reliably.
  • the spring of the present application is made of the above steel wire. By comprising the steel wire having excellent sag resistance and strength, the spring of the present application can provide a spring with excellent sag resistance and strength.
  • the compressive residual stress on the surface may be 300 MPa or more. By doing in this way, the fatigue life of a spring can be lengthened.
  • the surface hardness may be 450 HV or more. By doing in this way, the fatigue life of a spring can be lengthened.
  • steel wire 1 in the present embodiment has a circular cross section perpendicular to the longitudinal direction.
  • Steel wire 1 has a carbon content of 0.7 to 1.0% by mass, silicon of 0.12 to 0.32% by mass, and 0.3 to 0.9% by mass of silicon. It is made of steel containing manganese and the balance being iron and inevitable impurities.
  • As steel having such a component composition for example, SWRS87A and SWRS87B defined in JIS standard G3502 can be adopted.
  • the steel wire 1 has a metal structure including a pearlite structure, not a metal structure in a state where the quenching process and the tempering process are performed.
  • the difference between the maximum value and the minimum value of hardness is 50 HV or less. That is, when the hardness is measured along the straight line L, the difference between the maximum value and the minimum value of the hardness is 50 HV or less.
  • the hardness can be measured using, for example, a Vickers hardness meter (micro Vickers hardness meter).
  • the total decarburized layer depth d in the cross section perpendicular to the longitudinal direction of the steel wire 1 is 0.5% or less of the diameter.
  • the total decarburized layer depth d can be measured according to JIS standard G0558.
  • a decarburizing portion 4 is formed in the vicinity of the outer peripheral surface 2 of the steel wire 1.
  • the decarburizing part 4 extends in the substrate 5 from the outer peripheral surface 2 to the inside along the steel grain boundaries.
  • ferrite decarburization in which the entire crystal grains are decarburized does not occur, and partial decarburization (grain boundary decarburization) in which the decarburized portion 4 is formed along the crystal grain boundaries. ) Has occurred.
  • the total decarburized layer depth d is preferably 0.5% or less of the diameter of the steel wire 1, and more preferably 0.3% or less.
  • the steel wire 1 of the present embodiment steel having the above composition that can secure the strength required for the spring is employed.
  • the total decarburized layer depth d is suppressed to an extremely small level of 0.5% or less of the diameter, and the maximum value of hardness in the depth direction (radial direction). And the minimum value is suppressed to 50 HV or less.
  • the steel wire 1 is a steel wire excellent in sag resistance and strength.
  • P which is an inevitable impurity
  • S is 0.025% by mass or less
  • Cu is 0.2% by mass or less.
  • the diameter of the steel wire 1 is, for example, not less than 0.5 mm and not more than 7 mm.
  • the diameter of the steel wire 1 may be 2 mm or more and 6.5 mm or less.
  • the diameter of the steel wire 1 may be 2 mm or more and 5 mm or less.
  • the tensile strength of the steel wire 1 is preferably 1900 MPa to 2450 MPa. By setting the tensile strength to 1900 MPa or more, sufficient strength can be ensured. By setting the tensile strength to 2450 MPa or less, it becomes easy to ensure sufficient toughness. From the viewpoint of achieving higher strength, the tensile strength of the steel wire 1 is more preferably 1950 MPa or more. Moreover, from the viewpoint of ensuring sufficient toughness more reliably, the tensile strength of the steel wire 1 is more preferably 2160 MPa or less.
  • the value of the drawing in the tensile test is 40% or more and 60% or less.
  • the aperture value is 40% or more, the workability to the spring and the fatigue strength of the spring after processing can be improved.
  • the aperture value By setting the aperture value to 60% or less, it becomes easy to ensure sufficient strength.
  • the value of the drawing is more preferably 50% or more.
  • the area reduction rate during drawing of the steel wire 1 is 80% or more and 90% or less. Thereby, excellent sag resistance and strength can be obtained more reliably. It is more preferable that the surface area reduction rate of the steel wire 1 is 83% or more and 87% or less.
  • spring 100 in the present embodiment is made of steel wire 1 of the present embodiment.
