EP3336214B1 - Ressort à haute résistance, procédé de fabrication dudit ressort, acier destiné à un ressort à haute résistance et procédé de production dudit acier - Google Patents

Ressort à haute résistance, procédé de fabrication dudit ressort, acier destiné à un ressort à haute résistance et procédé de production dudit acier Download PDF

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EP3336214B1
EP3336214B1 EP17835988.1A EP17835988A EP3336214B1 EP 3336214 B1 EP3336214 B1 EP 3336214B1 EP 17835988 A EP17835988 A EP 17835988A EP 3336214 B1 EP3336214 B1 EP 3336214B1
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Prior art keywords
compound
steel
equal
less
spring
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German (de)
English (en)
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EP3336214A1 (fr
EP3336214A4 (fr
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Motoki Watanabe
Koki MINOGUCHI
Hiroyuki Oishi
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Mitsubishi Steel Mfg Co Ltd
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Mitsubishi Steel Mfg Co Ltd
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/56—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.7% by weight of carbon
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to a high strength spring and a method of manufacturing the same, and a steel for a high strength spring and a method of manufacturing the same.
  • High strength springs are used for automobiles and the like.
  • the high strength spring has high strength
  • the high strength spring can be formed by a thin wire, and can contribute to lightening of an automobile, and also improve fuel consumption of the automobile.
  • the strength of the spring is increased, fatigue strength, hydrogen embrittlement resistance, delayed fracture resistance and the like under corrosive environment are lowered.
  • a steel for a spring disclosed in Patent Document 1 is configured to capture hydrogens entering the steel from external environment by a hydrogen trap site made of a precipitate containing V and the like to suppress diffusion of the hydrogen in the steel.
  • JP2016125119 A relates to a high strength hollow seamless steel pipe for springs, and more particularly to a seamless steel pipe suitable for manufacturing a hollow suspension made of steel and the like used in automobiles and the like.
  • Patent Document 1 Japanese Laid-open Patent Publication No. 2001-288539
  • the precipitates contain V and the like.
  • the present invention is made in light of the above problems, and mainly provides a high strength spring which has good hydrogen embrittlement resistance, corrosion durability and delayed fracture resistance.
  • a high strength spring containing, by mass%, C: 0.40 to 0.50%, Si: 1.00 to 3.00%, Mn: 0.30 to 1.20%, Ni: 0.05 to 0.50%, Cr: 0.35 to 1.50%, Mo: 0.03 to 0.50%, Cu: 0.05 to 0.50%, Al: 0.005 to 0.100%, V: 0.05 to 0.50%, Nb: 0.005 to 0.150%, N: 0.0100 to 0.0200%, P: limited to be less than or equal to 0.015%, S: limited to be less than or equal to 0.010%, and the balance of Fe and inevitable impurities, wherein a Nb-compound including at least one of Nb-carbide, Nb-nitride and Nb-carbonitride is included, and wherein a V-compound including at least one of V-carbide and V-carbonitride that is precipitated around the Nb-compound is included, wherein the number of the complex precipitates, formed by the
  • a high strength spring and a steel for a high strength spring are provided which have good hydrogen embrittlement resistance, corrosion durability and delayed fracture resistance.
  • a high strength spring is used for, for example, a suspension spring of an automobile.
  • “high strength” means that its tensile strength is greater than or equal to 1800 MPa.
  • the shape of a test piece used in a measurement of tensile strength is based on the shape of a No. 4 test piece described in Japan Industrial Standard (JIS Z2241).
  • the high strength spring may be a coil spring.
  • the coil spring is manufactured by hot spring forming, cold spring forming or the like. According to the hot spring forming, after a wire is hot formed into a coil shape, a quenching process and a tempering process are performed. Further, according to the cold spring forming, after performing a quenching process and a tempering process on a wire, the wire is cold formed into a coil shape.
  • the high strength spring may be a leaf spring or the like.
  • the embodiment of the high strength spring is not specifically limited. Further, the purpose for the high strength spring to be used is not limited to a suspension device of an automobile as well.
  • the high strength spring is made of a steel for a high strength spring.
  • the steel for a high strength spring is obtained by performing a quenching process and a tempering process, and has a martensitic structure obtained by the quenching process. Before the quenching process, a pearlite structure is dominant, an austenite structure is dominant at quenching temperature, and the martensitic structure is dominant after the quenching process.
  • the steel for a high strength spring may have a shape of a spring (a coil shape, for example).
