EP3486344A1 - Stahlfederdraht, feder, stahlfederdrahtherstellungsverfahren und federherstellungsverfahren - Google Patents

Stahlfederdraht, feder, stahlfederdrahtherstellungsverfahren und federherstellungsverfahren Download PDF

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Publication number
EP3486344A1
EP3486344A1 EP17827290.2A EP17827290A EP3486344A1 EP 3486344 A1 EP3486344 A1 EP 3486344A1 EP 17827290 A EP17827290 A EP 17827290A EP 3486344 A1 EP3486344 A1 EP 3486344A1
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EP
European Patent Office
Prior art keywords
mass
spring
steel wire
starting
steel
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.)
Withdrawn
Application number
EP17827290.2A
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English (en)
French (fr)
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EP3486344A4 (de
Inventor
Fuminori OKADA
Kenichi Shimizu
Takafumi UWANO
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.)
Sumitomo SEI Steel Wire Corp
Sumitomo Electric Industries Ltd
Original Assignee
Sumitomo SEI Steel Wire Corp
Sumitomo Electric Industries Ltd
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Publication date
Application filed by Sumitomo SEI Steel Wire Corp, Sumitomo Electric Industries Ltd filed Critical Sumitomo SEI Steel Wire Corp
Publication of EP3486344A1 publication Critical patent/EP3486344A1/de
Publication of EP3486344A4 publication Critical patent/EP3486344A4/de
Withdrawn legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C3/00—Profiling tools for metal drawing; Combinations of dies and mandrels
    • B21C3/02—Dies; Selection of material therefor; Cleaning thereof
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21F—WORKING OR PROCESSING OF METAL WIRE
    • B21F35/00—Making springs from wire
    • 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
    • C21D1/06—Surface hardening
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to steel wires for springs, to springs, to methods for manufacturing steel wires for springs, and to methods for manufacturing springs.
  • a steel wire for a spring according to the present invention is formed of a steel containing from 0.5% by mass to 0.8% by mass of carbon, from 1.0% by mass to 2.5% by mass of silicon, from 0.2% by mass to 1.0% by mass of manganese, and from 0.5% by mass to 2.5% by mass of chromium, the balance being iron and incidental impurities.
  • the steel has a tempered martensite structure.
  • the hardness of a surface region that is a region within 10 ⁇ m from an outer surface is from more than 0 HV to 50 HV higher than the hardness of a region other than the surface region.
  • a method for manufacturing a steel wire for a spring according to a first aspect of the present invention includes the steps of providing a starting wire material containing from 0.5% by mass to 0.8% by mass of carbon, from 1.0% by mass to 2.5% by mass of silicon, from 0.2% by mass to 1.0% by mass of manganese, and from 0.5% by mass to 2.5% by mass of chromium, the balance being iron and incidental impurities; subjecting the starting wire material to first drawing; subjecting to carburizing treatment the starting wire material subjected to the first drawing such that the carbon concentration of a region including a surface of the starting wire material is from more than 0% by mass to 0.05% by mass higher than the carbon concentration of the interior thereof; and subjecting to quenching and tempering treatment the starting wire material subjected to the carburizing treatment.
  • a method for manufacturing a steel wire for a spring according to a second aspect of the present invention includes the steps of providing a starting wire material containing from 0.5% by mass to 0.8% by mass of carbon, from 1.0% by mass to 2.5% by mass of silicon, from 0.2% by mass to 1.0% by mass of manganese, and from 0.5% by mass to 2.5% by mass of chromium, the balance being iron and incidental impurities; subjecting the starting wire material to first drawing; subjecting to quenching and tempering treatment the starting wire material subjected to the first drawing; and subjecting to second drawing the starting wire material subjected to the quenching and tempering treatment.
  • the second drawing is performed at a reduction of area of from 1% to less than 5%.
  • an object of the present disclosure is to provide a steel wire for a spring, a spring, a method for manufacturing a steel wire for a spring, and a method for manufacturing a spring that can achieve improved fatigue strength with a reduced likelihood of fractures during coiling.
  • the steel wire for a spring and the method for manufacturing a steel wire for a spring according to the present disclosure can achieve improved fatigue strength with a reduced likelihood of fractures during coiling.
