EP1516940A1 - Verfahren zur Herstellung von Getrieben und/oder Achsen, die verbesserte Biegedauerfestigkeit und Dauerlochfrassfestigkeit als bisherige legierte Stähle aufweisen. - Google Patents

Verfahren zur Herstellung von Getrieben und/oder Achsen, die verbesserte Biegedauerfestigkeit und Dauerlochfrassfestigkeit als bisherige legierte Stähle aufweisen. Download PDF

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Publication number
EP1516940A1
EP1516940A1 EP03026668A EP03026668A EP1516940A1 EP 1516940 A1 EP1516940 A1 EP 1516940A1 EP 03026668 A EP03026668 A EP 03026668A EP 03026668 A EP03026668 A EP 03026668A EP 1516940 A1 EP1516940 A1 EP 1516940A1
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EP
European Patent Office
Prior art keywords
weight
steel
components
degree centigrade
pitting
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP03026668A
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English (en)
French (fr)
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EP1516940B1 (de
Inventor
Ajithkumar Sandur
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Mahindra and Mahindra Ltd
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Mahindra and Mahindra Ltd
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Publication of EP1516940A1 publication Critical patent/EP1516940A1/de
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    • 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
    • C23C8/80—After-treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like
    • C—CHEMISTRY; METALLURGY
    • 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
    • C23C8/28—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 more than one element being applied in one step
    • C23C8/30—Carbo-nitriding
    • C23C8/32—Carbo-nitriding of ferrous surfaces
    • 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
    • C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
    • 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
    • C21D9/32—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for gear wheels, worm wheels, or the like

