EP2601320B1 - Kugelstrahlverfahren - Google Patents

Kugelstrahlverfahren Download PDF

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Publication number
EP2601320B1
EP2601320B1 EP11760870.3A EP11760870A EP2601320B1 EP 2601320 B1 EP2601320 B1 EP 2601320B1 EP 11760870 A EP11760870 A EP 11760870A EP 2601320 B1 EP2601320 B1 EP 2601320B1
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EP
European Patent Office
Prior art keywords
shot peening
steel
compressive residual
shot
retained austenite
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Application number
EP11760870.3A
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English (en)
French (fr)
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EP2601320A1 (de
Inventor
Yuji Kobayashi
Toshiya Tsuji
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Sintokogio Ltd
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Sintokogio Ltd
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Publication of EP2601320A1 publication Critical patent/EP2601320A1/de
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to a method for shot peening. Specifically, it relates to a method for shot-peening a steel.
  • the stress shot peening can be used for a part, like a spring that can be stressed while shot-peening it, there have been problems in that stress shot peening cannot be used for a part like a gear that cannot be stressed while shot-peening it.
  • US 4,415,378 discloses a method for work hardening the surface of a carburised steel part, whereby an amount of 10-30% residual austenite in the case layer is transformed to at least 5-20% of untempered martensite, to induce compressive residual stresses.
  • the object of the present invention is to provide a method for shot peening for producing maximum compressive residual stresses that exceed 60% of the yield strength at 0.2% offset by controlling the properties of the material or the conditions for the heat treatment of the processed steel and the conditions for shot peening, without using the stress shot peening.
  • the method for shot peening of the first aspect of the present invention is to produce a compressive residual stress in a processed steel that has an amount of retained austenite in a range of 5 to 30%, by peening shot media onto the processed steel.
  • the amount of retained austenite is controlled to keep the change in the amount within a range of 2 to 30% before and after the shot peening.
  • the shot peening is controlled to keep the change in the amount of retained austenite at the depth where the maximum compressive residual stress is generated at a range of 2 to 30% before and after the shot peening.
  • the processed steel is a gas carburized steel.
  • a maximum compressive residual stress can be obtained that exceeds 60% of the yield strength at 0.2% offset.
  • no jig for stressing the processed steel for the shot peening is required.
  • efficient shot peening can be used for a part such as a gear that has a complicated shape.
  • the method for shot peening of the first aspect can always be performed.
  • a processed steel that has a desired amount of retained austenite can be easily obtained by changing carburizing.
  • Fig. 1 is a table showing the properties of the processed steels that were used in the embodiments of the present invention.
  • Steel-A to Steel-G are prepared as the processed steels.
  • the carbon contents (wt %), the conditions for heat treatment, and the yield strengths at 0.2% offset (MPa), as properties of the materials, and the tensile strengths (MPa), the hardness at the surfaces (HV0.3), and the amount of retained austenite ⁇ (Gamma) R (%), are all shown in the table.
  • the processed steels are prepared from the steels that are based on a chromium steel or a chromium-molybdenum steel and that have different carbon contents, i.e., between 0.2 and 0.8 wt%, and the steels that are based on a chromium-molybdenum steel that have a carbon content of 0.8 wt%, and that are tempered in different conditions.
  • These processed steels are gas carburized steels.
  • Fig. 2 is a table showing the conditions of the shot peening that were used in the embodiments of the present invention.
  • Two types of conditions for shot peening (the conditions for peening shot media onto the processed steels) were used.
  • a compressive-air shot peening system was used in both types.
  • the hardness (HV), the diameters (mm), and the air pressure for peening shot media are all shown in the table.
  • the coverage which represents the amount of shot media being peened, was 300% in all cases.
