EP1553197B1 - Acier pour structure mecanique extremement approprie pour le laminage, la trempe, la resistance aux fissures, ayant une excellente propriete de torsion et arbre menant - Google Patents

Acier pour structure mecanique extremement approprie pour le laminage, la trempe, la resistance aux fissures, ayant une excellente propriete de torsion et arbre menant Download PDF

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Publication number
EP1553197B1
EP1553197B1 EP02790877A EP02790877A EP1553197B1 EP 1553197 B1 EP1553197 B1 EP 1553197B1 EP 02790877 A EP02790877 A EP 02790877A EP 02790877 A EP02790877 A EP 02790877A EP 1553197 B1 EP1553197 B1 EP 1553197B1
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European Patent Office
Prior art keywords
content
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drive shaft
crack resistance
quenching
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EP02790877A
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German (de)
English (en)
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EP1553197A4 (fr
EP1553197A1 (fr
Inventor
Yasuhiro JFE Steel Corporation OMORI
Akihiro JFE Steel Corporation MATSUZAKI
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NTN Corp
JFE Steel Corp
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NTN Corp
JFE Steel Corp
NTN Toyo Bearing 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
    • C22C38/42—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
    • C22C38/001—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
    • C22C38/18—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to machine structural steel products.
  • the present invention relates to a machine structural steel product having superior formability of rotary-forming, quenching-crack resistance, and torsional properties.
  • a steel product is provided which is a machine structural steel product manufactured using an electric furnace instead of a blast furnace and which retains various properties even when a tramp element such as Cu or Ni is incorporated.
  • Machine structural members such as drive shafts for automobile use and constant velocity joints have been requested to have a torsional strength at a required level.
  • a hot-rolled steel bar has been generally processed by the steps of hot-forging, normalizing whenever necessary, cutting, cold-forging, and the like so as to have a predetermined shape, followed by induction hardening and tempering.
  • the inventors of the present invention proposed a machine structural steel product having superior machinability, quenching-crack resistance, and torsional properties as disclosed, for example, in Patent Document 2 in which the steel texture is controlled at the same time when the components of the steel product are appropriately adjusted.
  • JP-A-9-111401 discloses a steel for machine structural use having a composition consisting of, by mass, 0.35 -0.60% C, ⁇ 0.05% Si, 0.65-1.70% Mn, ⁇ 0.020% P, 0.005-0.035% S, ⁇ 0.15% Cr, 0.05-0.50% Mo, 0.01-0.05% Ti, 0.01-0.05% Al, ⁇ 0.01% N, 0.0005-0.0050% B, and the balance Fe and also having a structure containing bainitic phase by 5-30% by area ratio, wherein further, the above torsional strength is regulated to ⁇ 1400MPa in this steel.
  • Ms 538-317(%C)-33(%Mn)-28(%Cr)-17(%Ni)-11(%Si)-11(%Mo)
  • a primary object of the present invention is to solve the problems described above. That is, an object of the present invention is to provide a machine structural steel product which has superior quenching-crack resistance and torsional properties and which effectively prevents the degradation in formability of rotary-forming even when manufactured using an electric furnace instead of a blast furnace. In addition, a drive shaft formed from this steel product is also proposed.
  • C is an element having the largest influence on the high-frequency hardenability and is an effective element for increasing the hardness and the depth of a hardened layer by quenching and for ensuring a torsional strength of 1,400 MPa or more after induction hardening and tempering.
  • the content is less than 0.35%, the effect of the carbon component is not sufficient, and when the content is more than 0.50%, the machinability and quenching-crack resistance are degraded. Accordingly, the C content is set in the range of from 0.35% to 0.50%.
  • Si 0.15% or less, 0.05 or more
  • Si is an element having a function of reinforcing steel when being dissolved in ferrite, thereby improving the torsional strength.
  • the content is 0.05% or more.
  • the Si content is more than 0.15%, the machinability is remarkably deteriorated, and hence the content is set to 0.15% or less.
  • Mn 0.2% or more, 1.1% or less
  • Mn is an effective element for improving the hardenability and increasing the hardness penetration depth in induction hardening, thereby contributing the improvement of the torsional strength.
  • the content is less than 0.2%, the effect of the Mn component is not sufficient.
  • the content is more than 1.1%, in addition to the formability of rotary-forming, the machinability and the torsional strength are also degraded. Accordingly, the content of Mn is set in the range of from 0.2% to 1.1%. Preferable content is in the range of from 0.2% to 0.8%.
  • the content of P is preferably decreased as small as possible. From this point of view, the content is decreased to 0.020% or less.
  • S forms MnS in steel and has a function of improving the machinability, and hence the content is set to 0.005% or more. However, since MnS tends to initiate cracking and causes the decrease in strength and toughness, the maximum content of S is set to 0.035%. Preferable content is in the range of from 0.010% to 0.035%.