  • a steel wire for a spring according to the present application is formed of a steel containing from 0.5% by mass to 0.8% by mass of carbon (C), from 1.0% by mass to 2.5% by mass of silicon (Si), from 0.2% by mass to 1.0% by mass of manganese (Mn), and from 0.5% by mass to 2.5% by mass of chromium (Cr), the balance being iron and incidental impurities.
  • the steel has a tempered martensite structure.
  • the hardness of a surface region that is a region within 10 ⁇ m from an outer surface is from more than 0 HV to 50 HV higher than the hardness of a region other than the surface region.
  • a steel wire for a spring that can achieve improved fatigue strength with a reduced likelihood of fractures during coiling is obtained by slightly increasing the hardness of a steel wire formed of a steel having a suitable constituent composition and a tempered martensite structure only in an extremely thin surface region as compared to the interior.
  • the steel used for the steel wire for a spring according to the present application has a constituent composition that can ensure the strength required of springs and a tempered martensite structure.
  • the hardness of an extremely thin surface region that is within 10 ⁇ m from the outer surface (surface region) is set to be from more than 0 HV to 50 HV higher than the hardness of the region other than the surface region (interior region). Since the hardness is increased only in the surface region by 50 HV or less in this way, the steel wire for a spring according to the present application can achieve improved fatigue strength with a reduced likelihood of fractures during coiling.
  • Carbon from 0.5% by mass to 0.8% by mass
  • Carbon is an element that greatly affects the strength of a steel having a tempered martensite structure. To achieve sufficient strength for use as a steel wire for a spring, it is necessary that the carbon content be 0.5% by mass or more. On the other hand, high carbon contents would result in decreased toughness and thus decreased workability during coiling and drawing. To ensure sufficient workability, it is necessary that the carbon content be 0.8% by mass or less. To further improve the strength, it is preferred that the carbon content be 0.6% by mass or more. To improve the toughness and facilitate working, it is preferred that the carbon content be 0.7% by mass or less.
  • Silicon from 1.0% by mass to 2.5% by mass
  • Silicon has the property of reducing softening upon heating (softening resistance). To reduce softening during strain-removing heat treatment performed after the coiling of the steel wire for a spring, it is necessary that the silicon content be 1.0% by mass or more. On the other hand, the addition of excess silicon would decrease the toughness of the steel wire for a spring. To ensure sufficient toughness, it is necessary that the silicon content be 2.5% by mass or less. To further improve the resistance to softening upon heating, it is preferred that the silicon content be 1.3% by mass or more. To more reliably ensure sufficient toughness, it is preferred that the silicon content be 2.3% by mass or less.
  • Manganese is an element added as a deoxidizing agent in steel refining. To allow manganese to function as a deoxidizing agent, it is necessary that the manganese content be 0.2% by mass or more. On the other hand, the addition of excess manganese would result in the formation of a martensite structure upon cooling after heating. An unintentionally formed martensite structure would decrease workability during processes such as drawing. Accordingly, it is necessary that the manganese content be 1.0% by mass or less. To allow manganese to more reliably function as a deoxidizing agent, it is preferred that the manganese content be 0.3% by mass or more. To more reliably reduce unintentional formation of a martensite structure, it is preferred that the manganese content be 0.85% by mass or less.
  • Chromium from 0.5% by mass to 2.5% by mass
  • Chromium contributes to reducing softening upon heating after quenching and tempering. To reliably produce this effect, it is necessary that the chromium content be 0.5% by mass or more. On the other hand, the addition of excess chromium would result in the formation of a martensite structure upon cooling after heating. An unintentionally formed martensite structure would decrease workability during processes such as drawing. Accordingly, it is necessary that the chromium content be 2.5% by mass or less. To more reliably reduce softening upon heating after quenching and tempering, it is preferred that the chromium content be 0.7% by mass or more. To more reliably reduce unintentional formation of a martensite structure, it is preferred that the chromium content be 1.5% by mass or less.
  • impurities such as phosphorus (P), sulfur (S), and copper (Cu) are incidentally incorporated into the steel forming the steel wire for a spring.
  • P phosphorus
  • S sulfur
  • Cu copper
  • the phosphorus and sulfur contents are each preferably 0.035% by mass or less, more preferably 0.025% by mass or less.
  • Copper would decrease the hot workability of the steel. Accordingly, the copper content is preferably 0.2% by mass or less.