Definitions

  • This invention relates to achieving both superior Bending fatigue strength and Pitting fatigue life of gear(s) and/or shaft components, using "conventional alloy steel" by a method having following steps in sequence.
  • Step 1 Modified Carbonitriding treatment
  • Step 2 Hard Shot peening process
  • Carburising , hardening and tempering have been followed commonly over years for gear train transmission components in many designs so as to increase load carrying capacity.
  • load carrying capability produced after carburising is limited by microstructural and/or sub microstructural anomalies such as grain boundary oxidation , segregated carbides , bainite and alike anomalies. It has not been possible to extend, beyond certain limits, the load carrying capability of such transmissions without geometrical changes of components. Such geometrical changes in transmissions come with following significant disadvantages
  • the second aspect of the present invention is to provide the said method for enhancing load carrying capability of transmissions without geometrical changes resulting in reduction of weights for higher load carrying capability, fuel consumption, development cost, development time and product cost and in turn give higher satisfaction to the customer.
  • Another aspect of the present invention is to avoid geometrical changes in transmission components resulting in maintaining same weight and hence lower emission levels for enhanced load carrying capabilities.
  • Another aspect of the present invention is to provide solution to the problem of providing additional space in transmissions in case of geometric design changes are required to be introduced.
  • the invention is also beneficial in such cases where the space constraints do not permit any geometric changes.
  • the present invention features achieving both superior bending fatigue strength and pitting fatigue life of gear(s) and / or shaft components using "conventional steel" by a method having following steps in sequence.
  • Steel material comprising 0.10 to 0.30 weight % Carbon, 0.15 to 0.35 weight % Silicon, 0.8 to 1.5 weight % Chromium , 0.6 to 1.5 weight % Manganese , 0.017 to 0.040 weight % Aluminium , and balance iron including impurities , produced in vacuum degassing and alike routes.
  • Carbon inherently present in any steel is restricted in the range of 0.1 to 0.3 weight %. Lower than 0.1 weight % will not have sufficient core strength after the present processing. More than 0.3% will lead to core brittleness and reduced toughness. The response to heat treatment process will also be poor depending on higher Carbon contents.
  • Silicon is an essential element for de-oxidation of molten steel and hence minimum of 0.15 weight % is specified to ensure that de-oxidation is effectively taken care of. Higher than 0.35 weight % will entail more silicate inclusions affecting forgeability, machinability and reliability in service.
  • Chromium is easily available element for increasing hardenability. It is limited between 0.8 to 1.5 weight % to ensure adequate hardenability in the steels for gear(s) and / or shall components, in combination with Manganese. Higher than the limits will entail intergranular oxidation in the heat treated layers during carburising.
  • Manganese is yet another essential element effective in de-oxidation during melting and imparting hardenability. Not less than 0.6 weight % ensures de-oxidation and holds sulphur together. More than 1.5 weight % will lead to forgeability and machinability problems. It is easily available and cheaper element to increase the hardenability of the material for adequate core strengths and reasonable toughness
  • Aluminium content in the range 0.017 to 0.040 weight % gives fully killed steel and does not contribute significantly in the nitride formation and stabilizing retained Austenite necessitating use of Modified Carbonitriding treatment for the purpose.
  • Trace elements like Nb , Ti , Zr , Cu and B are adjusted in such a way that the total contents are below 0.60 weight % .
  • Nitrogen content is kept at 55 to 90 parts per million ( ppm ) and hydrogen is not more than than 2.5 ppm .
  • Calcium and Sulphur are usually added in suitable quantities to improve morphology of inclusions to facilitate machinability
  • the steel during melting is treated by standard Vacuum degassing cycle to maintain lower oxygen contents (Oxygen content in the product not more than 20 ppm ) and hence limit size and distribution of inclusions to a degree that the component is fit for the applications already mentioned .
  • Carbon inherently present in any steel is restricted in the range of 0.1 to 0.3 weight %. Lower than 0.1 weight % will not have sufficient core strength after the present processing. More than 0.3% will lead to core brittleness and reduced toughness. The response to heat treatment process will also be poor depending on higher Carbon contents.
  • Silicon is an essential element for de-oxidation of molten steel and hence minimum of 0.15 weight % is specified to ensure that dc-oxidition is effectively taken care of. Higher than 0.35 weight % will entail more silicate inclusions affecting forgeability, machinability and reliability in service.
  • Chromium is easily available element for increasing hardenability. It is limited between 0.3 to 1.5 weight % to ensure adequate hardenability in the steels for gear(s) and / or shaft components, in combination with Manganese , Nickel and Molybdenum. of suitable quantities mentioned above. Higher than the limits will entail intergranular oxidation in the heat treated layers during carburising.