  • Cr is a particularly important element in the present invention, and when Cr is contained, the adverse influence of tramp elements such as Cu and Ni can be advantageously removed, the adverse influence being degradation in formability of rotary-forming, torsion properties, machinability, and the like.
  • the content of Cr is 0.1% or less, the effect of Cr component is not sufficient.
  • the content of Cr is set to more than 0.1% to 0.2%.
  • Mo is not only effective for improving the hardenability but also has a function of facilitating the growth of bainite so as to improve the machinability.
  • the content must be 0.05% or more; however, when the content is more than 0.5%, the machinability is adversely degraded. Accordingly, the content of Mo is set in the range of from 0.05% to 0.5%. Preferable content is in the range of from 0.1% to 0.5%.
  • Ti forms a nitride with N and reduces the grain size of austenite in high-temperature heating.
  • This element is essential for ensuring dissolved B that is effective for improving the hardenability.
  • the content must be 0.01% or more; however, when the content is more than 0.05%, the toughness is degraded. Accordingly, the content of Ti is set in the range of from 0.01% to 0.05%.
  • Al 0.01% or more, 0.05% or less
  • Al is an effective element as a deoxidizing agent, and to obtain this effect, the content thereof must be at least 0.01%. However, when the content is more than 0.05%, giant alumina grains are grown and initiates fatigue damage, thereby decreasing the fatigue strength. Hence, the content of Ai is set in the range of from 0.01% to 0.05%.
  • N is an effective element for forming a nitride with Al or Ti and for reducing the grain size of austenite in high-frequency heating, and hence the fatigue strength can be improved.
  • the content thereof is more than 0.01%, the nitride is coarsely grown, and the fatigue strength is adversely degraded.
  • an strength is adversely degraded.
  • the content of N is set to 0.01% or less.
  • B has an effect of improving the torsional strength by improving the hardenability and by increasing the hardness penetration depth in high-frequency hardening.
  • the content thereof must be 0.0005% or more; however, when the content is more than 0.0050%, the toughness is decreased.
  • the content of B is set in the range of from 0.0005% to 0.0050%.
  • Cu is an element which is inevitably incorporated as a tramp element.
  • the content is more than 0.25%, degradation in formability of rotary-forming and the like may occur in some cases, and hence the content is set to 0.25% or less.
  • the content is decreased to less than 0.06%, the manufacturing cost is increased, and as a result, the content is set to 0.06% or more.
  • Ni 0.05% or more, 0.2% or less
  • Ni is an element which is inevitably incorporated as a tramp element.
  • the content is more than 0.2%, degradation in formability of rotary-forming and the like may occur in some cases, and hence the content is set to 0.2% or less.
  • the content is decreased to less than 0.05%, the manufacturing cost is increased, and as a result, the content is set to 0.05% or more.
  • V 0.01% or more, 0.30% or less
  • Nb 0.005% or more, 0.050% or less
  • V and Nb form carbonitrides and reduce the grain size of austenite, thereby effectively contributing the improvement of strength.
  • the contents of V and Nb are less than 0.01% and less than 0.005%, respectively, the effects thereof are not sufficient.
  • the contents of V and Nb are more than 0.30% and more than 0.050%, respectively, a large and coarse material is precipitated, and the toughness is decreased thereby.
  • the content of V is set in the range of from 0.01% to 0.30%
  • the content of Nb is set in the range of from 0.005% to 0.050%.
  • LD 0.569 ⁇ 7.98 ⁇ C 1 / 2 ⁇ 1 + 4.1 ⁇ Mn ⁇ 1 + 2.83 ⁇ P ⁇ 1 - 0.62 ⁇ S ⁇ 1 + 0.64 ⁇ Si ⁇ 1 + 2.33 ⁇ Cr ⁇ 1 + 0.52 ⁇ Ni ⁇ 1 + 3.14 ⁇ Mo ⁇ 1 + 0.27 ⁇ Cu ⁇ ( 1 + 1.5 ⁇ 0.9 - C ) ⁇ + 52.6
  • C, Mn, P, S, Si, Cr, Ni, Mo, and Cu each indicate the content (mass percent) of the respective elements.
  • This LD value is the index of the texture and the hardness through the hardenability.
  • Fig. 1 shows the results of measurement of the influence of the LD value on the formability of rotary-forming of high Cr steel and high Si steel.
  • the results of measurement of low Cr and low Si steel disclosed in Patent Document 2 described above are also shown for comparison.
  • the formability of rotary-forming are evaluated by a die life obtained in a form-rolling test.
  • the die life As shown in the figure, in both cases, when the LD value is more than 120, the die life is rapidly decreased; however, when the LD value is 120 or less, the die life, that is, the formability of rotary-forming, of the high Cr and high Si steel of the present invention is much superior.
  • the components are controlled to obtain an LD value of 120 or less.
  • the steel texture is not particularly specified; however, a texture composed of ferrite as a primary component and approximately 5 to 30% of a bainite phase on an area percent basis is preferably used.
  • the steel product described above is most preferably used for power transmission devices, particularly for automobile drive shafts and constant velocity joints.
  • a significant advantage that is, weight reduction, can be obtained.
  • a steel melting method for the steel product of the present invention may be performed by a known method and is not particularly limited.
  • the machine structural steel of the present invention has superior formability of rotary-forming even when Cu or Ni is incorporated, which is difficult to be removed in steel melting performed by using an electric furnace, and hence the steel melting is preferably performed using an electric furnace.