  • the total incidental impurity content is preferably 1% by mass or less.
  • the steel wire for a spring may have a diameter of 15 mm or less.
  • the steel wire for a spring according to the present application is suitable for use as a steel wire for a spring with such a wire diameter. If the steel wire for a spring has a non-circular cross-section perpendicular to the longitudinal direction, "diameter” as used herein means the diameter of a circle circumscribing the cross-section.
  • the carbon concentration of the surface region of the steel wire for a spring may be from more than 0% by mass to 0.05% by mass higher than the carbon concentration of the region other than the surface region. If the carbon content of the surface region is higher than the carbon content of the interior (the region other than the surface region), the hardness of the surface region can be easily made higher than the hardness of the interior.
  • the proportion of the ⁇ 110 ⁇ texture in the surface region of the steel wire for a spring may be from 5% to 35% higher than the proportion of the ⁇ 110 ⁇ texture in a central region that is a region within 10 ⁇ m from the center of gravity of a cross-section perpendicular to the longitudinal direction of the steel wire for a spring. This increases the elastic limit for shear stress. As a result, the fatigue strength and settling resistance of a spring manufactured from the steel wire for a spring can be improved.
  • the proportion of the ⁇ 110 ⁇ texture in the surface region is 5% or more higher than the proportion of the ⁇ 110 ⁇ texture in the central region, the effect described above is clear.
  • the proportion of the ⁇ 110 ⁇ texture in the surface region is more than 35% higher than the proportion of the ⁇ 110 ⁇ texture in the central region, the steel wire for a spring would exhibit decreased workability during coiling.
  • the proportion of the ⁇ 110 ⁇ texture in the surface region be 30% or less higher than the proportion of the ⁇ 110 ⁇ texture in the central region. It is more preferred that the proportion of the ⁇ 110 ⁇ texture in the surface region be 15% or less higher than the proportion of the ⁇ 110 ⁇ texture in the central region.
  • the proportion of the ⁇ 110 ⁇ texture in the central region is, for example, 3% or less.
  • the proportions of the ⁇ 110 ⁇ texture in the surface region and the central region can be measured, for example, as follows.
  • the steel wire for a spring is first cut, and the cross-section is mechanically polished.
  • the mechanically polished cross-sectional surface is then subjected to ion polishing with an ion beam, such as an argon ion beam, for removal of any surface region damaged by mechanical polishing to obtain an observation surface.
  • the resulting observation surface is then subjected to crystal orientation measurement to measure the proportions of the ⁇ 110 ⁇ texture in the surface region and the central region, for example, by electron back-scatter diffraction (EBSD).
  • EBSD electron back-scatter diffraction
  • the steel wire for a spring may have a circularity of 3 ⁇ m or less in a cross-section perpendicular to the longitudinal direction. This stabilizes the properties of a spring manufactured from the steel wire for a spring.
  • the steel wire for a spring may have a variation in diameter of 1% or less per meter in a cross-section perpendicular to the longitudinal direction. This stabilizes the properties of a spring manufactured from the steel wire for a spring.
  • the steel forming the steel wire for a spring may further contain from 0.05% by mass to 0.5% by mass of vanadium.
  • Vanadium contributes to reducing softening upon heating by forming fine carbides in the steel.
  • vanadium may be added in an amount of 0.05% by mass or more.
  • the addition of excess vanadium would decrease the toughness of the steel.
  • vanadium is preferably added in an amount of 0.5% by mass or less, preferably 0.25% by mass or less.
  • a spring according to the present application is formed of the foregoing steel wire for a spring. Since the spring according to the present application is formed of the steel wire for a spring according to the present application, a spring that exhibits improved fatigue strength can be provided with a reduced likelihood of fractures during coiling.
  • the spring may have a surface with a nitrogen concentration of 300 ppm or less.
  • the spring according to the present application exhibits sufficient fatigue strength without a treatment that increases the nitrogen concentration of the surface of the spring above such a range, for example, nitriding treatment.
