[go: up one dir, main page]
More Web Proxy on the site http://driver.im/

EP3276031A1 - Élément coulissant et structure coulissante - Google Patents

Élément coulissant et structure coulissante Download PDF

Info

Publication number
EP3276031A1
EP3276031A1 EP16768870.4A EP16768870A EP3276031A1 EP 3276031 A1 EP3276031 A1 EP 3276031A1 EP 16768870 A EP16768870 A EP 16768870A EP 3276031 A1 EP3276031 A1 EP 3276031A1
Authority
EP
European Patent Office
Prior art keywords
sliding
component
sliding component
equal
less
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.)
Withdrawn
Application number
EP16768870.4A
Other languages
German (de)
English (en)
Other versions
EP3276031A4 (fr
Inventor
Seishin Ueda
Kunichika Kubota
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Proterial Ltd
Original Assignee
Hitachi Metals Ltd
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 Hitachi Metals Ltd filed Critical Hitachi Metals Ltd
Publication of EP3276031A1 publication Critical patent/EP3276031A1/fr
Publication of EP3276031A4 publication Critical patent/EP3276031A4/fr
Withdrawn legal-status Critical Current

Links

Images

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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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
    • C22C38/44—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
    • C22C38/46—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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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 sliding component used in, for example, various sliding environment such as an oil ring and a cam lobe which are built in an internal combustion engine.
  • the present invention relates to a sliding structure such as an internal combustion engine, which includes the sliding component built therein.
  • SUJ2 or SKD11 which is JIS steel type has been used in a material of a sliding component such as an oil ring, a cam lobe, a tappet, a piston pin, a cylinder liner, a transmission gear, a thrust plate, or a vane, which is a constituent component of an internal combustion engine and constitutes a sliding structure.
  • SKD11 is a kind of steel having excellent wear resistance because high hardness of 60 HRC or higher can be achieved by quenching and tempering and carbide in the structure thereof is also abundant.
  • a press die in which sliding characteristics (self-lubricating property) are imparted to a material and wear resistance is improved by improving a composition of the material is suggested (PTL 1).
  • the press die in PTL 1 has excellent wear resistance by exhibiting the self-lubricating property. However, applying the material of the press die in PTL 1 to a component of an internal combustion engine was not considered.
  • An object of the present invention is to provide a sliding component having excellent wear resistance. Another object of the present invention is to provide a sliding structure including the sliding component.
  • a sliding component has a composition including: in mass%, 0.7 to 1.6% of C; 0.5 to 3.0% of Si; 0.1 to 3.0% of Mn; 0.05% or less of P; 0.01 to 0.12% of S; 0.3 to 1.5% of Ni; 7.0 to 13.0% of Cr; one or two of Mo and W satisfying a relational expression: (Mo+W/2) is 0.5 to 1.7%; 0 to 0.70% of V; 0.1 to 1.0% of Cu; 0.10 to 0.70% of Al; 0 to 0.30% of Nb; and the remainder of Fe and impurities.
  • Hardness of the sliding component is equal to or more than 52 HRC and less than 58 HRC.
  • a sliding structure includes the above-described sliding component in the present invention and a counterpart component, the sliding component configured to slide on a sliding surface of the counterpart component under an environment in which lubricant is provided on a sliding surface of the sliding component.
  • sliding components constituting various sliding structure are used in a manner of sliding on a sliding surface of the counterpart component under an environment in which a lubricant is provided on a sliding surface of the sliding component, as represented by components (such as an oil ring and a cam lobe) of an internal combustion engine. It was found that the sliding component in the present invention efficiently exhibited self-lubricating property and wear resistance of the sliding component was improved under the environment.
  • configuration requirements of the present invention will be described.
  • the feature of the sliding component in the present invention is "addition-together of S and Cu" which largely contributes to exhibition of the self-lubricating property.