  • Fig. 3 is a table showing the properties of the processed steels after the shot peening. The table also shows the properties before the shot peening. It shows the properties of Steel-A to Steel-G in the upper and lower sides for two respective types of conditions for shot peening.
  • That table shows the maximum compressive residual stress ⁇ (Sigma) R (MPa), Gamma R at the peak depth (%), Sigma R (max)/ Sigma 0.2 , and the rate of change in Gamma R at the peak depth (%), as the properties of the processed steels after shot peening.
  • the maximum compressive residual stress Sigma R means the maximum value of the compressive residual stresses that are measured at various depths from the surface (since a compressive residual stress is generally expressed as a negative value, it is the maximum value in absolute values).
  • the compressive residual stresses were measured by using a micro-stress analyzer that is available from Rigaku Corporation (X-ray tube: Cr-K ⁇ ( Alpha ); diffractive surface: (220); stress constant: -318 MPa/deg; Bragg angle of the strain-free 2 ⁇ : 156.4 °).
  • the Gamma R at the peak depth (%) denotes the amount of retained austenite at the depth where the maximum compressive residual stress is generated.
  • the amounts of retained austenite were also measured by using a micro-stress analyzer that is available from Rigaku Corporation (X-ray tube: Cr-K Alpha ; diffractive surface: (220); Gamma-diffraction plane: (311); time for measuring on Alpha-plane: 60 sec; range of diffraction on Alpha-plane: 156.4 °).
  • the Sigma R (max)/ Sigma 0.2 denotes the maximum compressive residual stress compared to the yield strength at 0.2% offset.
  • the rate of change in Gamma R at the peak depth (%) denotes a rate of change in the amount of retained austenite before and after the shot peening at the depth where the maximum compressive residual stress is generated.
  • Fig. 4 shows supplemental data for Fig. 3 .
  • the processed steels that have the maximum compressive residual stress that exceeds 60% of yield strength at 0.2% offset can be obtained by the following process, i.e., peening shot media onto a processed steel that has the amount of retained austenite in a range between 5 to 30%.
  • the rate of change (reduction) in the amount of retained austenite at the depth where the maximum compressive residual stress is generated is controlled to be in a range between 2 to 30%.
  • the threshold value of the amount of retained austenite i.e., 5 to 30%, is determined based on the maximum value in the range that is representative for industrial materials.
  • the upper limit for the rate of change in the amount of retained austenite i.e., 30%, is specified based on the maximum value of the amount of retained austenite.
  • the lower limit for the rate of change in the amount of retained austenite i.e., 2%, is determined by plotting the Sigma R (max)/ Sigma 0.2 in relation to the rate of change in Gamma R at the peak depth (%) and drawing an approximate curve by the least square method.
  • the rate of change (reduction) in the amount of retained austenite of the processed steel at the depth where the maximum compressive residual stress is generated is controlled to be in a range between 2 to 30%, the maximum compressive residual stress becomes over 60% of the yield strength at 0.2% offset. This is because the retained austenite expands by the deformation-induced martensitic transformation and thus the mechanical properties improve by the expansion of the retained austenite.
  • processed steels that have the amount of retained austenite in a range between 5 to 30% are subject to shot peening.
  • the change in the amount of retained austenite before and after shot peening is controlled to be in a range of 2 to 30%, so as to produce the compressive residual stress in the processed steel.
  • a maximum compressive residual stress that exceeds 60% of the yield strength at 0.2% offset can be produced. Therefore, no jig for stressing the processed steel for the stress shot peening is required. Further, a part such as a gear, which has a complicated shape, can be efficiently shot-peened.
  • the processed material is a gas carburized steel
  • a processed steel that has a desired amount of retained austenite can be easily obtained by adjusting the conditions for carburizing.
  • Any steels can be used for the processed steels, but a gas carburized steel that has a large amount of retained austenite is preferable.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Heat Treatment Of Articles (AREA)

