WO2004055226A1 - Fil d'acier pour ressort - Google Patents

Fil d'acier pour ressort Download PDF

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Publication number
WO2004055226A1
WO2004055226A1 PCT/JP2003/015689 JP0315689W WO2004055226A1 WO 2004055226 A1 WO2004055226 A1 WO 2004055226A1 JP 0315689 W JP0315689 W JP 0315689W WO 2004055226 A1 WO2004055226 A1 WO 2004055226A1
Authority
WO
WIPO (PCT)
Prior art keywords
tempering
quenching
mass
spring
wire
Prior art date
Application number
PCT/JP2003/015689
Other languages
English (en)
Japanese (ja)
Inventor
Yoshiro Fujino
Nozomu Kawabe
Norihito Yamao
Hiromu Izumida
Teruyuki Murai
Original Assignee
Sumitomo (Sei) Steel Wire Corp.
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sumitomo (Sei) Steel Wire Corp. filed Critical Sumitomo (Sei) Steel Wire Corp.
Publication of WO2004055226A1 publication Critical patent/WO2004055226A1/fr

Links

Classifications

    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • 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
    • 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
    • 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
    • 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

Definitions

  • the present invention relates to a spring steel wire having a quenched and tempered martensite structure and a spring manufactured from the steel wire.
  • the present invention relates to a high-strength, high-toughness spring steel wire and spring suitable for an engine valve spring of an automobile or a spring used in a transmission.
  • Patent Document 1 Japanese Patent Application Laid-Open No. 2-247354
  • Patent Patent Document 2 Japanese Patent Application Laid-Open No. 2000-313938 (Claims, see FIG. 1)
  • Patent Document 3 Japanese Patent Application Laid-Open No.
  • Patent Document 4 JP-A-2002-194496 (Claims, see Table 1)
  • Patent Document 5 JP-A-2002-180195, (Claims, Table 1)
  • Non-Patent Document 1 Spring Technical Meeting, Autumn Meeting, 1994, "8 Influence of Surface Defects on Fatigue Strength of High Fatigue Strength Spring," Jan. 1994, pp. 29-32 Gachi Has been.
  • Nitriding usually hardens the wire surface and increases the surface hardness, but reduces the hardness inside the wire. Also, by performing the nitriding treatment in addition to the strain relief annealing after the spring working, the hardness inside the wire is more likely to decrease. And, since the inside of the wire is low in hardness, there is a possibility that breakage starting from the inside of the wire may occur.
  • Patent Documents 1 and 4 do not describe the nitriding treatment, and do not consider the decrease in hardness inside the wire due to the nitriding treatment.
  • Patent Document 2 defines only the hardness of the wire surface.
  • the temperature of the nitriding treatment is increased. As can be seen from the test results described below, the higher the temperature of the nitriding treatment, the lower the toughness such as drawing tends to be.
  • a main object of the present invention is to provide a spring steel wire having good balance of strength and toughness, and a spring manufactured from this steel wire. Disclosure of the invention
  • the present invention achieves the above object by defining the internal hardness after heat treatment performed after spring working and the reduction value in addition to the chemical composition, austenite crystal grain size, and residual austenite amount.
  • the spring steel wire of the present invention has the following features.
  • C 0.55 to 0.75%
  • Si 1.80 to 2.70%
  • Mn 0.1 to 0.7%
  • Cr 0.70 to 1.50%
  • V 0.05 to 0.50%
  • Mo 0.05 to 0.50%
  • W 0.05 to 0.15%
  • Nb 0.05 to 0.15%
  • Ti at least one selected from the group consisting of 0.01 to 0.20%, with the balance being Fe and unavoidable impurities
  • Tempered martensite structure obtained by quenching and tempering
  • Austenite grain size after quenching and tempering is 1.0 to 18.0 m
  • the austenite crystal grain size is the former austenite crystal grain size.
  • Residual austenite after quenching and tempering is 10% by volume or less
  • an aperture value is used as an index of toughness.
  • heat resistance is improved by solid solution strengthening by Si in the above component range and precipitation strengthening of carbides of V, Mo, W, Nb, Ti.
  • heat treatment such as strain relief annealing (tempering treatment) and nitriding treatment is performed after quenching and tempering, the hardness inside the wire is hardly reduced and high hardness can be obtained.
  • the toughness can be improved not only after quenching and tempering but also after the subsequent heat treatment. Based on this knowledge, the above chemical components are specified.
  • the hardness at a position 1/4 of the diameter from the center of the line is defined as the hardness inside the line, not as the hardness of the surface layer such as the surface of the line or near the surface of the line.
  • the position 1/4 of the diameter from the center of the line is least susceptible to the increase in hardness near the surface due to surface decarburization / nitrogen treatment, segregation of the center, etc., so it is easy to properly evaluate the internal hardness after heat treatment. .
  • the chemical components are specified as described above in order to prevent a decrease in the hardness inside the wire, but the internal hardness may also be reduced by heat treatment. Specifically, the higher the heat treatment temperature and the longer the holding time, the lower the temperature. Therefore, in order to prevent the decrease in internal hardness due to heat treatment and to obtain the effect of improving heat resistance and improving surface hardness by heat treatment such as nitriding treatment, a relatively higher temperature range than that conventionally used: Heating at 420 "C or more and 480 ° C or less is required for 2 hours or more. Therefore, in the present invention, the heat treatment conditions after quenching and tempering are specified as 420 to 480 and 2 hours or more.
  • the improvement in toughness is affected by the crystal grain size of old austenite and the amount of residual austenite. Based on this knowledge, the present invention Defines these parameters.
  • the steel wire for springs of the present invention configured based on the above findings improves toughness, reduces a decrease in internal hardness after heat treatment performed after quenching and tempering, and suppresses breakage of a spring starting from inside the wire. Can be.
  • C is an important element that determines the strength of steel. If it is less than 0.55% by mass, sufficient strength cannot be obtained, and if it exceeds 0.75% by mass, the toughness is impaired. 75 mass% or less.
  • Si is used as a deoxidizing agent during refining. Further, the solid solution in the ferrite improves heat resistance, and prevents a decrease in hardness inside the wire due to heat treatment such as strain relief annealing and nitriding after spring processing. In order to maintain heat resistance, 1.8 mass% or more is required, and if it exceeds 2.7 mass%, toughness is reduced. Therefore, the content is 1.8 mass% or more and 2.7 mass% or less. Mn: 0.1 to 0.7 mass%