  • a method for manufacturing a steel wire for a spring includes the steps of providing a starting wire material containing from 0.5% by mass to 0.8% by mass of carbon, from 1.0% by mass to 2.5% by mass of silicon, from 0.2% by mass to 1.0% by mass of manganese, and from 0.5% by mass to 2.5% by mass of chromium, the balance being iron and incidental impurities; subjecting the starting wire material to first drawing; subjecting to carburizing treatment the starting wire material subjected to the first drawing such that the carbon concentration of a region including the surface of the starting wire material is from more than 0% by mass to 0.05% by mass higher than the carbon concentration of the interior thereof; and subjecting to quenching and tempering treatment the starting wire material subjected to the carburizing treatment.
  • the starting wire material having the foregoing suitable constituent composition is subjected to carburizing treatment to slightly increase the carbon concentration of the region including the surface, followed by quenching and tempering treatment.
  • carburizing treatment to slightly increase the carbon concentration of the region including the surface
  • quenching and tempering treatment This allows the hardness of the steel wire for a spring, which is formed of a steel having a suitable constituent composition and a tempered martensite structure, to be slightly increased only in an extremely thin surface region as compared to the interior.
  • the steel wire for a spring according to the present application can be easily manufactured such that the hardness of an extremely thin surface region that is within 10 ⁇ m from the outer surface (surface region) is set to be from more than 0 HV to 50 HV higher than the hardness of the region other than the surface region (interior region).
  • the step of subjecting to carburizing treatment the starting wire material subjected to the first drawing may include performing carburizing treatment by heating the starting wire material in an atmosphere whose composition is controlled to have a carbon potential (CP) value of from 0.5% by mass to 1.5% by mass. If the carburizing treatment is performed by gas carburizing in an atmosphere with a controlled CP value, the carbon concentration of the surface region becomes stable. As a result, the variation in the hardness of the surface region is reduced, and a steel wire for a spring can be easily manufactured such that the hardness of the surface region is from more than 0 HV to 50 HV higher than the hardness of the interior region.
  • CP carbon potential
  • the method for manufacturing a steel wire for a spring according to the first aspect may further include a step of subjecting to second drawing the starting wire material subjected to the quenching and tempering treatment. This improves the dimensional accuracy of the steel wire for a spring.
  • the second drawing may be performed at a reduction of area of from 1% to less than 5%. If the reduction of area is not less than 5%, it would be difficult to achieve an increase in hardness only in the extremely thin surface region since the hardness would also increase in the interior of the steel wire after drawing. If the reduction of area is set to less than 5% to achieve an increase in hardness only in the surface layer, the steel wire for a spring according to the present application can be more easily manufactured. If the reduction of area is 1% or more, an increase in hardness can be more reliably achieved in the extremely thin surface region after drawing.
  • a method for manufacturing a steel wire for a spring includes the steps of providing a starting wire material containing from 0.5% by mass to 0.8% by mass of carbon, from 1.0% by mass to 2.5% by mass of silicon, from 0.2% by mass to 1.0% by mass of manganese, and from 0.5% by mass to 2.5% by mass of chromium, the balance being iron and incidental impurities; subjecting the starting wire material to first drawing; subjecting to quenching and tempering treatment the starting wire material subjected to the first drawing; and subjecting to second drawing the starting wire material subjected to the quenching and tempering treatment.
  • the second drawing is performed at a reduction of area of from 1% to less than 5%.
  • the starting wire material having the foregoing suitable constituent composition is subjected to quenching and tempering treatment, followed by the second drawing at a reduction of area of from 1% to less than 5%.
  • the steel wire for a spring according to the present application can be easily manufactured such that the hardness of an extremely thin surface region that is within 10 ⁇ m from the outer surface (surface region) is set to be from more than 0 HV to 50 HV higher than the hardness of the region other than the surface region (interior region).
  • the second drawing may be performed while the starting wire material is heated to a temperature range from 25°C to 450°C. This forms a Cottrell atmosphere in the steel, thus increasing the strength of the steel wire for a spring.
  • the second drawing may be performed while the starting wire material is heated to a temperature range from 150°C to 450°C.
  • the second drawing may be performed through a die with an approach angle of from 0.1° to 7°. This allows an increase in hardness to be easily achieved only in the surface layer.
  • the starting wire material may be drawn to a diameter of 15 mm or less by the first drawing. If the settings for the first drawing are made such that the starting wire material is drawn to a diameter of 15 mm or less, a thin steel wire for a spring can be easily manufactured.