  • the steel for a high strength spring may have the shape of the spring, or a shape (a stick shape, for example) before being shaped into the shape of the spring.
  • the steel for a high strength spring contains, by mass%, C: 0.40 to 0.50%, Si: 1.00 to 3.00%, Mn: 0.30 to 1.20%, Ni: 0.05 to 0.50%, Cr: 0.35 to 1.50%, Mo: 0.03 to 0.50%, Cu: 0.05 to 0.50%, Al: 0.005 to 0.100%, V: 0.05 to 0.50%, Nb: 0.005 to 0.150% and N: 0.0100 to 0.0200%, wherein P is limited to be less than or equal to 0.015% and S is limited to be less than or equal to 0.010%, and contains the balance of Fe and inevitable impurities.
  • each component is described. For the description of each component, "%" means mass%.
  • C is an element effective for increasing strength of the steel.
  • the content of C is 0.40 to 0.50%.
  • strength necessary for a spring cannot be obtained.
  • the content of C exceeds 0.50%, corrosion durability is lowered.
  • Si is an element effective for improving strength of the steel by being solid-dissolved in ferrite.
  • the content of Si is 1.00 to 3.00%. When the content of Si is less than 1.00%, strength necessary for a spring cannot be obtained. Meanwhile, when the content of Si exceeds 3.00%, when the spring is hot formed, decarbonizing at a surface easily occurs and durability of the spring is lowered.
  • Mn is an element effective for improving hardenability of the steel.
  • the content of Mn is 0.30 to 1.20%.
  • the content of Mn is less than 0.30%, an effect of improving the hardenability cannot be sufficiently obtained.
  • the content of Mn exceeds 1.20%, toughness is deteriorated.
  • Ni is an element necessary for increasing corrosion durability of the steel.
  • the content of Ni is 0.05 to 0.50%. When the content of Ni is less than 0.05%, an expected effect of increasing the corrosion durability of the steel cannot be sufficiently obtained.
  • an upper limit of the content of Ni is 0.50%.
  • Cr is an element effective for increasing strength of the steel. The content of Cr is 0.35 to 1.50%. When the content of Cr is less than 0.35%, an expected effect of increasing the strength of the steel cannot be sufficiently obtained. Meanwhile, when the content of Cr exceeds 1.50%, toughness is easily deteriorated.
  • Mo is an element that ensures hardenability of the steel, and increases strength and toughness of the steel.
  • the content of Mo is 0.03 to 0.50%. When the content of Mo is less than 0.03%, an expected effect of adding Mo cannot be sufficiently obtained. Meanwhile, when the content of Mo exceeds 0.50%, the effect of adding Mo is saturated.
  • Cu is a component that increases corrosion durability.
  • the content of Cu is 0.05 to 0.50%.
  • the content of Cu is less than 0.05%, an effect of increasing the corrosion durability cannot be sufficiently obtained. Meanwhile, when the content of Cu exceeds 0.50%, cracking and the like may occur during hot rolling.
  • Al is an element necessary as a deoxidizer of the steel and for adjusting an austenite grain size.
  • the content of Al is 0.005 to 0.100%. When the content of Al is less than 0.005%, the crystal grain cannot be finely formed. Meanwhile, when the content of Al exceeds 0.100%, castability is easily lowered.
  • V is an element effective for increasing strength of the steel, and suppressing hydrogen embrittlement.
  • the content of V is 0.05 to 0.50%. When the content of V is less than 0.05%, an expected effect of adding V cannot be sufficiently obtained. Meanwhile, when the content of V exceeds 0.50%, carbide that does not dissolve in austenite increases, and spring characteristics are deteriorated.
  • Nb is an element that increases strength and toughness of the steel by finely forming a crystal grain and precipitating fine carbide. Further, Nb is an element that contributes to fine dispersion of a V-compound including at least one of V-carbide and V-carbonitride (hereinafter, simply referred to as a "V-compound"), and increases hydrogen embrittlement resistance.
  • the content of Nb is 0.005 to 0.150%. When the content of Nb is less than 0.005%, an expected effect of adding Nb cannot be sufficiently obtained. Meanwhile, when the content of Nb exceeds 0.150%, carbide that does not dissolve in austenite increases, and spring characteristics are deteriorated.
  • N is an element that forms A1N or NbN by bonding with Al or Nb, and has an effect in making austenite grain size fine. With this fine structure, toughness is improved.
  • the content of N is 0.0100 to 0.0200%. When the content of N is greater than or equal to 0.0100%, a sufficient effect of improving toughness can be obtained. Meanwhile, if N is excessively added, bubbles may be generated at a surface of a steel ingot in solidification, or castability of the steel may be deteriorated, an upper limit of the content of N is 0.0200%.
