EP3020841B1 - Ressort hélicoïdal et procédé de fabrication de ce dernier - Google Patents

Ressort hélicoïdal et procédé de fabrication de ce dernier Download PDF

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Publication number
EP3020841B1
EP3020841B1 EP14823237.4A EP14823237A EP3020841B1 EP 3020841 B1 EP3020841 B1 EP 3020841B1 EP 14823237 A EP14823237 A EP 14823237A EP 3020841 B1 EP3020841 B1 EP 3020841B1
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Prior art keywords
coil spring
less
grain size
fatigue resistance
depth
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EP14823237.4A
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German (de)
English (en)
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EP3020841A1 (fr
EP3020841A4 (fr
Inventor
Fumio Yamamoto
Kengo TSURUGAI
Nao Yoshihara
Kei Masumoto
Hiroshi Oura
Tetsuo Jinbo
Toshio MAEHATA
Yoshiharu Yamamoto
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NHK Spring Co Ltd
Kobe Steel Ltd
Kobelco Wire Co Ltd
Original Assignee
NHK Spring Co Ltd
Kobe Steel Ltd
Shinko Wire Co Ltd
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Publication of EP3020841A1 publication Critical patent/EP3020841A1/fr
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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
    • 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
    • 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
    • C21D1/773—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material under reduced pressure or vacuum
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/20—Carburising
    • C23C8/22—Carburising of ferrous surfaces