  • Vacuum degassing such as RH degassing, refining using ladles, and the like may be additionally performed.
  • Molten steel is solidified by a continuous casting method or an ingot-making method and is then formed into materials having predetermined shapes through hot rolling or hot/warm forging. After processed by intermediate heat treatment, whenever necessary, such as normalizing, spheroidized annealing, or softening annealing, the materials thus obtained are finished into a desired shape by cold working such as cutting, forging, or form rolling.
  • the product having a predetermined shape is formed by hot rolling or hot forging, or is then further processed by normalizing. Cooling after the formation of austenite by this hot rolling or hot forging followed by normalizing or the like is preferably performed at a rate of approximately 0.2 to 2.0°C/sec in order to produce an appropriate amount of bainite. In particular, for a steel bar having a large diameter, accelerated cooling in which cooling is controlled is preferably performed.
  • final induction hardening and tempering may be performed by heating for approximately 0.2 to 1.0 second at an output of approximately 120 kW using a induction hardening apparatus at a frequency of approximately 15 kHz, followed by tempering at a temperature of 170°C for approximately 30 minutes.
  • the measurement method of the steel texture and the various properties are as follows.
  • the formability of rotary-forming were evaluated by the die life in accordance with a form-rolling test.
  • the die life was determined by the number of material which was form-rolled until the form-rolling could not be further continued due to tooth tipping, peeling of a fracture surface, tooth abrasion, and the like.
  • Tooth form involute form, module: 1.27, pressure angle: 30°, number of teeth: 21, pitch diameter: 26.27 mm, large diameter: 28.1 mm, small diameter: 24.88 mm, over-pin diameter (pin 2.5 mm in diameter): 30.49 mm
  • a torsion test piece in the form of a smooth round bar having a parallel portion 20 mm in diameter was formed from a straight bar and was then quenched at a frequency of 15 kHz using a induction hardening apparatus, tempering treatment at 170°C for 30 minutes was performed, and the torsion test was then performed.
  • the hardness penetration depth after the induction hardening and tempering was set to approximately 4 mm.
  • the torsion test was performed by using a torsion tester of 4,900 J (500 kgf ⁇ m), and the maximum torsional shear strength was measured as the torsional strength.
  • a round bar (20 mm in diameter) having a V-shaped groove on the surface thereof along the shaft direction was formed from the above straight bar 25 mm in diameter and was then processed by induction hardening equivalent to that described above. After 10 locations on a C cross-section of the round bar were polished and observed, the evaluation was performed by the number of generated cracks.
  • an opening having a length of 12 mm was formed using a drill made of SKH 4 having a diameter of 4 mm at a rotation speed of 1,500 rpm, and the operation described above was repeated until the formation of the opening could not be further continued, thereby obtaining the total length (mm) of the openings. This total length of the openings thus formed was evaluated as a tool life.
  • the steel products obtained according to the present invention have superior formability of rotary-forming, torsional properties, quenching-crack resistance, and machinability.
  • the static strength and the fatigue strength of a drive shaft which was formed from the steel product of the present invention provided with a hardened layer by induction hardening and tempering, will be described with reference to Figs. 2 and 3, respectively.
  • the drive shaft of the example according to the present invention was formed from a steel product of No. 2 shown in Table 1.
  • the drive shaft of the comparative example was formed from a steel product of No. 18 shown in Table 1.
  • Fig. 2 is a graph showing the results of measurement of the static strength of the drive shafts by a static strength test.
  • the static strength test (static strength test) is to evaluate the static strength by measuring the maximum torque obtained when the drive shaft is broken.
  • the number of the drive shafts used for the test was one for the comparative example and two for the examples.
  • the results of the comparative example, example 1, and example 2 are shown in Fig. 2.
  • the maximum torque obtained when the drive shaft of the comparative example was broken is set to be 1, and the maximum torque obtained when the drive shaft of the example was broken was represented by the ratio thereto. It was understood that the static strength of the drive shaft of the example was improved by approximately 1.17 times that of the drive shaft of the comparative example.
  • Fig. 3 is a graph showing the results of the fatigue strengths of the drive shaft of the example and the drive shaft of the comparative example measured by a fatigue strength test.
  • the fatigue strength test is a test for measuring the fatigue strength obtained when torque is repeatedly loaded. A predetermined load torque is repeatedly applied to the drive shaft, and the number of cycles N of load application which causes the fracture of the drive shaft is obtained.
  • the vertical axis indicates the value obtained by dividing the load torque by the static strength of the drive shaft of the comparative example, and the value thus obtained is dimensionless.
  • the horizontal axis indicates the number of cycles of load application causing the fracture of the drive shaft.