  • a method for manufacturing a spring according to the present application includes the steps of providing a steel wire for a spring by the methods for manufacturing a steel wire for a spring according to the present application; and coiling the steel wire for a spring.
  • a steel wire for a spring manufactured by the methods for manufacturing a steel wire for a spring according to the present application is coiled in the method for manufacturing a spring according to the present application, a spring that exhibits improved fatigue strength can be manufactured with a reduced likelihood of fractures during coiling.
  • the method for manufacturing a spring may further include a step of subjecting the coiled steel wire for a spring to shot peening treatment.
  • the steel wire for a spring to be subjected to the shot peening treatment may have a surface with a nitrogen concentration of 300 ppm or less. If the shot peening treatment is performed in the method for manufacturing a spring according to the present application without a treatment that increases the nitrogen concentration of the surface of the spring above such a range, for example, nitriding treatment, a spring that exhibits sufficient fatigue strength can be manufactured.
  • a steel wire 1 for a spring is a steel wire having a circular cross-section 10 perpendicular to the longitudinal direction and a cylindrical outer surface 11.
  • the steel wire 1 for a spring has a diameter of, for example, 15 mm or less, preferably from 2 mm to 10 mm.
  • the steel wire 1 for a spring is formed of a steel containing from 0.5% by mass to 0.8% by mass of carbon, from 1.0% by mass to 2.5% by mass of silicon, from 0.2% by mass to 1.0% by mass of manganese, and from 0.5% by mass to 2.5% by mass of chromium, the balance being iron and incidental impurities.
  • the steel has a tempered martensite structure.
  • the hardness of a surface region 12 that is a region within 10 ⁇ m from the outer surface 11 is from more than 0 HV to 50 HV higher than the hardness of an interior region 13 that is a region other than the surface region.
  • the carbon concentration of the surface region 12 is from more than 0% by mass to 0.05% by mass higher than the carbon concentration of the interior region 13.
  • the surface region 12 is a carburized layer.
  • the steel used for the steel wire 1 for a spring has the foregoing constituent composition, which can ensure the strength required of springs, and a tempered martensite structure.
  • the hardness of an extremely thin surface region that is within 10 ⁇ m from the outer surface 11 (surface region 12) is set to be from more than 0 HV to 50 HV higher than the hardness of the interior region13. Since the hardness is increased only in the surface region 12 by 50 HV or less in this way, the steel wire 1 for a spring can achieve improved fatigue strength with a reduced likelihood of fractures during coiling.
  • the hardness of the surface region 12 is preferably from 5 HV to 25 HV, preferably from 5 HV to 15 HV, higher than the hardness of the interior region 13.
  • the carbon concentration of the surface region 12 is preferably from 0.01% by mass to 0.03% by mass, more preferably from 0.01% by mass to 0.02% by mass, higher than the carbon concentration of the interior region 13.
  • the proportion of the ⁇ 110 ⁇ texture in the surface region 12 of the steel wire 1 for a spring is preferably from 5% to 35% higher than the proportion of the ⁇ 110 ⁇ texture in a central region 14 that is a region within 10 ⁇ m from the center of gravity of a cross-section perpendicular to the longitudinal direction of the steel wire 1 for a spring. This increases the elastic limit for shear stress. As a result, the fatigue strength and settling resistance of a spring manufactured from the steel wire 1 for a spring can be improved.
  • the proportion of the ⁇ 110 ⁇ texture in the central region 14 is, for example, 3% or less.
  • the steel wire 1 for a spring preferably has a circularity of 3 ⁇ m or less in the cross-section 10 perpendicular to the longitudinal direction. This stabilizes the properties of a spring manufactured from the steel wire 1 for a spring.
  • the steel wire 1 for a spring may have a variation in diameter of 1% or less per meter in the cross-section 10 perpendicular to the longitudinal direction. This stabilizes the properties of a spring manufactured from the steel wire 1 for a spring.
  • the variation in diameter means the difference between the maximum and minimum diameters per meter in the longitudinal direction.
  • the steel forming the steel wire 1 for a spring may further contain from 0.05% by mass to 0.5% by mass of vanadium. This reduces softening upon heating.
  • Examples of steels that may be employed to form the steel wire 1 for a spring include SWOSC-B in accordance with JIS G3560 and SWOCV-V and SWOSC-V in accordance with JIS G3561.