Definitions

  • the present invention relates to a coil spring and a method for manufacturing same, and more particularly to a coil spring with excellent fatigue resistance and a method for manufacturing same.
  • Coil springs are used as a valve spring, a clutch spring, a suspension spring, etc., in the engine, clutch and suspension of an automobile and the like.
  • a coil spring is repeatedly used under a high stress over a long period of time and thus required to have a high level of fatigue resistance.
  • Wires for the valve spring in the engine as specified by JIS include, for example, an oil-tempered wire for a valve spring (SWO-V: JIS G 3561), a chrome-vanadium steel oil-tempered wire for a valve spring (SWOCV-V: JIS G 3565), and a silicon-chromium steel oil-tempered wire for a valve spring (SWOSC-V: JIS G 3566) .
  • SWOSC-V has been mainly used because of its excellent fatigue resistance.
  • a general method for manufacturing a valve spring involves coiling such a wire into a spring having a required shape, followed by nitriding, shot peening, tempering, setting, and the like, thereby producing a spring with excellent fatigue resistance.
  • the valve spring is modified to improve its fatigue resistance, making the valve spring more compact, which can further contribute to the reduction in weight of the engine. For this reason, some proposals have been presented to improve the fatigue resistance of the valve spring.
  • Patent Document 1 discloses the technical feature in which a coil spring is designed to have on its surface a carburized layer (of 0.05 to 1.00 mm in depth) with a predetermined composition and also to exhibit the hardness in a depth of 0.02 mm from its surface within a predetermined range (of 650 to 1,000 HV), thereby improving the fatigue resistance.
  • Patent Document 1 JP 2012-77367 A JP 2003 213372 describes a steel wire for a spring containing, by mass, 0.50 to 0.90% C, 1.0 to 3.0% Si, 0.5 to 1.5% Mn and 0.1 to 5.0% Cr, and having a metallic structure mainly consisting of tempered martensite.
  • the old austenite grain size (JIS G 0551) of tempered martensite is #11 to 15, and the maximum grain size is ⁇ 8 ⁇ m.
  • JP 2012 144752 describes a spring having Rockwell hardness of HRC 53 to HRC 56, and when the Rockwell hardness of the spring is defined as H, in the range of the Rockwell hardness range of HRC 53 to HRC 56, dislocation density D (cm) satisfies the following formula (1): D ⁇ 1.4 ⁇ 10 ⁇ H-6.7 ⁇ 10, and the prior austenitic grain size number is No.10 or higher.
  • EP 1 619 264 describes a steel wire having tempered martensite, comprising, as essential components, by mass, C: 0.53 to 0.68%; Si: 1.2 to 2.5%; Mn: 0.2 to 1.5%; Cr: 1.4 to 2.5%; Al: 0.05% or less; further comprising, as a selective component, Ni: 0.4% or less; V: 0.4% or less; Mo: 0.05 to 0.5%; or Nb: 0.05 to 0.5%; and further comprising remainder essentially consisting of Fe and inevitable impurities, wherein the grain size number of prior austenite is 11.0 or larger, and the proof stress ratio ( ⁇ 0.2 / ⁇ B ), namely, a ratio of 0.2% proof stress ( ⁇ 0.2 ) to tensile strength ( ⁇ B ) is 0.85 or lower.
  • EP 0 643 148 a steel material comprising: 0.35-0.70 % of carbon, over 0.15 to 2.5 % of silicon, 0.2-1.5 % of manganese, 0.20-1.5 % of chromium, 0.05-0.5 % of molybdenum, 0.015-0.05 % of aluminum, 0.002-0.02 % of nitrogen, and reduced amounts of phosphorus, copper and oxygen, and, occasionally, specified amounts of titanium, boron and other element (s) .
  • a shaft part is made from this material and has a mean sectional hardness HVa of 560 or above, and/or an austenite grain size of the induction-hardened layer of No. 9 or above, and/or a surface residual stress of -80 kgf/mm 2 or below.
  • the coil spring mentioned in Patent Document 1 has a fatigue resistance of a level of fifty million times. In recent years, along with the progress in reducing the weight and enhancing the output of the vehicle, coil springs have been required to exhibit more excellent fatigue resistance.
  • the present invention has been made in light of the foregoing circumstance, and it is an object of the present invention to provide a coil spring with excellent fatigue resistance and a method for manufacturing such a coil spring with the excellent fatigue resistance.
  • the present invention that can solve the foregoing problems provides a coil spring made of steel, consisting of (in % by mass, the same shall apply for a chemical composition) : C: 0.40 to 0.70%; Si: 1.50 to 3.50%; Mn: 0.30 to 1.50%; Cr: 0.10 to 1.50%; V: 0.50 to 1.00%, and Al: 0.01% or less (excluding 0%), optionally further consisting of: Ni: 1.50% or less (excluding 0 %) ; and/or Nb: 0.50% or less (excluding 0%), with the balance being iron and inevitable impurities including: P 0.016% or less; and S: 0.015% or less, wherein an average crystal grain size number of prior austenite crystals in a depth of 0.3 mm from a surface is 11.0 to 15.0, while a difference in grain size number between the respective prior austenite crystals is in a range of less than 3 from a grain size number observed at the maximum frequency, and wherein a carburized layer is provided in a depth of 0.