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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 Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Shafts, Cranks, Connecting Bars, And Related Bearings (AREA)

Claims (3)

  1. Produit en acier pour construction mécanique doté d'une aptitude au formage rotatif, d'une résistance aux fissures de trempe et de propriétés de torsion supérieures, comprenant : sur la base d'un pourcentage en masse,
    C : 0,35 % à 0,50 %
    Si : 0,05 % à 0,15 %
    Mn : 0,20 % à 1,1 % ;
    P : 0,02 % ou moins ;
    S : 0,005 % à 0,035 % ;
    Cr : plus de 0,1 % à 0,2 % ;
    Mo : 0,05 % à 0,5 % ;
    Ti : 0,01 % à 0,05 % ;
    Al : 0,01 % à 0,05 % ;
    N : 0,01 % ou moins ;
    B : 0,0005 % à 0,0050 % ;
    Cu : 0,06 % à 0,25 % ;
    Ni : 0,05 % à 0,2 %, facultativement V : 0,01 % à 0,30 % et facultativement Nb : 0,005 % à 0,05 %,
    dans lequel une valeur LD représentée par l'équation (1) suivante de 120 ou moins est satisfaite, et l'équilibre de la composition comprend Fe et des impuretés inévitables :
    note °LD = 0 , 569 × 7 , 98 × C 1 / 2 × 1 + 4 , 1 ⁢ Mn ⋅ ( 1 + 2 , 83 P ) ⋅ 1 - 0 , 62 ⁢ S ⋅ 1 + 0 , 64 ⁢ Si ⋅ 1 + 2 , 33 ⁢ Cr ⋅ ( 1 + 0 , 52 Ni ) ⋅ 1 + 3 , 14 ⁢ Mo ⋅ 1 + 0 , 27 ⁢ Cu ⋅ ( 1 + 1 , 5 ( 0 , 9 - C ) ) } + 52 , 6
    Figure imgb0005
    où C, Mn, P, S, Si, Cr, Ni, Mo et Cu dans l'équation indiquent chacun la teneur (pourcentage en masse) des éléments respectifs.
  2. Produit en acier pour construction mécanique possédant une aptitude au formage rotatif, une résistance aux fissures de trempe et des propriétés de torsion supérieures, selon la revendication 1, comprenant en outre : sur la base d'un pourcentage en masse,
    V : 0,01 % à 0,30 %, et
    Nb : 0,005 % à 0,05 %.
  3. Arbre d'entraînement comprenant le produit en acier pour construction mécanique selon la revendication 1 ou 2, dans lequel une couche trempée est formée dessus en effectuant une trempe par induction et un revenu.
EP02790877A 2002-10-18 2002-12-26 Acier pour structure mecanique extremement approprie pour le laminage, la trempe, la resistance aux fissures, ayant une excellente propriete de torsion et arbre menant Expired - Fee Related EP1553197B1 (fr)