  • S and Cu are elements which have been hardly actively added to a steel material because of being considered as elements that hinder hot workability of the steel material. An effect of the composition of the sliding component in the present invention will be described below.
  • C is an element that is subjected to solid solution in a base and imparts strength to the sliding component.
  • C is an element that forms carbide and thus improves wear resistance or galling resistance of the sliding component.
  • C is set to be 0.7% to 1.6%.
  • C is equal to or more than 0.9%.
  • C is set to be equal to or less than 1.3%. More preferably, C is set to be equal to or less than 1.1%.
  • Si is an element that improves resistance to high temperature softening of the sliding component. However, if Si is provided too much, delta ferrite is significantly formed in the structure, and this hinders maintaining of hardness of the sliding component.
  • Si is set to be 0.5% to 3.0%. Preferably, Si is equal to or more than 0.9%. In addition, preferably, Si is set to be equal to or less than 2.0%. More preferably, Si is set to be equal to or less than 1.5%. Further preferably, Si is set to be equal to or less than 1.1%.
  • Mn is an element that improves hardenability. However, if Mn is provided too much, machinability is deteriorated. Thus, Mn is set to be 0.1% to 3.0%. Preferably, Mn is equal to or more than 0.3%. More preferably, Mn is set to be equal to or more than 0.4%. In addition, preferably, Mn is set to be equal to or less than 1.0%. More preferably, Mn is set to be equal to or less than 0.6%.
  • P is an element which is generally inevitably contained although P is not added.
  • P is an element that hinders toughness of the sliding component.
  • P is set to be equal to or less than 0.05%.
  • P is set to be equal to or less than 0.03%. More preferably, P is set to be equal to or less than 0.02%.
  • S is an element that contributes to improvement of the self-lubricating property of the sliding component in the present invention, along with Cu which will be described later.
  • the inventors examined a phenomenon occurring on a sliding surface when a sliding component having a composition in PTL 1 was used under an environment in which a lubricant was provided on the sliding surface. As a result, the inventors found that, when this sliding component was used, if sliding surfaces of the sliding component and the counterpart component came into contact with each other at surface pressure which was as high as galling occurs, an organic component in the lubricant adhering to the sliding surface of the sliding component was dehydrogenated, and thus was changed to a substance such as diamond or graphite.
  • a graphite intercalation compound having a configuration in which sulfate ions or sulfuric acid molecules were regularly interposed could improve the self-lubricating property of the sliding component and maintain a low frictional coefficient between the sliding surfaces.
  • S in the sliding component is oxidized on the sliding surface which is being used, and thus generates sulfate ions.
  • the generated sulfate ions are interposed between graphite layers, and thus accelerate forming of the graphite intercalation compound.
  • the generated sulfate ions are combined with hydrogen ions generated by dehydrogenating the lubricant, and thus form sulfuric acid molecules.
  • the formed sulfuric acid molecules are interposed between the graphite layers, and thus accelerate forming of the graphite intercalation compound. Accordingly, spacing of the graphite in a C-axial direction is increased and thus allotropic modification of graphite to diamond in a nano-level state is suppressed, the degree of freedom of sliding is improved, and lubricity is improved.
  • S is set to be 0.01% to 0.12%.
  • S is equal to or more than 0.03%. More preferably, S is equal to or more than 0.04%. Further preferably, S is equal to or more than 0.05%. In addition, preferably, S is equal to or less than 0.09%. More preferably, S is equal to or less than 0.08%.
  • Ni is an element that is combined to Al (which will be described later) so as to precipitate a Ni-Al intermetallic compound, and contributes to maintaining of hardness of the sliding component in a quenching and tempering process.
  • Ni is set to be 0.3% to 1.5%.
  • Ni is equal to or more than 0.4%.
  • Ni is equal to or less than 1.0%. More preferably, Ni is equal to or less than 0.8%. Further preferably, Ni is equal to or less than 0.6%.