  • the present invention can control the carburizing depth of the surface of the coil spring and the Vickers hardness thereof as appropriate, while properly controlling the chemical composition and the prior austenite crystal grain size, thereby producing the coil spring with excellent fatigue resistance. Furthermore, the method according to the present invention can provide the coil spring with excellent fatigue resistance.
  • the inventors have studied chemical compositions, metallographic structures, and the like. As a result of intensive studies, it has been found that as the toughness and strength of the coil spring affect fatigue fracture of the coil spring in use, these factors can be controlled as appropriate to enable drastic improvement of the fatigue resistance of the coil spring.
  • the inventors have diligently investigated and, as a result, found that the chemical composition of the steel can be appropriately controlled to solve the above-mentioned problems.
  • the crystal grain of prior austenite is prevented from being coarsened even after the carburization process at a high temperature, further suppressing generation of duplex-grains.
  • the present invention has been made based on the findings that, on the assumption that the following chemical composition is satisfied, the carburized layer depth, the Vickers hardness, and the prior austenite crystal grain size are appropriately controlled to enable keeping balance between the strength and toughness required for improving the fatigue resistance, thereby providing a coil spring with the excellent fatigue resistance mentioned above.
  • Carbon (C) is an element that is effective in ensuring the adequate strength of a coil spring used under a high load and the Vickers hardness of the coil spring in the position of 1/4 ⁇ D.
  • the C content is 0.40% or more, preferably 0.45% or more, and more preferably 0.50% or more. Any excessive C content, however, degrades the toughness of the coil spring and increases surface flaws of the coil spring, resulting in reduced fatigue resistance. Accordingly, the C content should be 0.70% or less, preferably 0.65% or less, and more preferably 0.60% or less.
  • Si is an element that is effective in ensuring the adequate Vickers hardness, similar as C. Further, Si is also effective in improving the strength of the coil spring, the fatigue resistance and the sagging resistance. To exhibit these effects, the Si content is 1.50% or more, preferably 1.80% or more, and more preferably 2.10% or more. Any excessive Si content, however, degrades the toughness of the coil spring and reduces the cold workability and the hot workability during the manufacturing procedure for the coil spring, which leads to poor yield of products and assists in decarburization due to a heat treatment, thus degrading the fatigue resistance. Accordingly, the Si content should be 3.50% or less, preferably 3.30% or less, and more preferably 3.10% or less.
  • Manganese (Mn) is an element that is effective in improving the strength of the coil spring by enhancing the quenching properties. Further, Mn serves to fix, in the steel, sulfur (S) that would adversely affect the fatigue resistance, to thereby convert it into MnS, which reduces the above-mentioned disadvantage. To exhibit these effects, the Mn content is 0.30% or more, preferably 0.40% or more, and more preferably 0.50% or more. Any excessive Mn content, however, degrades the toughness of the coil spring and also reduces the cold workability and the fatigue strength. Accordingly, the Mn content should be 1.50% or less, preferably 1.20% or less, and more preferably 0.90% or less.
  • Chromium (Cr) is an element that is effective in improving the strength of the coil spring by enhancing the quenching properties, similar as Mn. Cr also has the effects of reducing activity of C to prevent the decarburization in the hot-rolling process or the heat treatment. To exhibit these effects, the Cr content is 0.10% or more, preferably 0.15% or more, and more preferably 0.20% or more. Any excessive Cr content, however, drastically decreases a C diffusion coefficient in a vacuum carburization process, making it difficult to form a desired carburized layer, resulting in reduced fatigue resistance.
  • the Cr content should be 1.50% or less, preferably 1.20% or less, and more preferably 0.90% or less.
  • V 0.50 to 1.00%
  • Vanadium (V) is an element that is effective in making the prior austenite crystal grains finer. Especially, V is the element that is also effective in suppressing the coarsening of the prior austenite crystal grains and generation of duplex-grains, which are problems in the related art when the carburization temperature is increased to ensure the desired carburized layer.
  • the V content is 0.50% or more, preferably 0.53% or more, and more preferably 0.56% or more. Any excessive V content, however, forms a large amount of V carbide, degrading the ductility, the cold workability, and the resistance to the fatigue of the coil spring. Accordingly, the V content should be 1.00% or less, preferably 0.90% or less, and more preferably 0.80% or less.
  • Aluminum (Al) is a deoxidizing element but any excessive Al content forms inclusions, such as AlN. These inclusions drastically degrade the fatigue resistance of the coil spring. Accordingly, the Al content needs to be reduced to 0.01% or less, preferably 0.008% or less, and more preferably 0.006% or less.