  • the spring 100 is obtained by processing the steel wire 1 into a spiral spring shape.
  • the spring 100 is made of a steel wire 1 having a spiral shape.
  • the spring 100 is a helical spring.
  • the spring 100 is a spring excellent in sag resistance and intensity
  • the compressive residual stress on the surface (the surface corresponding to the outer peripheral surface of the steel wire 1) is preferably 300 MPa or more. Thereby, the fatigue life of the spring 100 becomes long.
  • the compressive residual stress on the surface is basically better as it is larger.
  • the compressive residual stress on the surface can be 800 MPa or less.
  • the surface hardness is preferably 450 HV or more. This increases the fatigue life of the spring. The higher the surface hardness, the better. However, achieving a hardness exceeding 650 HV can cause problems such as a reduction in production efficiency. Therefore, the surface hardness can be 650 HV or less.
  • a raw material wire preparation process is first implemented as process (S10).
  • step (S10) referring to FIG. 5, 0.7% by mass or more and 1.0% by mass or less of carbon, 0.12% by mass or more and 0.32% by mass or less of silicon, and 0.3% by mass.
  • a raw material wire 10 is prepared which is made of steel containing 0.9% by mass or less of manganese and the balance being iron and inevitable impurities.
  • a raw material wire 10 made of SWRS87B defined in JIS standard G3502 is prepared.
  • the shape of the cross section perpendicular to the longitudinal direction of the raw material wire 10 is circular.
  • a surface layer removing step is performed as a step (S20).
  • the surface layer portion including the outer peripheral surface of the raw material wire 10 prepared in the step (S10) is removed over the entire circumference.
  • the removal of the surface layer portion can be performed by, for example, cutting.
  • a process (S20) is not an essential process in manufacture of the steel wire 1, the decarburization layer of the raw material wire 10 prepared in the process (S10) can be removed by implementing this.
  • a patenting step is performed as a step (S30).
  • step (S30) patenting is performed on the raw material wire 10 on which the step (S20) has been performed. Specifically, after the raw material wire 10 is heated to a temperature range equal to or higher than the austenitizing temperature (A 1 point), it is rapidly cooled to a temperature range higher than the M s point, and a heat treatment that is held in the temperature range is performed. The Thereby, the metal structure of the raw material wire 10 becomes a fine pearlite structure with a small lamella interval.
  • the process of heating the raw material wire 10 to a temperature range above a point A is carried out the occurrence of decarburization from the viewpoint of suppressing in an inert gas atmosphere. From the same viewpoint, it is preferable that the process for heating the raw material wire 10 to a temperature range of A 1 point or higher is a minimum necessary time.
  • a wire drawing step is performed as a step (S40).
  • the raw material wire 10 is drawn (drawn).
  • FIG. 6 is a view showing a cross section along the traveling direction ⁇ of the workpiece of the drawing device for carrying out the step (S40).
  • the drawing apparatus for carrying out the step (S ⁇ b> 40) includes a die 50.
  • a through hole is formed in the die 50 so as to penetrate the die 50 along the traveling direction ⁇ of the workpiece.
  • a wall surface surrounding the through hole is a processing surface 51 that contacts the workpiece.
  • the raw material wire 10 is processed and plastically deformed so that the shape of the cross section perpendicular to the longitudinal direction corresponds to the shape of the work surface 51 in the cross section perpendicular to the traveling direction ⁇ of the work piece.
  • the area of the cross section of the through hole of the die 50 perpendicular to the traveling direction ⁇ of the workpiece is smaller at the outlet 59 than at the inlet 58.
  • the through-hole of the die 50 has a tapered region in which the cross-sectional area perpendicular to the traveling direction ⁇ of the workpiece becomes smaller as it approaches the outlet 59 from the inlet 58.
  • the die half angle ⁇ which is the taper angle of the taper region, the difference between the maximum value and the minimum value of the hardness on the straight line passing through the center of gravity is reduced in the cross section perpendicular to the longitudinal direction of the obtained steel wire 1. can do.