  • Cr is an element that improves hardenability of the base. Cr is an element that forms carbide along with the above-described C and improves the wear resistance or the galling resistance of the sliding component. However, an increase of carbide causes deterioration of machinability.
  • Cr is set to be 7.0% to 13.0%.
  • Cr is equal to or more than 7.5%. More preferably, Cr is equal to or more than 8.0%.
  • Cr is equal to or less than 11.0%. More preferably, Cr is equal to or less than 10.0%. Further preferably, Cr is equal to or less than 9.0%.
  • Mo and W are elements that form fine carbide in the structure after quenching and tempering, and impart fatigue strength to the sliding component. However, if Mo and W are provided too much, Mo and W cause degradation of the machinability or the toughness. Mo and W can be added singly or in complex thereof. The added amount of Mo and W at this time can be defined together in a relational expression of (Mo+W/2) because W has an atomic weight of about twice that of Mo.
  • the value of (Mo+W/2) is set to be 0.5% to 1.7%.
  • the value is equal to or more than 0.7%. More preferably, the value is equal to or more than 0.9%. Further preferably, the value is equal to or more than 1.0%.
  • the value is equal to or less than 1.5%. More preferably, the value is equal to or less than 1.3%. Further preferably, the value is equal to or less than 1.2%.
  • V can be contained in order to improve hardenability. Since V forms hard VC carbide, if V is excessively contained, machinability is hindered. Thus, in the present invention, although V is contained, V is set to be equal to or less than 0.70%. Preferably, V is equal to or less than 0.50%. More preferably, V is equal to or less than 0.30%. Further preferably, V is equal to or less than 0.20%.
  • Cu is an element that contributes to improvement of the self-lubricating property of the sliding component in the present invention, along with the above-described S. That is, Cu is an element that shows a catalyst action for generating "the graphite intercalation compound". A very small amount of Cu can be precipitated on the sliding surface of the sliding component after quenching and tempering. Cu precipitated on the sliding surface has a function as a catalyst of promoting forming of the above-described "graphite intercalation compound". However, if Cu is excessively contained, Cu causes hot embrittlement of the material and thus hot workability is deteriorated. Thus, Cu is set to be 0.1% to 1.0%. Preferably, Cu is equal to or more than 0.2%. More preferably, Cu is equal to or more than 0.3%. In addition, preferably, Cu is equal to or less than 0.8%. More preferably, Cu is equal to or less than 0.6%. Further preferably, V is equal to or less than 0.5%.
  • Al is an element that is combined to Ni so as to form a Ni-Al intermetallic compound, and contributes to maintaining of hardness of the sliding component. However, if Al is provided too much, delta ferrite is significantly formed in the structure, and this hinders maintaining of hardness of the sliding component.
  • Al is set to be 0.10% to 0.70%.
  • Al is set to be equal to or more than 0.15%. More preferably, Al is set to be equal to or more than 0.25%.
  • Al is set to be equal to or less than 0.50%. More preferably, Al is equal to or less than 0.45%.
  • Nb can be contained in order to improve the hardenability. However, if Nb is excessively contained, machinability is hindered.
  • Nb is set to be equal to or less than 0.30%.
  • Nb is set to be equal to or less than 0.20%. More preferably, Nb is set to be equal to or less than 0.15%.
  • the content of Nb, which is preferable for obtaining the above effect is equal to or more than 0.03%. More preferably, the content of Nb is equal to or more than 0.05%. Further preferably, the content of Nb is equal to or more than 0.07%.
  • the self-lubricating property of the sliding component in the present invention is exhibited by using "an alteration action by friction" of the lubricant provided on the sliding surface.
  • the lubricant which is, for example, hydrocarbon type may be interposed between the component and the counterpart component during the use.
  • the material of the counterpart component may be widely selected.
  • the frictional coefficient shown by the sliding component during the use is effectively reduced with an increase of the value of the fatigue strength of the sliding component.