  • the basic chemical composition of the steel configuring the coil spring in the present invention has been mentioned above, with the balance being substantially iron.
  • the term "substantially” as used herein means that the present invention allows, without departing from the feature of the invention, the contamination of a very small amount of elements present in a steel raw material, including scraps, and which would inevitably occur during an iron manufacture process, a steel manufacture process, further, a steel-manufacture preliminary treatment process, and the like.
  • exemplary inevitable impurities include P (of 0.016% or less, and more preferably 0.015% or less), and S (of 0.015% or less).
  • the invention may contain both or either of Ni and Nb in the following ranges as other elements, as needed.
  • the characteristics of the coil spring are further improved depending on the kinds of contained elements.
  • Ni 1.50% or less (excluding 0%)
  • Nickel (Ni) is an element that is effective in improving the toughness of the coil spring that increased its strength by C. To exhibit these effects, the Ni content is preferably 0.05% or more, and more preferably 0.10% or more. Any excessive Ni content, however, generates residual austenite in an excessively amount, which degrades the fatigue resistance of the coil spring. Accordingly, the Ni content is preferably 1.50% or less, more preferably 1.20% or less, and much more preferably 0.90% or less.
  • Nb 0.50% or less (excluding 0%)
  • Niobium has the effect of making the crystal grains finer in the hot-rolling process as well as the quenching-and-tempering process, thereby improving the ductility of the coil spring.
  • the Nb content is preferably 0.01% or more, and more preferably 0.02% or more. Any excessive Nb content, however, generates the V carbides in an excessive amount to thereby degrade the ductility of the coil spring, reducing the cold workability and the fatigue strength. Accordingly, the Nb content is preferably 0.50% or less, more preferably 0.40% or less, and much more preferably 0.30% or less.
  • Average crystal grain size number of the prior austenite crystals 11.0 to 15.0
  • the crystal grain size of the prior austenite crystals in a depth of 0.3 mm from the surface of the coil spring can be made finer to increase its crystal grain size number, thereby enhancing the toughness thereof to drastically improve the fatigue resistance of the coil spring.
  • the lower limit of the average crystal grain size number of the prior austenite crystal is 11.0, preferably 12.0, and more preferably 13.0.
  • the upper limit of the average crystal grain size number is 15.0, and more preferably 14.0.
  • Difference in grain size number between the prior austenite crystals within a range of less than 3 from the grain size number observed at the maximum frequency
  • the measured crystal grain size number of each prior austenite crystal needs to be within a difference of less than 3, preferably 2 or less, and more preferably 1 or less from the grain size number observed at the maximum frequency. Note that in the present invention, the state in which such a condition for the difference in grain size number is satisfied is referred to as "no duplex-grain".
  • the austenite crystal grains in the steel wire of the coil spring satisfy the above-mentioned average crystal grain size number, and further the formation of duplex-grains is suppressed, whereby the fatigue resistance can be improved.
  • Carburized layer in a depth of 0.30 to 1.00 mm from the surface of the coil spring
  • the appropriate carburized layer is effective in improving the fatigue resistance of the coil spring. That is, the surface side of the coil spring is sufficiently hardened, which can suppress the occurrence of fracture starting from the surface of the spring when the coil spring is repeatedly used under the high load stress. To exhibit these effects, the carburized layer needs to be formed in at least a depth of 0.30 mm or more, preferably 0.40 mm or more, and more preferably 0.50 mm or more, from the surface of the coil spring. However, when the rate of the carburized layer in the steel wire of the coil spring becomes excessive, coarsened carbides are precipitated, which might degrade the fatigue resistance of the coil spring. Therefore, the carburized layer needs to be formed in a depth of 1.00 mm or less, preferably 0.90 mm or less, and more preferably 0.80 mm or less from the surface of the coil spring.
  • the coil spring formed of steel, the inside of which has an appropriate Vickers hardness (Hv), is effective in improving the fatigue resistance of the coil spring.
  • Hv Vickers hardness
  • the lower limit of an average Vickers hardness at least in the depth (1/4) ⁇ D from the surface of the coil spring is 600, preferably 670, and more preferably 690.
  • the upper limit of the above-mentioned average Vickers hardness is 750, and more preferably 730.
  • manufacturing conditions therefor can be desirably controlled as appropriate.
  • it is effective to control the temperature of the vacuum carburization process.
  • Preferable conditions for manufacturing the coil spring in the present invention will be described below.