  • Nickel is another essential element effective in ensuring hardenability and improve toughness , required in critical applications.
  • the required quantity is to be not less than 0.3 weight % for ensuring the toughness and hardenability.
  • the upper limit is set to 2 weight % arrived at based on the effect in combination with other elements mentioned above.
  • Molybdenum is yet another highly effective element in promoting hardenability of the surface and in the core portion.
  • the lower limit is set to 0.08 weight % to be effective in promoting hardenability.
  • the upper limit of 0.5 % is set in combination with other elements mentioned above.
  • Manganese is yet another essential element effective in imparting hardenability, de-oxidation during melting .Not less than 0.6 weight % ensures de-oxidation and holds sulphur together. More than 1.5 weight % will lead to forgeability and machinability problems. It is also easily available and cheaper element to increase the hardenability of the material for adequate core strengths and reasonable toughness.
  • Aluminium content in the range 0.017 to 0.040 weight % gives fully killed steel and does not contribute significantly in the nitride formation and stabilizing retained Austenite necessitating use of Modified Carbonitriding treatment for the purpose.
  • Trace elements like Nb , Ti , Zr , Cu and B are adjusted in such a way that the total contents are below 0.60 weight % .
  • Nitrogen content is kept at 55 to 90 parts per million ( ppm ) and hydrogen is not more than than 2.5 ppm .
  • Calcium and Sulphur are usually added in suitable quantities to improve morphology of inclusions to facilitate machinability
  • the steel during melting is treated by standard Vacuum degassing cycle to maintain lowcr oxygen contents (Oxygen content in the product not more than 20 ppm ) and hence limit size and distribution of inclusions to a degree that the component is fit for the applications already mentioned .
  • the gear(s) and/or shaft components are manufactured as per conventional gear machining practice for highway, off-highway vehicle transmissions and similar industrial transmissions.
  • the said components after machining are loaded in a standard sealed quench furnace having requisite facilities for automatic measurement and feedback mechanisms for carbon potential, temperature and time and facility for ammonia introduction is to be in place. Furnaces other than standard sealed quench furnaces having above requisite capabilities are also covered in the object of the invention.
  • the first step in the heat treatment cycle is Carburising (Refer FIGURE ).
  • the carburising is done at 915 degree Centigrade with equal boost and diffusion periods with Carbon potential (Cp ) 1.0 and 0.8 respectively , using carrier gas and enricher gases.
  • the temperature of not less than 900 degree Centigrade at which the carbon diffusion is more pronounced is covered in the invention.
  • the effective case depth covered is in the range of 0.3 to 1.7 mm (cut off hardness 513 Hv). Effective case depths less than 0.3 mm do not provide adequate pitting resistance and more than 1.7 mm have deleterious effects on the fatigue properties for the applications covered in the scope of invention.
  • the component is cooled inside the furnace to 850 degree Centigrade and ammonia is introduced with 15% of the whole furnace gas mixture ( rest of the percent being carrier gas ) .
  • the cycle is carried out for minimum 30 minutes.
  • Temperature not less than 840 degree Centigrade and not more than 870 degree Centigrade is also covered as part of the invention to facilitate pronounced nitrogen diffusion upto a depth of 0.3 mm.
  • ammonia not less than 15% and not more than 20% of the whole furnace gas mixture is covered for the "conventional steel" in which nitrogen absorbing elements and elements promoting diffusion of nitrogen are not in sufficient quantities.
  • quenching in suitable medium at 120 to 150 degree Centigrade is maintained in the present invention.
  • the quenching medium temperature of not less than 50 C is covered in the object of the invention.
  • Tempering temperature of 180 degree Centigrade is adopted for the purpose of relieving quenching stresses, without reduction in retained austenite produced after quenching, as above.
  • the temperature not less than 160 degree Centigrade is covered to relieve quenching stresses.
  • Hardness after Modified Carbonitriding is maintained at not less than 74U Hv at a depth of 0.05 to 0.35 mm below the surface.
  • the stresses responsible for pitting are maximum at depth range mentioned here in the applications mentioned above. The hardness will get further enhanced during Hard shot peening and will provide adequate safety against pitting failures for the applications already covered.
  • the bending fatigue strength which is a function of maximum residual compressive stress below the surface, is also enhanced by Hard shot peening.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Gears, Cams (AREA)
EP03026668A 2003-09-18 2003-11-19 Verfahren zur Herstellung von Getrieben und/oder Achsen, die verbesserte Biegedauerfestigkeit und Dauerlochfrassfestigkeit als bisherige legierte Stähle aufweisen. Expired - Lifetime EP1516940B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
INBO09752003 2003-09-18
IN975BO2003 2003-09-18