Claims (2)

  1. Verfahren zum Kugelstrahlen,
    wobei Strahlmaterialien auf einen verarbeiteten Stahl gestrahlt werden, der eine Menge von eingeschlossenem Austenit in einem Bereich von 5 bis 30% aufweist, und
    wobei eine Änderung in der Menge des eingeschlossenen Austenits in einer Tiefe, an der die maximale Druckeigenspannung erzeugt wird, auf einen Bereich von 2 bis 30 % vor und nach dem Kugelstrahlen gesteuert wird, um eine Druckeigenspannung in dem verarbeiteten Stahl zu erzeugen, die 60% der Streckfestigkeit bei 0,2% Dehnung überschreitet.
  2. Verfahren zum Kugelstrahlen Anspruch 1,
    wobei der verarbeitete Stahl ein aufgekohlter Stahl ist.
EP11760870.3A 2010-08-05 2011-08-04 Kugelstrahlverfahren Active EP2601320B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2010176682 2010-08-05
PCT/JP2011/004414 WO2012017656A1 (en) 2010-08-05 2011-08-04 A method for shot peening

Publications (2)

Publication Number Publication Date
EP2601320A1 EP2601320A1 (de) 2013-06-12
EP2601320B1 true EP2601320B1 (de) 2018-01-17

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EP11760870.3A Active EP2601320B1 (de) 2010-08-05 2011-08-04 Kugelstrahlverfahren

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US (1) US20130160510A1 (de)
EP (1) EP2601320B1 (de)
JP (1) JP5790656B2 (de)
CN (1) CN102906282A (de)
WO (1) WO2012017656A1 (de)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103604874A (zh) * 2013-10-30 2014-02-26 北京理工大学 残余压应力定值试块的制作工艺及其使用和保存方法

Family Cites Families (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4191599A (en) * 1978-09-13 1980-03-04 Ford Motor Company Method of heat treating high carbon alloy steel parts to develop surface compressive residual stresses
US4495002A (en) * 1981-05-27 1985-01-22 Westinghouse Electric Corp. Three-step treatment of stainless steels having metastable austenitic and martensitic phases to increase resistance to chloride corrosion
US4415378A (en) * 1982-04-22 1983-11-15 Dana Corporation Case hardening method for steel parts
JPH0643604B2 (ja) * 1986-02-20 1994-06-08 住友金属工業株式会社 機械構造用部品の製造方法
JPH0756043B2 (ja) * 1988-09-27 1995-06-14 マツダ株式会社 鋼部材の製造方法
JPH0466863A (ja) * 1990-07-09 1992-03-03 Toyota Motor Corp 鋼材の加工による残留応力の測定方法
JPH06271930A (ja) * 1993-03-18 1994-09-27 Nisshin Steel Co Ltd 疲労特性に優れた高強度高靭性鋼の製法
JPH09123145A (ja) * 1995-10-26 1997-05-13 Mishima Kosan Co Ltd 舗装用コンクリートブロック製造用金型の製造方法
JP3975314B2 (ja) * 1999-08-27 2007-09-12 株式会社ジェイテクト 軸受部品素材及び転がり軸受の軌道輪の製作方法
JP2004011737A (ja) * 2002-06-06 2004-01-15 Nsk Ltd 自動調心ころ軸受
JP2004339575A (ja) * 2003-05-16 2004-12-02 Nsk Ltd 転動装置部品の製造方法
JP4137122B2 (ja) * 2003-10-31 2008-08-20 日本ピストンリング株式会社 カムシャフトの製造方法、カムシャフト及びこれに用いるカムロブ材
JP2006250316A (ja) * 2005-03-14 2006-09-21 Nsk Ltd 転動装置
JP4749073B2 (ja) * 2005-07-26 2011-08-17 独立行政法人産業技術総合研究所 金型及びその製造方法
CN101135344A (zh) * 2006-08-30 2008-03-05 上海百信轴承有限公司 摇臂轴承高碳铬钢外圈复合处理技术
CN100516593C (zh) * 2006-10-17 2009-07-22 武汉理工大学 锰铜合金奥贝球铁汽车后桥螺旋锥齿轮及其制备方法
JP2008207279A (ja) * 2007-02-27 2008-09-11 Sanyo Special Steel Co Ltd 金型の表面改質方法および金型
JP5164539B2 (ja) * 2007-11-28 2013-03-21 大同特殊鋼株式会社 ショットピーニング方法
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JP5090257B2 (ja) * 2008-06-05 2012-12-05 山陽特殊製鋼株式会社 アルミ加工用金型に適した工具鋼およびアルミ加工用金型

Also Published As

Publication number Publication date
JP2013532583A (ja) 2013-08-19
US20130160510A1 (en) 2013-06-27
JP5790656B2 (ja) 2015-10-07
EP2601320A1 (de) 2013-06-12
CN102906282A (zh) 2013-01-30
WO2012017656A1 (en) 2012-02-09

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