  • the coil spring in the present invention can be manufactured by subjecting a steel material satisfying the above predetermined chemical composition to melting, hot forging, and hot rolling into a wire rod having a desired wire diameter, followed by shaving, patenting, wire-drawing and oil tempering of the wire rod, and thereafter forming the obtained wire into a spring, which is then subjected to vacuum carburization process. Thereafter, to further improve the fatigue properties, shot peening, setting, or the like may be performed as needed.
  • the conditions for the aforesaid melting, hot forging and hot rolling are not specifically limited, and thus may be conventional manufacturing conditions.
  • a steel ingot satisfying the above predetermined chemical composition is manufactured through melting in a blast furnace, and the steel ingot is subjected to blooming to produce a billet with a predetermined size.
  • the billet might be heated, for example, to approximately 900°C to 1100°C, and then hot-rolled at a desired rolling reduction to form a wire rod with a desired shape property. Thereafter, a deoxidized layer formed on the surface of the wire rod is removed by being shaved by a desired thickness.
  • the patenting process, or a soft annealing process or the like in an IH (induction heating) equipment is performed.
  • the wire rod is drawn into one with a desired wire diameter, followed by the oil tempering process to thereby form a wire for a spring. Then, the wire is formed into a spring with the desired coil diameter, free height and number of turns.
  • the reason why the wire is formed into the spring shape before the carburization process is that after the carburization quenching and tempering for forming the carburized layer, the surface part of the steel (carburized layer) becomes hard and the ductility of the wire is degraded, making it difficult to form the coil spring.
  • the vacuum carburization process is performed.
  • the vacuum carburization process needs to be performed at a high carburization temperature of 1,000°C to 1,100°C.
  • the lower limit of the carburization temperature is preferably 1,020°C, and more preferably 1,040°C .
  • the upper limit of the carburization temperature is 1,100°C, and more preferably 1,080°C.
  • the vacuum carburization process is performed from the viewpoint of suppressing the decarburization and temperature variation.
  • the vacuum carburization process is performed at a temperature of 1,000°C to 1,100°C, whereby the carburized layer can be uniformly formed in the desired thickness.
  • the carburization time and the diffusion time are not specifically limited and may be any adequate times that form the desired carburized layer. For example, the carburization time may be set at 1 to 10 minutes, and the diffusion time may be set at 1 to 10 minutes.
  • gas cooling or oil quenching is continuously performed down to a temperature of the A 1 transformation temperature or lower.
  • a re-heating process (for example, at a temperature of 830°C to 850°C for 10 minutes to 30 minutes) is desirably performed, whereby the prior austenite crystal grains can be made much finer.
  • the tempering process may be performed to improve the toughness and ductility as needed.
  • the obtained coil spring may be subjected to the conventional shot peening and setting as appropriate for the purpose of further improving the fatigue resistance of the coil spring.
  • any conditions other than the above-mentioned ones are not specifically limited, and general manufacturing conditions may be applied.
  • the coil spring obtained in this way can be used as the coil spring with excellent fatigue resistance in various applications, including a valve spring for an engine, a spring for a transmission, and the like, as mentioned above.
  • a steel material was melted in a vacuum melting furnace to form steels A to H having the chemical compositions shown in Table 1 below (with the balance being iron and inevitable impurities) and subjected to hot forging, thereby fabricating billets of 155 mm square.
  • Each billet was heated at 1,000°C and hot-rolled to produce a wire rod for a spring having a diameter of 8.0 mm.
  • the wire rod for a spring was subjected to the soft annealing (while being kept at 660°C for 2 hours), and then a surface part of the wire rod for a spring was shaved by 0.15 mm to thereby remove a decarburized layer.
  • the wire rod for a spring was heated at a temperature of 900°C or higher in a neutral gas atmosphere to thereby be austenitized. Then, a lead-patenting process (heating temperature: 980°C, lead furnace temperature: 620°C) was performed on the wire rod for a spring to take place pearlite transformation. Thereafter, the wire rod for a spring was subjected to the cold drawing into a wire having a diameter of 4.1 mm, and then to the oil tempering process under the conditions appropriate for the respective components of the wire (heating temperature: 900°C to 1,000°C, quenching oil temperature: 60°C, tempering temperature: 400 to 500°C), thus fabricating the wire for a spring. The wire for a spring was used to be cold-formed, thereby producing a spring (average coil diameter: 24.60 mm, free height: 46.55 mm, the effective number of turns: 5.75).