  • a spring 2 is formed of the steel wire 1 for a spring. Since the spring 2 is formed of the steel wire 1 for a spring, the spring 2 exhibits improved fatigue strength with a reduced likelihood of fractures during coiling.
  • the surface of the spring 2 (the outer surface 11 of the steel wire 1 for a spring) has a nitrogen concentration of 300 ppm or less.
  • the spring 2 exhibits sufficient fatigue strength without a treatment that increases the nitrogen concentration of the surface of the spring 2 (the outer surface 11 of the steel wire 1 for a spring) above such a range, for example, nitriding treatment.
  • a method for manufacturing the steel wire 1 for a spring begins by performing a starting-wire-material providing step as step (S10).
  • a starting wire material 5 is provided in step (S10).
  • the starting wire material 5 contains from 0.5% by mass to 0.8% by mass of carbon, from 1.0% by mass to 2.5% by mass of silicon, from 0.2% by mass to 1.0% by mass of manganese, and from 0.5% by mass to 2.5% by mass of chromium, the balance being iron and incidental impurities.
  • the starting wire material 5 is provided by subjecting a steel material such as SWOSC-B in accordance with JIS G3560 or SWOCV-V or SWOSC-V in accordance with JIS G3561 to processes such as rolling and patenting (transformation into fine pearlite).
  • the starting wire material 5 is a steel wire material having a circular cross-section 50 perpendicular to the longitudinal direction and a cylindrical outer surface 51.
  • step (S20) A first drawing step is then performed as step (S20).
  • step (S20) the starting wire material 5 is subjected to first drawing (drawing process). Specifically, the starting wire material 5 provided in step (S10) is drawn.
  • step (S20) the starting wire material 5 is drawn to a diameter of, for example, 15 mm or less.
  • step (S30) A carburizing step is then performed as step (S30).
  • Figure 5 shows the relationship between time and temperature in the carburizing step and the quenching and tempering step.
  • the horizontal axis indicates elapsed time
  • the vertical axis indicates temperature.
  • step (S30) the starting wire material 5 subjected to the first drawing in step (S20) is subjected to carburizing treatment.
  • the starting wire material 5 subjected to the first drawing in step (S20) begins to be heated at time t 0 and reaches a carburizing temperature T 1 at time t 1 . Thereafter, the starting wire material 5 is maintained at the carburizing temperature T 1 until time t 2 .
  • the carburizing temperature T 1 is a temperature higher than or equal to the austenite transformation point (A 1 transformation point). For example, the carburizing temperature T 1 is from 920°C to 930°C.
  • the starting wire material 5 is held in a carburizing atmosphere. That is, the starting wire material 5 is heated in a carburizing atmosphere.
  • the carbon concentration of the region including the surface (outer surface 51) of the starting wire material 5 becomes slightly, specifically, from more than 0% by mass to 0.05% by mass, higher than the carbon concentration of the interior thereof.
  • step (S30) the composition of the atmosphere is controlled such that the CP value of the atmosphere is from 0.5% by mass to 1.5% by mass, more preferably from 0.8% by mass to 1.2% by mass.
  • gases such as propane gas, oxygen gas, and nitrogen gas are introduced into a furnace in which the carburizing treatment is performed.
  • the introduced propane gas decomposes and reacts with the oxygen gas to produce gases such as carbon monoxide gas (CO) and methane gas (CH 4 ), which contribute to carburizing, as well as carbon dioxide gas (CO 2 ).
  • the CP value can be controlled, for example, by measuring the concentrations of carbon dioxide gas and oxygen gas in the atmosphere with a carbon dioxide sensor and an oxygen sensor and, based on these measurements, changing the amounts of propane gas and oxygen gas introduced into the furnace.
  • the carburizing treatment is performed in this way by gas carburizing while measuring the gas composition of the atmosphere and controlling the CP value based on these measurements, the carbon concentration of the surface region 12 becomes stable. As a result, the variation in the hardness of the surface region 12 is reduced, and the steel wire 1 for a spring can be easily manufactured such that the hardness of the surface region 12 is from more than 0 HV to 50 HV higher than the hardness of the interior region 13.
  • step (S40) the starting wire material 5 subjected to the carburizing treatment in step (S30) is subjected to quenching and tempering treatment.