  • P becomes a factor to lower an impact value by being precipitated at an austenite grain boundary to embrittle the grain boundary.
  • the content of P is limited to be less than or equal to 0.015%.
  • S exists as an inclusion of MnS in the steel, and becomes a factor to lower fatigue life and corrosion durability.
  • the inclusion means something that is already formed when the steel is molten.
  • the content of S is limited to be less than or equal to 0.010%, preferably, less than or equal to 0.005%.
  • the steel for a high strength spring is manufactured by having the V-compound solid-dissolved in iron at the quenching temperature, and thereafter, precipitating the V-compound around the Nb-compound that is finely dispersed in the steel.
  • the steel for a high strength spring includes the Nb-compound and the V-compound precipitated around the Nb-compound.
  • the V-compound may not completely surround a periphery of the Nb-compound or may completely surround a periphery of the Nb-compound.
  • the Nb-compound may exist inside the V-compound.
  • the Nb-compound is a precipitate that is precipitated in iron while a molten steel is being solidified.
  • the Nb-compound includes at least one of Nb-nitride, Nb-carbide and Nb-carbonitride.
  • the Nb-compound is finely dispersed in the steel before the quenching process, is not solid-dissolved in iron at the quenching temperature, and becomes a starting point of precipitation of the V-compound in quenching from the quenching temperature or in the tempering process.
  • Nb-nitride that is more finely dispersed is preferably used compared with Nb-carbide and Nb-carbonitride.
  • the V-compound exists in the steel as a coarse precipitate before the quenching process, the V-compound is solid-dissolved in iron at the quenching temperature, and thereafter, is precipitated from the Nb-compound as the starting point.
  • the Nb-compound is finely dispersed, the V-compound that is precipitated from the Nb-compound as the starting point can be finely dispersed.
  • the quenching temperature is set to be greater than or equal to 950 °C and less than or equal to 1000 °C in order for the V-compound to be solid-dissolved in iron at the quenching temperature.
  • Such quenching temperature is higher than dissolution temperature at which the V-compound is solid-dissolved in iron, and when the content of V is less than or equal to 0.50% as described above, the V-compound is completely solid-dissolved in iron according to the calculation of a solubility product.
  • the quenching temperature is high temperature, in order to suppress the crystal grain to be coarse, appropriate amounts of Nb, Al, N and the like are added. With this, lowering of toughness can be suppressed, and lowering of delayed fracture resistance can be suppressed as well. Therefore, the steel for a high strength spring which has good delayed fracture resistance can be obtained.
  • a complex precipitate is formed by the Nb-compound and the V-compound precipitated around the Nb-compound.
  • An average grain size of the complex precipitate may be greater than or equal to 0.01 ⁇ m and less than or equal to 1 ⁇ m.
  • the number of the complex precipitates per unit may be greater than or equal to 100 / mm 2 and less than or equal to 100000 / mm 2 .
  • the average grain size and the number per unit are measured using a SEM (Scanning Electron Microscope), for example.
  • the average grain size is obtained by measuring each equivalent area diameter (diameter) of 100 complex precipitates, and calculating an average value of the measured values.
  • the number per unit is obtained by measuring the number of the complex precipitates those exist at a region whose total area is 15 mm 2 , and dividing the number by the total area.
  • the content of C is limited to be less than or equal to 0.5%.
  • the tempering temperature is limited to be less than 390 °C. Therefore, the steel for a high strength spring which has good corrosion durability and high strength can be obtained.
  • a lower limit of the tempering temperature is set to be 250 °C, more preferably, to be 300 °C.
  • the steel for a high strength spring includes 0.0100 to 0.0200% of N.
  • the steel for a high strength spring contains appropriate amounts of Nb and Al, and N is detoxified by precipitating NbN and AlN instead of N. With this, lowering of toughness can be suppressed, and lowering of delayed fracture resistance can be suppressed as well. Thus, the steel for a high strength spring which has good delayed fracture resistance can be obtained.
  • a quenching process and a tempering process were performed on a steel having a composition as follows, and a rotating bending fatigue test piece and a hydrogen embrittlement test piece were manufactured by machining.
  • the quenching temperature was 950 °C, and its retention time was 30 minutes. Oil cooling was used to cool the steel from the quenching temperature.
  • the tempering temperature was 360 °C, and its retention time was 1 hour. Air cooling was used to cool the steel from the tempering temperature.