  • the carburized layer depth in each test sample was determined by measuring the carbon content in the coil spring. Specifically, as shown in Fig. 1 , four lines were drawn at intervals of 90 degrees from the center of the cross section of the steel wire forming the coil spring in each test sample. Then, the depth on each line in which the carbon (C) content (%) became substantially equal to that of carbon added to the steel was measured in the sample. Measurements in this test were shown in the "carburized layer depth" column in the table. In the present invention, the samples having the carburized layer depth in a range from 0.30 mm to 1.00 mm were rated as "pass".
  • the hardness (Hv) of the coil spring in each test sample was measured using the Vickers hardness tester. Specifically, as shown in Fig. 1 , the hardness of the coil spring in each sample was measured on the four lines drawn at intervals of 90 degrees from the positions at 1/4 ⁇ diameter D (d/4) of the cross section of the steel wire that forms the coil spring in each test sample (test load: 10 kgf). Then, an average of these measurements was determined. The average Vickers hardness was shown in the "Vickers hardness" column. In the present invention, the samples having the Vickers hardness of 600 to 750 were rated as "pass".
  • a method for measuring a crystal grain size of the prior austenite crystals in the coil spring was as follows. Specifically, first, as shown in Fig. 2 , the cross section of the coil spring in each sample was partitioned at intervals 45 degrees from the center thereof into eight regions. In the respective regions, the crystal grain size of the prior austenite crystal in the depth of 0.3 mm from the surface of the steel wire forming the coil spring in the direction to the center thereof was observed and measured in each test sample with an optical microscope (at 400-fold magnification) in accordance with JIS G 0551 (size of the field of view: 250 ⁇ m x 200 ⁇ m). The average of measurements was shown in the "average crystal grain size number of prior ⁇ -crystal" column. In the present invention, the samples having the average crystal grain size number of the prior austenite crystals of 11.0 to 15.0 were rated as pass.
  • a method for determining a difference in grain size number between the prior austenite crystals in the coil spring was as follows. Some samples had the above-mentioned measured crystal grain size number of the prior austenite crystal that differed by three or more from the grain size number observed at the maximum frequency. These samples were determined to contain duplex-grains. The samples where the duplex-grain was present were defined as "present” in the "Duplex-grain” column of the table, while the samples where the duplex-grain was not present were defined as "not present”.
  • a shear stress with the maximum shear stress ( ⁇ max ) of 588 ⁇ 441 MPa was applied to each test sample obtained in the above way, and the test sample was subjected to the fatigue test up to sixty million times.
  • the test samples to which the shear stress could be applied sixty million times (that is, which were not broken) were defined as the "A” determination (which means excellent fatigue resistance), and then these samples were shown as "> 6000" in the table.
  • the test samples to which the shear stress could not be applied sixty million times (that is, when the test sample was broken midway) were defined as the "F” determination (which means the failure of the test, or inferior fatigue resistance), and then the number of application of the shear stress that caused the breakage of the sample was recorded in the table.
  • Samples Nos. 1 to 7 are examples that met the requirements defined by the present invention (chemical composition, crystal grain size, carburized layer depth, and Vickers hardness). All the coil springs of samples Nos. 1 to 7 are found to have a long fracture lifetime with a high load applied thereto (A determination) and an excellent fatigue resistance.
  • samples Nos. 8 to 13 did not satisfy the requirements defined by the present invention, including the chemical composition and the preferable manufacturing conditions, and thus could not ensure the predetermined crystal grain size, carburizing depth, Vickers hardness, and the like, leading to the result of inferior fatigue resistance (F determination).
  • Samples Nos. 8 and 9 are examples in which the same type of steel was used. These are the examples simulating Example No. 4 disclosed in Patent Document 1 (steel type of A and carburization condition L in Patent Document 1). Samples Nos. 8 and 9 are the examples in which the amount of added V was small, and the amount of added Cr was large. Since the diffusion coefficient of C was drastically reduced, the carburized layer was shallow. In particular, in sample No. 8, the carburization temperature was low, so that the adequate carburizing depth could not be obtained, resulting in worse fatigue resistance. Although in sample No. 9, the processing was performed at the carburization temperature recommended by the present invention, the amount of added V was small, which could not exhibit the sufficient effect of making the crystal grains of the prior austenite crystals finer. As a result, the duplex-grains were generated to degrade the fatigue resistance.
  • Sample No. 11 is an example in which the amounts of added C and Si were small, and thus the carburization temperature was low. In this example, the predetermined Vickers hardness was not obtained, thereby degrading the fatigue resistance.