  • a die 50 whose die half angle ⁇ is smaller by about 30% than a die used for manufacturing a general spring steel wire is employed.
  • a certain area reduction ratio (S 0 -S) / S 0 is preferably 80% or more and 90% or less, and more preferably 83% or more and 87% or less.
  • the wire drawing in the step (S40) may be performed in a plurality of times using a plurality of dies.
  • the steel wire 1 in this Embodiment is obtained by the above procedure.
  • a decarburized layer is removed by implementing a process (S20).
  • the total decarburized layer depth in the cross section perpendicular to the longitudinal direction of the steel wire 1 can be 0.5% or less of the diameter.
  • wire drawing is implemented using the die
  • the difference between the maximum value and the minimum value of the hardness on the straight line passing through the center of gravity of the cross section perpendicular to the longitudinal direction of the steel wire 1 can be reduced to 50 HV or less.
  • a spring machining step is performed as a step (S50).
  • the steel wire 1 obtained by performing steps (S10) to (S40) is processed into a spring shape.
  • cold coiling is performed, whereby the steel wire 1 is processed into a helical spring shape having a helical shape (see FIG. 3).
  • a strain removing step is performed.
  • a process of reducing the strain (working strain) introduced into the spring by performing step (S50) is performed.
  • an annealing process is performed in which the spring obtained by performing the step (S50) is heated to, for example, a temperature of 200 ° C. or more and 400 ° C. or less and held for a time of 10 minutes or more and 60 minutes or less.
  • step (S70) a shot peening step is performed.
  • shot peening is performed after, for example, bearing surface polishing is performed on the spring whose distortion has been reduced in step (S60). Thereafter, treatments such as annealing and cold setting are performed as necessary.
  • the spring 100 in the present embodiment is obtained by the above procedure.
  • the spring 100 is manufactured by processing the steel wire 1 having excellent sag resistance and strength. Therefore, the spring 100 having excellent sag resistance and strength can be manufactured.
  • the compressive residual stress on the surface of the spring 100 is increased.
  • the hardness can be adjusted to a preferable range (compressive residual stress of 300 MPa or more, hardness of 450 HV or more).
  • the shot peening may be performed a plurality of times, for example, twice.
  • the size of the shot grain may be different between the first time and the second time.
  • the second shot peening may be performed using smaller shot grains than the first shot peening.
  • the average of the diameter of the first shot grain and the diameter of the second shot grain can be, for example, about 0.3 mm.
  • the diameter of the first shot grain can be, for example, 0.3 mm or more and 0.8 mm or less.
  • the diameter of the second shot grain can be, for example, 0.05 mm or more and 0.3 mm or less.
  • Example 1 An experiment was conducted to confirm the sag resistance of the steel wire of the present application.
  • the experimental procedure is as follows. First, a raw material wire made of SWRS87B defined in JIS standard G3502 was prepared, and a steel wire 1 was manufactured by the same method as in the above embodiment. Manufacture steel wire 1 (Examples A, B, C and D) in which the area reduction rate of wire drawing in the step (S40) is 78.2%, 83.0%, 84.9% and 86.4% did. For comparison, a general-purpose oil temper wire (Comparative Example A) and a general-purpose piano wire (Comparative Example B) were also prepared.
  • an oil temper wire for valve springs (SWOSC-V defined in JIS standard G3561) was adopted.
  • As the general-purpose piano wire a material wire material made of SWRS82A defined in JIS standard G3522 was subjected to a patenting treatment and then drawn.
  • the prepared steel wires 1 of Examples A to D are connected to the straight long side 72 and both ends of the long side 72 as shown in FIG. 7 so as to face each other in the direction perpendicular to the long side 72. It processed into the test piece 70 of the shape containing a pair of linear short side 71 extended. Next, the test piece 70 is heated to 350 ° C. and held for 20 minutes, and then the test piece 70 has a long side 72 and a pair of short sides 71 on the main surface 81A of the base plate 81. Placed in contact. And while heating the test piece 70 to 120 degreeC, as shown in FIG.
  • Examples A to D which are steel wires of the present application, have a reduced residual shear strain as compared with Comparative Example B, which is a general-purpose piano wire, and have excellent sag resistance. Is confirmed.