Publications (2)

Publication Number Publication Date
EP1516940A1 true EP1516940A1 (de) 2005-03-23
EP1516940B1 EP1516940B1 (de) 2010-09-15

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EP03026668A Expired - Lifetime EP1516940B1 (de) 2003-09-18 2003-11-19 Verfahren zur Herstellung von Getrieben und/oder Achsen, die verbesserte Biegedauerfestigkeit und Dauerlochfrassfestigkeit als bisherige legierte Stähle aufweisen.

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EP (1) EP1516940B1 (de)
AT (1) ATE481510T1 (de)
DE (1) DE60334216D1 (de)

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103993154A (zh) * 2014-06-09 2014-08-20 江西航宇热处理有限公司 合金钢齿轮的热处理方法
CN106191757A (zh) * 2015-06-01 2016-12-07 株式会社捷太格特 滑动构件、离合器板及其制造方法
CN104460339B (zh) * 2014-10-27 2017-02-15 上海理工大学 用于车辆传动结构轻量化设计的主动载荷谱控制方法
JP2017066498A (ja) * 2015-10-02 2017-04-06 大同特殊鋼株式会社 鋼の熱処理方法および鋼部材
CN110331258A (zh) * 2019-08-07 2019-10-15 无锡东大汉森冶金实业有限公司 超低碳硅镇静钢在RH真空处理时控制Cr含量的生产工艺
WO2020129770A1 (ja) * 2018-12-20 2020-06-25 日本精工株式会社 磁歪式トルクセンサ用シャフトの製造方法
WO2020129769A1 (ja) * 2018-12-20 2020-06-25 日本精工株式会社 磁歪式トルクセンサ用シャフトの製造方法
CN111349872A (zh) * 2020-03-10 2020-06-30 上海振华重工(集团)股份有限公司 钢材、齿条及其热处理方法、升降机构、自升式平台
CN112809397A (zh) * 2020-04-26 2021-05-18 昆明嘉和科技股份有限公司 高温浓硫酸液下泵泵轴加工装置及加工方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5595610A (en) * 1991-06-07 1997-01-21 Kabushiki Kaisha Kobe Seiko Sho Method of manufacturing case-hardened parts with little distortion in heat treatment and superior strength in bending fatigue
US5595613A (en) * 1994-03-09 1997-01-21 Nissan Motor Co., Ltd. Steel for gear, gear superior in strength of tooth surface and method for producing same
JPH10158743A (ja) * 1996-11-26 1998-06-16 Nissan Motor Co Ltd 表面硬化処理方法および歯車
EP0950723A1 (de) * 1996-12-17 1999-10-20 Komatsu Ltd. Stahlteilen mit hohem ballastwiderstand und verfahren zur herstellung
JP2000129347A (ja) * 1998-10-19 2000-05-09 Kobe Steel Ltd 高強度部品の製造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5595610A (en) * 1991-06-07 1997-01-21 Kabushiki Kaisha Kobe Seiko Sho Method of manufacturing case-hardened parts with little distortion in heat treatment and superior strength in bending fatigue
US5595613A (en) * 1994-03-09 1997-01-21 Nissan Motor Co., Ltd. Steel for gear, gear superior in strength of tooth surface and method for producing same
JPH10158743A (ja) * 1996-11-26 1998-06-16 Nissan Motor Co Ltd 表面硬化処理方法および歯車
EP0950723A1 (de) * 1996-12-17 1999-10-20 Komatsu Ltd. Stahlteilen mit hohem ballastwiderstand und verfahren zur herstellung
JP2000129347A (ja) * 1998-10-19 2000-05-09 Kobe Steel Ltd 高強度部品の製造方法

Non-Patent Citations (5)

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PATENT ABSTRACTS OF JAPAN vol. 1995, no. 10 30 November 1995 (1995-11-30) *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 09 30 September 1996 (1996-09-30) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 03 27 February 1998 (1998-02-27) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 11 30 September 1998 (1998-09-30) *
PATENT ABSTRACTS OF JAPAN vol. 2000, no. 08 6 October 2000 (2000-10-06) *

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103993154A (zh) * 2014-06-09 2014-08-20 江西航宇热处理有限公司 合金钢齿轮的热处理方法
CN104460339B (zh) * 2014-10-27 2017-02-15 上海理工大学 用于车辆传动结构轻量化设计的主动载荷谱控制方法
CN106191757A (zh) * 2015-06-01 2016-12-07 株式会社捷太格特 滑动构件、离合器板及其制造方法
CN106191757B (zh) * 2015-06-01 2021-02-02 株式会社捷太格特 滑动构件、离合器板及其制造方法
JP2017066498A (ja) * 2015-10-02 2017-04-06 大同特殊鋼株式会社 鋼の熱処理方法および鋼部材
WO2020129769A1 (ja) * 2018-12-20 2020-06-25 日本精工株式会社 磁歪式トルクセンサ用シャフトの製造方法
WO2020129770A1 (ja) * 2018-12-20 2020-06-25 日本精工株式会社 磁歪式トルクセンサ用シャフトの製造方法
JP2020101404A (ja) * 2018-12-20 2020-07-02 日立金属株式会社 磁歪式トルクセンサ用シャフトの製造方法
JP2020101403A (ja) * 2018-12-20 2020-07-02 日立金属株式会社 磁歪式トルクセンサ用シャフトの製造方法
JP7008616B2 (ja) 2018-12-20 2022-01-25 日立金属株式会社 磁歪式トルクセンサ用シャフトの製造方法
CN110331258A (zh) * 2019-08-07 2019-10-15 无锡东大汉森冶金实业有限公司 超低碳硅镇静钢在RH真空处理时控制Cr含量的生产工艺
CN110331258B (zh) * 2019-08-07 2021-04-06 苏州东大汉森冶金实业有限公司 超低碳硅镇静钢在RH真空处理时控制Cr含量的生产工艺
CN111349872A (zh) * 2020-03-10 2020-06-30 上海振华重工(集团)股份有限公司 钢材、齿条及其热处理方法、升降机构、自升式平台
CN112809397A (zh) * 2020-04-26 2021-05-18 昆明嘉和科技股份有限公司 高温浓硫酸液下泵泵轴加工装置及加工方法

Also Published As

Publication number Publication date
ATE481510T1 (de) 2010-10-15
DE60334216D1 (de) 2010-10-28
EP1516940B1 (de) 2010-09-15

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