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

Claims (2)

  1. Ressort hélicoïdal en acier, constitué de (en % en masse, il en va de même pour une composition chimique) : C : 0,40 à 0,70 % ; Si : 1,50 à 3,50 % ; Mn : 0,30 à 1,50 % ; Cr: 0,10 à 1,50 % ; V : 0,50 à 1,00 % ; et Al : 0,01 % ou moins (excepté 0 %),
    éventuellement constitué en outre de : Ni : 1,50 % ou moins (excepté 0 %) ; et/ou Nb : 0,50% ou moins (excepté 0 %),
    le reste étant du fer et les impuretés inévitables, y compris : P : 0,016 % ou moins ; et S : 0,015 % ou moins,
    un chiffre de la taille moyenne de grain cristallin des précédents cristaux d'austénite à une profondeur de 0,3 mm de la surface étant compris entre 11,0 et 15,0, tandis qu'une différence entre les chiffres de la taille de grain des précédents cristaux d'austénite étant dans une plage inférieure à 3 par rapport au chiffre de la taille de grain le plus fréquent, et une couche carburée étant prévue à une profondeur de 0,30 à 1,00 mm de la surface, tandis qu'une dureté Vickers moyenne est de 600 à 750 à une position à une profondeur de (1/4) x diamètre dans la direction de la profondeur à partir de la surface.
  2. Procédé de fabrication du ressort hélicoïdal selon la revendication 1, qui comprend l'étape consistant à effectuer un processus de carburation sous vide à une température comprise entre 1 000 °C et 1 100 °C, suivie d'une étape consistant en continu à refroidir au gaz ou rapidement à l'huile jusqu'à une température égale ou inférieure à la température de transformation de l'A1.
EP14823237.4A 2013-07-09 2014-07-08 Ressort hélicoïdal et procédé de fabrication de ce dernier Active EP3020841B1 (fr)

Applications Claiming Priority (2)

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JP2013143514A JP5941439B2 (ja) 2013-07-09 2013-07-09 コイルばね、およびその製造方法
PCT/JP2014/068123 WO2015005311A1 (fr) 2013-07-09 2014-07-08 Ressort hélicoïdal et procédé de fabrication de ce dernier

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EP (1) EP3020841B1 (fr)
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KR (1) KR101789944B1 (fr)
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WO (1) WO2015005311A1 (fr)

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CN106939372B (zh) * 2017-02-14 2018-12-18 江西昌河航空工业有限公司 一种弹簧的制造方法
JP7165522B2 (ja) * 2018-07-10 2022-11-04 日本発條株式会社 圧縮コイルばねおよびその製造方法
DE112020000034T5 (de) * 2019-07-01 2022-03-24 Sumitomo Electric Industries, Ltd. Stahldraht und Feder

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EP0643148B1 (fr) * 1993-03-12 2002-06-19 Nippon Steel Corporation Materiau en acier pour partie d'arbre trempee par induction et partie d'arbre ainsi produite
JPH0959745A (ja) * 1995-08-24 1997-03-04 Daido Steel Co Ltd 結晶粒粗大化防止鋼
JP2003213372A (ja) * 2002-01-25 2003-07-30 Sumitomo Denko Steel Wire Kk ばね用鋼線およびばね
CN100445408C (zh) * 2003-03-28 2008-12-24 株式会社神户制钢所 加工性优异的高强度弹簧用钢丝以及高强度弹簧
JP5114665B2 (ja) * 2006-03-31 2013-01-09 新日鐵住金株式会社 高強度ばね用熱処理鋼
JP5476597B2 (ja) * 2010-03-04 2014-04-23 株式会社神戸製鋼所 高強度中空ばね用シームレス鋼管
JP5693126B2 (ja) * 2010-10-06 2015-04-01 日産自動車株式会社 コイルばね及びその製造方法
JP5711539B2 (ja) * 2011-01-06 2015-05-07 中央発條株式会社 腐食疲労強度に優れるばね
JP5064590B1 (ja) * 2011-08-11 2012-10-31 日本発條株式会社 圧縮コイルばねおよびその製造方法

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EP3020841A1 (fr) 2016-05-18
KR101789944B1 (ko) 2017-10-25
CN105358726B (zh) 2017-06-09
JP2015017288A (ja) 2015-01-29
CN105358726A (zh) 2016-02-24
JP5941439B2 (ja) 2016-06-29
US20160160306A1 (en) 2016-06-09
EP3020841A4 (fr) 2017-03-29
WO2015005311A1 (fr) 2015-01-15
KR20160018720A (ko) 2016-02-17

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