  • Mn like Si
  • the lower limit of the required amount of the deoxidizing agent is set to 0.1% by mass.
  • Mn is an element that easily causes center segregation.If added excessively, Mn forms martensite in the center segregated part during the patenting process after hot rolling, which causes wire breakage during subsequent wire drawing.
  • the toughness after quenching and tempering In order to improve toughness, the amount of addition is made relatively small compared to conventional ones. Specifically, the upper limit is set to 0.7% by mass as the amount of addition to prevent a decrease in toughness. Cr: 0.7 to 1.5 mass%
  • Cr improves the hardenability of steel and increases the softening resistance after quenching and tempering, so it is effective in preventing softening during heat treatment such as tempering and nitriding after spring processing. If the addition amount is less than 0.7% by mass, the effect of preventing softening during the heat treatment is small, so the lower limit is set to 0.7% by mass as an addition amount that can provide a sufficient effect. On the other hand, if it is added in excess of 1.5% by mass, martensite is liable to be generated during patenting, causing wire breakage during wire drawing and reducing toughness after oil tempering. Therefore, the amount of Cr added is set to 1.5% by mass or less.
  • Si and Cr have an effect of improving heat resistance by forming carbides. Therefore, in the present invention, the content of Si and Cr is set relatively high to improve the heat resistance. However, the amount to be included depends on the balance with toughness. In order to obtain sufficient heat resistance, it is preferable that the atomic% of Si + the atomic% of Cr be 0.09 or more.
  • C 0.60% to 0.70% by mass
  • Si 2.20% to 2.5% by mass
  • Mn 0.2% by mass or more and 0.5% by mass or less
  • Cr 0.9% by mass or more and 1.3% by mass or less.
  • Co 0.02 to 1.00 mass%
  • Co is an element that raises the Ms point (martensite transformation start temperature). Reduces the amount of residual austenite after quenching and improves toughness after quenching and tempering. Therefore, in the present invention, it is added to further improve the toughness. In order to obtain the effect of improving toughness, it is preferable to add 0.02% by mass or more. On the other hand, even if a certain amount or more is added, the above effect cannot be improved, and Co is relatively expensive, so the upper limit is made 1.00% by mass or less. A more preferable addition amount in consideration of both improvement in toughness and cost is 0.05% by mass or more and 0.20% by mass or less.
  • T i forms carbides during tempering and has the effect of increasing softening resistance. To obtain this effect, it is preferable to add 0.01% by mass or more. However, if added in excess, high melting point non-metallic inclusions TIO may be formed and the toughness may be reduced. In consideration of the decrease in toughness due to the formation of inclusions, the content is set to 0.20% by mass or less.
  • the hardness inside the wire may be reduced, or breakage may occur from the inside of the wire.
  • the internal hardness and toughness tend to decrease as the heating temperature of the nitriding treatment increases. Therefore, in the present invention, heat resistance and toughness are improved by defining chemical components. Specifically, the hardness inside the wire is 550HV or more.
  • the grain size of the former onestenite affects the fatigue resistance.
  • the grain size is 18.0 ⁇ m or less, the fatigue characteristics are improved due to the effect of refining the crystal grains.
  • the crystal grain size of the former austenite is set to be more than 1.0 m and 18.0 m or less.
  • the crystal grain size of old austenite can be controlled by changing the heating temperature during quenching when the holding time is constant. Specifically, the particle size can be reduced by lowering the heating temperature, and can be increased by increasing the heating temperature.
  • the content of residual austenite is set to 10% by volume or less.
  • the amount of residual austenite can be controlled by specifying the chemical components as described above. ⁇ Toughness>
  • the drawn value after heat treatment performed after quenching and tempering is set to 35% or more.
  • the aperture value can be controlled by specifying the chemical composition, austenite crystal grain size, and residual austenite amount as described above.
  • the spring steel wire of the present invention is preferably used for manufacturing a spring by performing spring working after quenching and tempering, nitriding, and performing one or more shot peening.
  • the manufactured spring may be used for an engine valve spring of an automobile, an interior of a transmission, and the like.
  • wires with a diameter of 6.3 ⁇ were prepared by hot rolling. After patenting this wire, stripping, annealing, and wire drawing were performed sequentially to obtain a wire with a diameter of 3.2 mm. The wire was quenched and tempered.
  • the tensile strength was controlled by changing the tempering temperature.
  • the grain size was controlled by changing the quenching temperature.
  • the particle size is 10 Sample Nos. 4 to 6, 14, and 15 with a particle size of less than 900 m are 900, heating rate is 500 ° C / s, holding time is 2 s, and sample Nos. 2, 3, and 7-13 have a particle size of 10 to 15 zm or less.
  • the sample No. 1 having a temperature of 1000, a heating rate of 500 / s, a holding time of 2 s and an r particle size of more than 20 m was set to 1100 ° C, a heating rate of 500 / s, and a holding time of 2 s.
  • the amount of residual a and the hardness inside the wire were varied depending on the chemical composition.
  • samples ⁇ 8 to 15 that satisfy the specified chemical composition, ⁇ particle size, and residual r content have high internal hardness and excellent toughness even after heat treatment after quenching and tempering. You can see it. Also, it can be seen that the relatively low heat treatment temperature has excellent internal hardness and toughness.
  • Sample No. 1 which has a low C content and a high quenching temperature, has a low internal hardness after heat treatment.
  • Samples Nos. 3 and 7 have low heat resistance due to their low Cr and Si contents, low internal hardness after heat treatment, and small aperture values.
  • Sample No. 2 has a high residual C content due to a high C content, and has low toughness.
  • Samples Nos. 4 to 6 each had a high Si, Mn, and Cr content, resulting in poor toughness and a low drawing value.
  • the spring steel wire of the present invention by providing both the strength and the toughness in a well-balanced manner, it is possible to achieve an excellent effect that the fatigue characteristics can be improved. Therefore, the spring having excellent fatigue characteristics can be obtained by using the spring steel wire of the present invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Springs (AREA)