  • the starting wire material 5 subjected to the carburizing treatment over the period from time t 1 to t 2 is quenched over the period from time t 2 to t 3 .
  • the starting wire material 5 is cooled from a temperature higher than or equal to the austenite transformation point (A 1 transformation point) to a temperature lower than or equal to the M s point. Cooling can be performed, for example, by immersing the starting wire material 5 in quenching oil. This transforms the structure of the steel forming the starting wire material 5 into a martensite structure.
  • the quenching treatment is complete.
  • the starting wire material 5 then begins to be heated at time t 4 and reaches a tempering temperature T 2 at time t 5 . Thereafter, the starting wire material 5 is maintained at the tempering temperature T 2 until time t 6 .
  • the tempering temperature T 2 is a temperature lower than the austenite transformation point (A 1 transformation point). For example, the tempering temperature T 2 is from 450°C to 600°C.
  • the starting wire material 5 is then cooled over the period from time t 6 to t 7 . Cooling can be performed, for example, by air cooling. This transforms the structure of the steel forming the starting wire material 5 into a tempered martensite structure. Thus, the tempering treatment is complete.
  • step (S50) A second drawing step is then performed as step (S50).
  • step (S50) the starting wire material 5 subjected to the quenching and tempering treatment in step (S40) is subjected to second drawing.
  • Figure 6 shows a cross-section of a drawing device for performing step (S50) in the advancing direction ⁇ , of the starting wire material 5.
  • the drawing device for performing step (S50) includes a die 70.
  • the die 70 has a through-hole formed through the die 70 in the advancing direction ⁇ of the starting wire material 5.
  • the wall surface surrounding the through-hole is a working surface 71 that comes into contact with the starting wire material 5.
  • the starting wire material 5 subjected to step (S40) advances in the longitudinal direction to enter the through-hole of the die 70.
  • the outer surface 51 of the starting wire material 5 comes into contact with the working surface 71 of the die 70.
  • the starting wire material 5 is then worked and plastically deformed such that the shape of the starting wire material 5 in a cross-section perpendicular to the longitudinal direction corresponds to the shape of the working surface 71 in a cross-section perpendicular to the advancing direction ⁇ of the starting wire material 5.
  • the area of the through-hole of the die 70 in a cross-section perpendicular to the advancing direction ⁇ of the starting wire material 5 is smaller at an exit 79 than at the entrance 78.
  • the through-hole of the die 70 has a tapered region whose cross-sectional area perpendicular to the advancing direction ⁇ of the starting wire material 5 becomes smaller in the direction from the entrance 78 toward the exit 79.
  • the taper angle of the tapered region i.e., the approach angle ⁇ , is from 0.1° to 7°.
  • the starting wire material 5 having the foregoing suitable constituent composition is subjected to carburizing treatment in step (S30) to slightly increase the carbon concentration of the region including the surface, followed by quenching and tempering treatment in step (S40).
  • carburizing treatment in step (S30) to slightly increase the carbon concentration of the region including the surface
  • quenching and tempering treatment in step (S40).
  • the steel wire 1 for a spring can be easily manufactured such that the hardness of an extremely thin surface region that is within 10 ⁇ m from the outer surface 11 (surface region 12) is set to be from more than 0 HV to 50 HV higher than the hardness of the interior region 13.
  • step (S50) is not an essential step in the method for manufacturing a steel wire for a spring according to this embodiment, performing this step improves the dimensional accuracy of the steel wire 1 for a spring.
  • the reduction of area in step (S50) is preferably from 1% to less than 5%, more preferably from 2% to 3.5%. This allows an increase in hardness to be achieved only in the surface layer, so that the steel wire 1 for a spring can be more easily manufactured.
  • step (S50) also increases the proportion of the ⁇ 110 ⁇ texture in the surface region 12 while maintaining the proportion of the ⁇ 110 ⁇ texture in the central region 14 at a low level (e.g., 3% or less). As a result, the proportion of the ⁇ 110 ⁇ texture in the surface region 12 can be made, for example, from 5% to 35% higher than the proportion of the ⁇ 110 ⁇ texture in the central region 14.
  • the second drawing in step (S50) may be performed while the starting wire material 5 is heated to a temperature range from 150°C to 450°C, preferably from 200°C to 350°C. That is, the starting wire material 5 may be subjected to warm working (warm drawing) in step (S50). This forms a Cottrell atmosphere in the steel, thus increasing the strength of the steel wire 1 for a spring.