  • Vickers hardness of the steel after the tempering process was 590 Hv.
  • Fig. 1-(a) to Fig. 1-(e) are SEM images of a part of a cross-section of the steel after the tempering process in example 1
  • Fig. 2-(a) to Fig. 2-(e) are SEM images of another part of the cross-section of the steel after the tempering process in example 1.
  • Fig. 1-(a) and Fig. 2-(a) are backscattered electron images
  • Fig. 1-(b) and Fig. 2-(b) are characteristic X ray maps of Nb
  • Fig. 1-(c) and Fig. 2-(c) are characteristic X ray maps of N
  • 2-(a) are images of reflected electrons of electron beam that rebound near the cross-section of the steel, those images express the size of observed surfaces as they are.
  • the characteristic X ray maps of Fig. 1-(b) to Fig. 1-(e) and Fig. 2-(b) to Fig. 2-(e) are images of characteristic X rays generated when the electron beam enters the steel from the cross-section of the steel. Further, a threshold value is provided for intensity of the characteristic X ray to be detected. Thus, the images of the characteristic X ray maps are different from the size that is observed at the observed surface.
  • V-compound was precipitated such that to surround the Nb-compound after the tempering process in the steel of example 1.
  • test piece was based on the shape of a No. 1 test piece described in Japan Industrial Standard (JIS Z2274).
  • the test piece has a constriction portion called a parallel part at a center portion of a round bar.
  • the diameter of both end parts was 15 mm
  • the diameter of the parallel part was 8 mm
  • the length of the parallel part was 20 mm.
  • the diameter of both end parts was 10 mm
  • the diameter of the parallel part was 4 mm
  • the length of the parallel part was 15 mm.
  • comparative example 1 a quenching process and a tempering process were performed on a steel having a composition as follows, and a rotating bending fatigue test piece and a hydrogen embrittlement test piece were manufactured by machining.
  • the quenching temperature was 900 °C, and its retention time was 30 minutes. Oil cooling was used to cool the steel from the quenching temperature.
  • the tempering temperature was 420 °C, and its retention time was 1 hour. Air cooling was used to cool the steel from the tempering temperature.
  • Vickers hardness of the steel after the tempering process was 570 Hv.
  • test pieces were the same as those of the test pieces of example 1.
  • Fig. 3 illustrates results of the rotating bending fatigue test of example 1 and comparative example 1.
  • a solid line illustrates the result of the rotating bending fatigue test of example 1
  • a broken line illustrates the result of the rotating bending fatigue test of comparative example 1.
  • the non-breaking stress of the test piece of example 1 was 325 MPa, while the non-breaking stress of the test piece of comparative example 1 was 240 MPa. Thus, it was confirmed that the steel of example 1 had good hydrogen embrittlement resistance, corrosion durability and delayed fracture resistance compared with the steel of comparative example 1.
  • a diffusible hydrogen amount of the test piece was measured.
  • the test piece was heated to increase temperature of the test piece at constant speed, the amount of hydrogen discharged from the test piece was continuously measured by a gas chromatography method, and the diffusible hydrogen amount was obtained from its profile.
  • the hydrogen discharged at temperature less than 300 °C is diffusible hydrogen
  • the hydrogen discharged at temperature greater than or equal to 300 °C is non-diffusible hydrogen. Discharging of the diffusible hydrogen is almost finished before the temperature of the test piece reaches 220 °C, and when the temperature of the test piece exceeds 400 °C, the non-diffusible hydrogen is started to be discharged.
  • the hydrogen captured at the hydrogen trap site is not discharged at the temperature less than 300 °C.
  • the diffusible hydrogen amount of the test piece of example 1 was 0.36 mass ppm, while the diffusible hydrogen amount of the test piece of comparative example 1 was 1.87 mass ppm. Thus, it was confirmed that the steel of example 1 had more hydrogen trap sites and had good hydrogen embrittlement resistance compared with the steel of comparative example 1.
  • example 2 a quenching process and a tempering process were performed on a steel having a composition same as that of the steel of example 1, and a tensile strength test piece was manufactured by machining to conduct a tensile test.
  • the quenching temperature was 950 °C, and its retention time was 30 minutes. Oil cooling was used to cool the steel from the quenching temperature.
  • the tempering temperature was 380 °C or 350 °C, and its retention time was 1 hour. Air cooling was used to cool the steel from the tempering temperature.
  • the shape of the tensile test piece was based on the shape of a No. 4 test piece described in Japan Industrial Standard (JIS Z2241).