  • the comparison is an oil tempered wire that increases the manufacturing cost by performing quenching and tempering treatment. It has the same settling resistance as Example A. From this, it is confirmed that the area reduction rate during wire drawing is preferably 80% or more and 90% or less (83% or more and 87% or less).
  • the residual shear strain of Example C is 0.18% or less, and the sag resistance is particularly excellent.
  • Example 2 An experiment was conducted to confirm the effect of the die half angle ⁇ during wire drawing on the properties of the steel wire.
  • the die half angle ⁇ at the time of wire drawing is a condition (comparative example C) that is a range used for manufacturing a general spring steel wire, and a die that is 30% smaller than that.
  • a steel wire made of steel having the same composition was manufactured under the conditions of the above-described embodiment where the half angle ⁇ was adopted (the above-mentioned Example B), and a tensile test was performed.
  • the steel wire of Example B not only exceeds Comparative Example C in tensile strength, but also exceeds Comparative Example C in drawing. From this, it is confirmed that setting a small die half angle is effective from the viewpoint of improving the aperture while ensuring high strength.
  • the hardness of the steel wire of Comparative Example C has a difference of 69 HV in the radial direction, whereas the hardness of the steel wire of Example B is suppressed to a difference of 43 HV in the radial direction. It has been. From this, it is confirmed that setting the die half angle to be small is effective from the viewpoint of reducing the difference in hardness.
  • Example 3 Experiments were conducted to investigate the effects of surface hardness and the amount of compressive stress on the surface on the durability of the spring. The experimental procedure is as follows.
  • a raw material wire made of SWRS87B defined in JIS standard G3502 was prepared, and steps (S10) to (S40) were performed in the same manner as in the above embodiment to produce steel wire 1.
  • the steel wire 1 was cold coiled (average coil diameter: 21.6 mm, number of turns: 5.75, number of effective turns: 3.25), then heated to 300 ° C. and held for 25 minutes Strain relief annealing was performed. Thereafter, seating surface polishing and shot peening were performed. Shot peening was performed in two steps. The average diameter of the first and second shot grains was 0.3 mm. Thereafter, the spring 100 was fabricated by further performing low-temperature annealing and cold setting for heating to 230 ° C. and holding for 10 minutes.
  • sample size and treatment time of the first and second shot grains in the shot peening were adjusted to obtain seven types of samples having different surface hardness and compressive residual stress on the surface (samples A to G).
  • the surface hardness was measured according to JIS Z2244. Residual stress was measured by X-ray diffraction. Then, a fatigue test was repeatedly performed on the springs 100 of Samples A to G repeatedly in the axial direction under conditions of an average stress of 588 MPa and a stress amplitude of 534 MPa. For each of samples A to G, 8 springs were prepared and used for the experiment. Then, the durability was evaluated by the number of unbroken springs at the time when the number of stress repetitions was 10 6 times and 10 7 times. Table 3 shows the surface hardness of each sample, the compressive residual stress on the surface, and the experimental results.
  • the surface hardness is preferably 450 HV or more, and more preferably 500 HV or more.
  • the compressive residual stress on the surface is preferably 300 MPa or more.
  • Example 4 An experiment was conducted to confirm the sag resistance of the spring of the present application. Specifically, the springs 100 of the samples E, F, and A were compressed in the axial direction while being heated to 120 ° C. and held for 48 hours. For comparison, a general-purpose oil tempered wire (sample H; the same type of oil tempered wire as in Example 1) and a general-purpose piano wire (sample I; the same type of piano wire as in Example 1) are outside the scope of the present application. A similar spring was prepared for the above and was subjected to the same experiment. Thereafter, the compression was released, and the residual shear strain was calculated from the change in the axial length of the spring before and after the test. The relationship between the shear stress value and the amount of shear strain was investigated by changing the shear stress value during compression. The experimental results are shown in FIG.
  • the amount of residual shear strain increases as the shear stress increases.
  • the amount of shear strain of sample E, F, and A which is a spring of this application is smaller than sample I which is a spring which consists of a general-purpose piano wire in each stress.