  • the second drawing in step (S50) may be performed while the starting wire material 5 is heated to a temperature range from 25°C to 450°C.
  • step (S50) a method for manufacturing the spring 2 from the steel wire 1 for a spring obtained in step (S50) will be described.
  • a coiling step is performed as step (S60).
  • the steel wire 1 for a spring is coiled in step (S60), for example, by plastically forming the steel wire 1 for a spring into the spiral shape shown in Fig. 2 .
  • step (S70) An tempering step is then performed as step (S70).
  • step (S70) the steel wire 1 for a spring coiled in step (S60) (spring 2) is subjected to tempering treatment. Specifically, the spring 2 is heated to reduce strain induced into the spring 2 in step (S60).
  • step (S80) A shot peening step is then performed as step (S80).
  • step (S80) the spring 2 subjected to the tempering treatment in step (S70) is subjected to shot peening.
  • step (S80) is not an essential step in the method for manufacturing a spring according to this embodiment, performing this step applies a compressive stress to the region including the surface of the spring 2, thus contributing to improved fatigue strength.
  • the spring 2 according to this embodiment is finished through the foregoing steps.
  • the method for manufacturing a spring according to this embodiment allows a spring that exhibits improved fatigue strength to be manufactured with a reduced likelihood of fractures during coiling.
  • the steel wire 1 for a spring (spring 2) to be subjected to the shot peening in step (S80) may have a surface with a nitrogen concentration of 300 ppm or less. That is, the shot peening in step (S80) may be performed without subjecting the spring 2 to nitriding treatment. If the shot peening treatment is performed without nitriding treatment in the method for manufacturing the spring 2 according to this embodiment, a spring with sufficient fatigue strength can be manufactured.
  • a steel wire 1 for a spring and a spring 2 according to the second embodiment basically have the same configuration and advantages as those according to the first embodiment.
  • the steel wire 1 for a spring and the spring 2 according to the second embodiment differ from those according to the first embodiment in that they have no carburized layer.
  • the hardness of the surface region 12 of the steel wire 1 for a spring and the spring 2 according to the second embodiment is higher than the hardness of the interior region 13; however, they have the same carbon concentration. That is, the carbon concentration is uniform in the cross-section 10 perpendicular to the longitudinal direction. Even with this configuration, the steel wire 1 for a spring and the spring 2 can achieve improved fatigue strength with a reduced likelihood of fractures during coiling.
  • the method for manufacturing a steel wire for a spring and a spring according to the second embodiment is basically performed as in the first embodiment.
  • the method for manufacturing a steel wire for a spring and a spring according to the second embodiment differs from that according to the first embodiment in that the carburizing treatment performed as step (S30) is omitted and the second drawing step performed as step (S50) is an essential step.
  • the method for manufacturing a steel wire for a spring and a spring according to the second embodiment begins by performing steps (S10) and (S20) as in the first embodiment. Thereafter, steps (S40) and (S50) are performed without performing step (S30). Whereas step (S50) is not an essential step in the first embodiment, step (S50) is an essential step in the second embodiment.
  • step (S50) The reduction of area in step (S50) is from 1% to less than 5%, preferably from 2% to 3.5%. This allows an increase in hardness to be achieved only in the surface layer even through the carburizing step performed as step (S30) in the first embodiment is omitted, so that the steel wire 1 for a spring according to the second embodiment can be manufactured. Furthermore, the spring 2 according to the second embodiment can be manufactured by performing steps (S60) to (S80) as in the first embodiment.

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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)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Springs (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
EP17827290.2A 2016-07-14 2017-06-08 Stahlfederdraht, feder, stahlfederdrahtherstellungsverfahren und federherstellungsverfahren Withdrawn EP3486344A4 (de)

Applications Claiming Priority (3)

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JP2016139668 2016-07-14
JP2017038665 2017-03-01
PCT/JP2017/021367 WO2018012158A1 (ja) 2016-07-14 2017-06-08 ばね用鋼線、ばね、ばね用鋼線の製造方法およびばねの製造方法

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JP6891889B2 (ja) 2021-06-18
EP3486344A4 (de) 2019-05-22

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