Abstract

L'invention concerne un fil d'acier pour ressort, qui se caractérise en ce qu'il possède la composition chimique suivante, en % en masse : 0,55 à 0,75 % de C, 1,80 à 2,70 % de Si, 0,1 à 0,7 % de Mn, 0,70 à 1,50 % de Cr, un ou plusieurs des éléments du groupe suivant : 0,05 à 0,50 % de V, 0,05 à 0,50 de Mo, 0,005 à 0,15 de W, 0,05 à 0,15 de Nb et 0,01 à 0,20 % de Ti, le solde étant constitué de Fe et des impuretés inévitables. Ledit fil présente une structure martensitique frittée formée par refroidissement suivi d'un revenu, et présente, après le refroidissement, une structure austénitique de 1,0 à 18,0 νm et une quantité d'austénite retenue d'au plus 10 % en volume. Après le traitement thermique à 420 à 480 °C pendant deux heures ou plus, après le refroidissement et le revenu, il possède une dureté en position ¼ du diamètre du fil excentré par rapport au centre du fil de 550 Hv ou moins et une réduction de surface d'au moins 35 %. Le fil d'acier de l'invention présente un excellent équilibre de résistance et de ténacité et présente ainsi des caractéristiques de fatigue améliorées.
PCT/JP2003/015689 2002-12-13 2003-12-08 Fil d'acier pour ressort WO2004055226A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2002362131A JP2004190116A (ja) 2002-12-13 2002-12-13 ばね用鋼線
JP2002-362131 2002-12-13