  • Table 1 TEMPERING TEMPERATURE [°C] TENSILE STRENGTH [MPa] 0.2% YIELD STRENGTH [MPa] BREAKING ELONGATION [%] DRAWING [%] HARDNESS [Hv] 380 1973 1765 14 50 584 350 2055 1827 14 49 601
  • a steel having a composition same as that of the steel of example 1 and example 2 was hot formed into a coil shape. Thereafter, a quenching process, a tempering process, shot peening and setting were performed on the obtained component to manufacture a coil spring. Thereafter, a durability test of the obtained coil spring was conducted.
  • the quenching temperature was 990 °C, and its retention time was 20 minutes. Oil cooling was used to cool the coil spring from the quenching temperature.
  • the tempering temperature was 360 °C, and its retention time was 1 hour. Air cooling was used to cool the coil spring from the tempering temperature. Vickers hardness of the coil spring after the tempering process was 580 Hv.
  • a steel having a composition same as that of the steel of comparative example 1 was hot formed into a coil shape similarly as example 3, and a component having a shape same as that of example 3 was obtained. Thereafter, a quenching process, a tempering process, shot peening and setting were performed on the obtained component, and a coil spring having the same shape as that of example 3 was manufactured. Thereafter, a durability test of the obtained coil spring was conducted.
  • the quenching temperature was 940 °C, and its retention time was 20 minutes. Oil cooling was used to cool the coil spring from the quenching temperature.
  • the tempering temperature was 420 °C, and its retention time was 1 hour. Air cooling was used to cool the coil spring from the tempering temperature. Vickers hardness of the coil spring after the tempering process was 560 Hv.
  • the stress amplitudes were 735 MPa ⁇ 620 MPa (maximum stress: 1355 MPa, minimum stress: 115 MPa) and 735 MPa ⁇ 550 MPa (maximum stress: 1285 MPa, minimum stress: 185 MPa).
  • the stress amplitudes were 735 MPa ⁇ 525 MPa (maximum stress: 1260 MPa, minimum stress: 210 MPa) and 735 MPa ⁇ 500 MPa(maximum stress: 1235 MPa, minimum stress: 235 MPa).
  • Fig. 4 illustrates results of the durability test of example 3 and comparative example 2.
  • a solid line illustrates the result of the durability test of example 3
  • a broken line illustrates the result of the durability test of comparative example 2.

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Claims (4)

  1. Ressort à haute résistance contenant, en % en masse, C: 0,40 à 0,50%, Si: 1,00 à 3,00%, Mn: 0,30 à 1,20%, Ni: 0, 05 à 0,50%, Cr: 0,35 à 1,50%, Mo: 0, 03 à 0,50%, Cu: 0, 05 à 0,50%, Al:0,005 à 0,100%, V: 0, 05 à 0,50%, Nb: 0,005 à 0,150%, N : 0,0100 à 0,0200%, P : limité à 0,015% ou moins, S: limité à 0,010% ou moins, le reste étant du Fe et des impuretés inévitables,
    dans lequel un composé à base de Nb contenant au moins l'un parmi le carbure de Nb, le nitrure de Nb et le carbonitrure de Nb est inclus, et
    dans lequel un composé à base de V contenant au moins l'un parmi le carbure de V et le carbonitrure de V qui est précipité autour du composé à base de Nb est inclus, et dans lequel le nombre des précipités complexes, formés par le composé à base de Nb et le composé à base de V précipité autour du composé à base de Nb, par unité est supérieur ou égal à 100/mm2 et inférieur ou égal à 100 000/mm2.
  2. Procédé de fabrication d'un ressort à haute résistance, le procédé comprenant :
    la mise en œuvre d'un procédé de trempe dans lequel la température de trempe est supérieure ou égale à 950 °C et inférieure ou égale à 1000 C, et d'un procédé dans lequel la température de revenu est supérieure ou égale à 250 C et inférieure à 390C, sur un acier contenant, en % en masse, C: 0,40 à 0,50%, Si: 1,00 à 3,00%, Mn: 0,30 à 1,20%, Ni: 0,05 à 0,50%, Cr: 0,35 à 1,50%, Mo: 0,03 à 0,50%, Cu: 0,05 à 0,50%, Al: 0,005 à 0,100%, V: 0,05 à 0,50%, Nb: 0,005 à 0,150%, N: 0,0100 à 0,0200%, P: limité à 0,015% ou moins, S: limité à 0,010% ou moins, le reste étant du Fe et des impuretés inévitables,
    dans lequel un composé à base de V contenant au moins l'un parmi le carbure de V et le carbonitrure de V est dissous en solution solide dans du Fe à la température de trempe, et ensuite le composé à base de V est précipité autour d'un composé du Nb contenant au moins l'un parmi le carbure de Nb, le nitrure de Nb et le carbonitrure de Nb, et
    dans lequel le nombre des précipités complexes, formés par le composé à base de Nb et le composé à base de du V précipité autour du composé du Nb, par unité est supérieur ou égal à 100/mm2 et inférieur ou égal à 100 000/mm2.