  • the amount of shear strain of Samples E, F, and A is a value comparable to that of Sample H, which is a spring made of a general-purpose oil tempered wire whose manufacturing cost increases with the heat treatment cost. From this, it is confirmed that the spring of this application is a spring excellent in sag resistance.
  • Example 5 An experiment was conducted to confirm the effect of the total decarburization depth on the surface hardness of the steel wire.
  • the steel wire from which the total decarburization layer depth differs was prepared by changing the conditions of the heat processing in the presence or absence of implementation of a process (S20), and a process (S30).
  • the surface layer hardness of each steel wire was measured.
  • the surface hardness was measured in accordance with JIS Z2244 for the hardness within a region of 25 ⁇ m from the surface of the cross section.
  • the experimental results are shown in FIG.
  • the horizontal axis represents the ratio of the total decarburized layer depth in the cross section perpendicular to the longitudinal direction to the diameter of the steel wire.
  • the vertical axis represents the surface hardness.
  • the surface hardness decreases as the total decarburized layer depth increases. And when the total decarburization layer depth is 0.5% or less of the diameter of a steel wire, surface layer hardness (surface hardness) is 450HV or more which is a desirable value. From this, in the steel wire, it is confirmed that the total decarburized layer depth in the cross section perpendicular to the longitudinal direction is preferably 0.5% or less of the diameter.

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

Abstract

L'invention concerne un fil d'acier constitué d'acier formé de 0,7 à 1,0 % en masse de carbone, de 0,12 à 0,32 % en masse de silicium, de 0,3 à 0,9 % en masse de manganèse, le reste étant du fer et des impuretés inévitables. La profondeur totale de la couche décarbonisée dans une section transversale perpendiculaire à la direction longitudinale du fil d'acier est inférieure ou égale à 0,5 % du diamètre. La différence entre la valeur maximale et la valeur minimale pour une dureté sur une ligne droite passant par le centre de gravité dans une section transversale perpendiculaire à la direction longitudinale du fil d'acier est inférieure ou égale à 50 HV.
PCT/JP2017/043632 2017-03-28 2017-12-05 Fil d'acier et ressort Ceased WO2018179597A1 (fr)

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EP3702638A1 (fr) * 2019-02-26 2020-09-02 NV Bekaert SA Actionneur d'ouverture et de fermeture d'une porte ou d'un hayon d'une voiture
WO2020173647A1 (fr) * 2019-02-26 2020-09-03 Nv Bekaert Sa Ressort de compression hélicoïdal pour actionneur d'ouverture et de fermeture de porte ou de hayon de voiture
WO2021249686A1 (fr) * 2020-06-12 2021-12-16 Nv Bekaert Sa Ressort de compression hélicoïdal à section transversale non ronde pour actionneur d'ouverture et de fermeture de porte ou de hayon de voiture
JPWO2022085230A1 (fr) * 2020-10-19 2022-04-28
JP7173410B1 (ja) * 2021-06-08 2022-11-16 住友電気工業株式会社 鋼線およびばね
WO2022259606A1 (fr) * 2021-06-08 2022-12-15 住友電気工業株式会社 Ressort et fil d'acier

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WO2021249686A1 (fr) * 2020-06-12 2021-12-16 Nv Bekaert Sa Ressort de compression hélicoïdal à section transversale non ronde pour actionneur d'ouverture et de fermeture de porte ou de hayon de voiture
JP7704149B2 (ja) 2020-10-19 2025-07-08 住友電気工業株式会社 スチールワイヤー、タイヤ
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CN116194308A (zh) * 2020-10-19 2023-05-30 住友电气工业株式会社 钢丝和轮胎
WO2022259606A1 (fr) * 2021-06-08 2022-12-15 住友電気工業株式会社 Ressort et fil d'acier
CN115943225A (zh) * 2021-06-08 2023-04-07 住友电气工业株式会社 钢线和弹簧
JP7173410B1 (ja) * 2021-06-08 2022-11-16 住友電気工業株式会社 鋼線およびばね

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