Applications Claiming Priority (3)

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JP2002304190 2002-10-18
JP2002304190 2002-10-18
PCT/JP2002/013564 WO2004035848A1 (fr) 2002-10-18 2002-12-26 Acier pour structure mecanique extremement approprie pour le laminage, la trempe, la resistance aux fissures, ayant une excellente propriete de torsion et arbre menant

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EP1553197A1 EP1553197A1 (fr) 2005-07-13
EP1553197A4 EP1553197A4 (fr) 2006-07-05
EP1553197B1 true EP1553197B1 (fr) 2007-09-19

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US (1) US20060065328A1 (fr)
EP (1) EP1553197B1 (fr)
JP (1) JP4170294B2 (fr)
CN (1) CN1307319C (fr)
DE (1) DE60222595T2 (fr)
ES (1) ES2292836T3 (fr)
WO (1) WO2004035848A1 (fr)

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SE0500812L (sv) * 2005-04-12 2006-01-24 Scania Cv Abp Borstålsort för induktionshärdning jämte axel
JP2007154305A (ja) * 2005-07-05 2007-06-21 Jfe Steel Kk 強度、延性及び靱性に優れた機械構造用鋼およびその製造方法
WO2018212327A1 (fr) * 2017-05-18 2018-11-22 新日鐵住金株式会社 Fil, fil d'acier et procédé de fabrication d'un fil d'acier
WO2020179800A1 (fr) * 2019-03-05 2020-09-10 日本製鉄株式会社 Vilebrequin
WO2023248556A1 (fr) * 2022-06-24 2023-12-28 Ｊｆｅスチール株式会社 Acier pour durcissement à haute fréquence

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JPS61174322A (ja) * 1985-01-28 1986-08-06 Nippon Steel Corp 機械構造用鋼の圧延材軟質化法
US5279688A (en) * 1989-12-06 1994-01-18 Daido Tokushuko Kabushiki Kaisha Steel shaft material which is capable of being directly cut and induction hardened and a method for manufacturing the same
JP3062275B2 (ja) * 1990-05-02 2000-07-10 川崎製鉄株式会社 高強度軸部品用鋼材
JP3598147B2 (ja) * 1995-06-19 2004-12-08 エヌケーケー条鋼株式会社 冷間加工性および高周波焼入れ性に優れた機械構造用鋼
JPH0920958A (ja) * 1995-06-30 1997-01-21 Nkk Corp 耐二次加工性に優れたプレス成形用熱延鋼板及びその製造方法
JP3288563B2 (ja) * 1995-10-17 2002-06-04 川崎製鉄株式会社 被削性および耐焼割れ性に優れた機械構造用鋼材およびその製造方法
CN1163942A (zh) * 1996-02-08 1997-11-05 阿斯克迈塔尔公司 制造锻件用钢及锻件制造方法
JP3402562B2 (ja) * 1996-07-19 2003-05-06 大同特殊鋼株式会社 高周波焼入れ部品
DE69811200T2 (de) * 1997-07-22 2003-10-09 Nippon Steel Corp Einsatzstahl mit hervorragender verhinderung der sekundärrekristallisation während der aufkohlung, verfahren zu dessen herstellung, halbzeug für aufzukohlende teile
JP2000154828A (ja) * 1998-11-19 2000-06-06 Nippon Steel Corp 耐フレーキング特性と軸部強度に優れた等速ジョイント用外輪とその製造方法

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WO2004035848A1 (fr) 2004-04-29
CN1307319C (zh) 2007-03-28
DE60222595D1 (de) 2007-10-31
US20060065328A1 (en) 2006-03-30
EP1553197A4 (fr) 2006-07-05
ES2292836T3 (es) 2008-03-16
CN1688733A (zh) 2005-10-26
JPWO2004035848A1 (ja) 2006-02-16
DE60222595T2 (de) 2008-06-19
EP1553197A1 (fr) 2005-07-13
JP4170294B2 (ja) 2008-10-22

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