  3. Acier pour ressort à haute résistance contenant, en % en masse, C: 0,40 à 0,50 %, Si: 1,00 à 3,00%, Mn: 0,30 à 1,20%, Ni: 0,05 à 0,50%, Cr: 0,35 à 1,50%, Mo: 0,03 à 0,50%, Cu: 0, 05 à 0,50%, Al: 0, 005 à 0,100%, V: 0,05 à 0,50%, Nb : 0,005 à 0,150%, N: 0,0100 à 0,0200%, P: limité à 0,015% ou moins, S: limité à 0,010% ou moins, le reste étant du Fe et des impuretés inévitables,
    dans lequel un composé du Nb contenant au moins l'un parmi le carbure de Nb, le nitrure de Nb et le carbonitrure de Nb est inclus, et
    dans lequel un composé du V contenant au moins l'un parmi le carbure de V et le carbonitrure de V qui est précipité autour du composé du Nb est inclus, et dans lequel le nombre des précipités complexes, formés par le composé du Nb et le composé du V précipité autour du composé du Nb, par unité est supérieur ou égal à 100/mm2 et inférieur ou égal à 100 000/mm2.
  4. Procédé de fabrication d'un acier pour ressort à haute résistance, le procédé comprenant :
    la mise en œuvre d'un procédé de trempe dans lequel la température de trempe est supérieure ou égale à 950 °C et inférieure ou égale à 1000 C, et d'un procédé de revenu dans lequel la température de revenu est supérieure ou égale à 250 C et inférieure à 390 C, sur un acier contenant, en % en masse, C: 0,40 à 0,50%, Si: 1,00 à 3,00%, Mn: 0,30 à 1,20%, Ni: 0, 05 à 0,50%, Cr: 0,35 à 1,50%, Mo: 0, 03 à 0,50%, Cu: 0, 05 à 0,50%, Al: 0,005 à 0,100%, V: 0,05 à 0,50%, Nb: 0,005 à 0,150%, N: 0,0100 à 0,0200%, P: limité à 0,015% ou moins, S: limité à 0,010% ou moins, le reste étant du Fe et des impuretés inévitables,
    dans lequel un composé à base de V contenant au moins l'un parmi le carbure de V et le carbonitrure de V est dissous en solution solide dans du Fe à la température de trempe, et ensuite le composé à base de V est précipité autour d'un composé à base de Nb contenant au moins l'un parmi le carbure de Nb, le nitrure de Nb et le carbonitrure de Nb, et
    dans lequel le nombre des précipités complexes, formés par le composé à base de Nb et le composé à base de V précipité autour du composé à base de Nb, par unité est supérieur ou égal à 100/mm2 et inférieur ou égal à 100 000/mm2.
EP17835988.1A 2016-10-19 2017-06-01 Ressort à haute résistance, procédé de fabrication dudit ressort, acier destiné à un ressort à haute résistance et procédé de production dudit acier Active EP3336214B1 (fr)

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PCT/JP2017/020501 WO2018074003A1 (fr) 2016-10-19 2017-06-01 Ressort à haute résistance, procédé de fabrication dudit ressort, acier destiné à un ressort à haute résistance et procédé de production dudit acier

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JP4464524B2 (ja) 2000-04-05 2010-05-19 新日本製鐵株式会社 耐水素疲労特性の優れたばね用鋼、およびその製造方法
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JP5064060B2 (ja) * 2007-02-22 2012-10-31 新日本製鐵株式会社 高強度ばね用鋼線及び高強度ばね並びにそれらの製造方法
JP5146063B2 (ja) * 2007-04-12 2013-02-20 新日鐵住金株式会社 耐内部疲労損傷特性に優れた高強度鋼及びその製造方法
JP2016125119A (ja) * 2015-01-07 2016-07-11 株式会社神戸製鋼所 ばね用中空シームレス鋼管

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BR112018003077B1 (pt) 2023-01-17
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