Publications (1)

Publication Number Publication Date
WO2004055226A1 true WO2004055226A1 (fr) 2004-07-01

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WO (1) WO2004055226A1 (fr)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1731625A1 (fr) * 2004-02-04 2006-12-13 Sumitomo (Sei) Steel Wire Corp. Fil d acier pour ressort
EP1930458A1 (fr) * 2005-08-05 2008-06-11 Sumitomo Electric Industries, Ltd. Fil revenu à l huile et son procédé de production
US20090205753A1 (en) * 2006-03-31 2009-08-20 Masayuki Hashimura High strength spring-use heat treated steel
CN101892425A (zh) * 2010-08-20 2010-11-24 武汉中磁浩源科技有限公司 一种软磁合金粉末、磁粉芯及其制备方法
CN102378823A (zh) * 2009-07-09 2012-03-14 新日本制铁株式会社 高强度弹簧用钢线
WO2015052035A1 (fr) * 2013-10-11 2015-04-16 Nv Bekaert Sa Fil d'acier à haute résistance à la traction
CN106442495A (zh) * 2016-09-18 2017-02-22 扬州大学 一种测定奥贝球铁中是否存在马氏体的热处理方法

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101287851B (zh) * 2005-08-05 2012-09-05 住友电气工业株式会社 油回火线及其制造方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH108203A (ja) * 1996-06-24 1998-01-13 Nippon Steel Corp デスケーリング性と伸線性の優れた線材
US5904787A (en) * 1995-09-01 1999-05-18 Sumitomo Electric Industries, Ltd. Oil-tempered wire and method of manufacturing the same
JP2003105498A (ja) * 2001-09-28 2003-04-09 Togo Seisakusho Corp 高強度ばねおよびその製造方法
JP2003213372A (ja) * 2002-01-25 2003-07-30 Sumitomo Denko Steel Wire Kk ばね用鋼線およびばね
JP2003306747A (ja) * 2002-04-16 2003-10-31 Sumitomo Denko Steel Wire Kk 鋼線およびその製造方法ならびにばね

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5904787A (en) * 1995-09-01 1999-05-18 Sumitomo Electric Industries, Ltd. Oil-tempered wire and method of manufacturing the same
JPH108203A (ja) * 1996-06-24 1998-01-13 Nippon Steel Corp デスケーリング性と伸線性の優れた線材
JP2003105498A (ja) * 2001-09-28 2003-04-09 Togo Seisakusho Corp 高強度ばねおよびその製造方法
JP2003213372A (ja) * 2002-01-25 2003-07-30 Sumitomo Denko Steel Wire Kk ばね用鋼線およびばね
JP2003306747A (ja) * 2002-04-16 2003-10-31 Sumitomo Denko Steel Wire Kk 鋼線およびその製造方法ならびにばね

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1731625A1 (fr) * 2004-02-04 2006-12-13 Sumitomo (Sei) Steel Wire Corp. Fil d acier pour ressort
EP1731625A4 (fr) * 2004-02-04 2012-03-28 Sumitomo Sei Steel Wire Corp Fil d acier pour ressort
EP1930458A1 (fr) * 2005-08-05 2008-06-11 Sumitomo Electric Industries, Ltd. Fil revenu à l huile et son procédé de production
EP1930458A4 (fr) * 2005-08-05 2015-04-29 Sumitomo Electric Industries Fil revenu à l huile et son procédé de production
US20090205753A1 (en) * 2006-03-31 2009-08-20 Masayuki Hashimura High strength spring-use heat treated steel
CN102378823A (zh) * 2009-07-09 2012-03-14 新日本制铁株式会社 高强度弹簧用钢线
CN101892425A (zh) * 2010-08-20 2010-11-24 武汉中磁浩源科技有限公司 一种软磁合金粉末、磁粉芯及其制备方法
WO2015052035A1 (fr) * 2013-10-11 2015-04-16 Nv Bekaert Sa Fil d'acier à haute résistance à la traction
CN105579595A (zh) * 2013-10-11 2016-05-11 贝卡尔特公司 高抗拉强度钢丝
CN106442495A (zh) * 2016-09-18 2017-02-22 扬州大学 一种测定奥贝球铁中是否存在马氏体的热处理方法
CN106442495B (zh) * 2016-09-18 2018-11-30 扬州大学 一种测定奥贝球铁中是否存在马氏体的热处理方法

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