  • the self-lubricating property in the present invention is synergistically improved (see Fig. 3 ).
  • the object of the present invention is a sliding component having fatigue strength which is more than 600 MPa. It is difficult to reach the fatigue strength which is more than 600 MPa by using SKD11 in the related art.
  • the fatigue strength is more than 630 MPa.
  • the hardness of the sliding component in the present invention is set to be less than 58 HRC as a range in which fatigue strength of more than 600 MPa can be easily achieved.
  • the hardness is equal to or less than 57 HRC.
  • the sliding component in the present invention When the sliding component in the present invention is used, if it is assumed that hardness of the counterpart component is high, reduction in hardness of the sliding component in the present invention is not favorable measures therefor.
  • the hardness of the counterpart component is generally adjusted to be 60 to 62 HRC. That is, the hardness is higher than that of the sliding component in the present invention.
  • SUJ2 is "high carbon chromium bearing steel" standardized in JIS-G-4805.
  • the composition of SUJ2 is as follows, in mass%.
  • the sliding surface of the sliding component slides on the sliding surface of the counterpart component in an "intermittent" contact form which is referred to as a rotational motion or a reciprocating motion.
  • a rotational motion or a reciprocating motion if the hardness of the sliding component in the present invention is much less than the hardness of the counterpart component, Hertz stress to be applied is increased. If the Hertz stress exceeds the fatigue strength of the sliding component, fine plastic deformation occurs on the sliding surface. Peeling and wear from the sliding component are induced, and thus the frictional coefficient between the sliding surfaces is increased, and self-lubricating property in the present invention is hindered.
  • the lower limit of the hardness of the sliding component in the present invention is set to 52 HRC.
  • the lower limit thereof is preferably 53 HRC.
  • the lower limit thereof is more preferably 54 HRC.
  • the lower limit thereof is further preferably 55 HRC.
  • Sample No. 2 is SKD11.
  • Sample No. Composition (mass%) C Si Mn P S Ni Cr Mo W V Cu Al Nb Fe* 1 1.0 1.0 0.5 0.02 0.06 0.5 8.0 0.9 0.4 - 0.4 0.35 0.10 Bal. 2 1.5 0.3 0.3 0.02 - - 12.0 1.0 - 0.25 - - - Bal. *Including impurities
  • sliding components in which hardness was adjusted to have three types of A (50 HRC), B (55 HRC), and C (60 HRC) were prepared.
  • a sliding component 1-A was 50.4 HRC
  • a sliding component 1-B was 56.2 HRC
  • a sliding component 1-C was 62.0 HRC
  • a sliding component 2-A was 50.0 HRC
  • a sliding component 2-B was 55.8 HRC
  • a sliding component 2-C was 61.0 HRC.
  • the sliding component 2-C which has the aimed hardness of 60 HRC which is hardness of SKD11 corresponds to the sliding component in the related art.
  • the fatigue strength of each of the sliding components was measured.
  • each of the sliding components was worked to make a rotary bending fatigue test piece and an Ogoshi-type rotary bending fatigue test was performed on the test piece.
  • Surface stress of the test piece was adjusted by a sectional secondary moment determined by the shape of the test piece and adjustment of the weight of a weight hung at the center of parts of the test piece, which are parallel to each other.
  • Stress amplitude had a condition (referred to as an Amplitude ratio: 1) in which stress of tension was equal to stress of compression, in one rotation of the test piece.
  • a rotation speed of the test piece was set to 50Hz (3,000 rpm). Stress when the rotary bending fatigue test piece was broken was set to be the fatigue strength.
  • Fig. 1 shows results.
  • a ball-on-disk test was performed on each of the sliding component and the self-lubricating property of each of the sliding components was evaluated. Test conditions are as follows. A change of the frictional coefficient was continuously measured until the sliding distance reached 100 m. Fig. 2 shows results.
  • the sliding components 1-A, 1-B, and 1-C being compositions which exhibited the self-lubricating property, galling did not occur until the sliding distance reached 100 m.
  • the value of the frictional coefficient during that period was maintained so as to be equal to or less than 0.30.
  • the self-lubricating property was synergistically improved, the frictional coefficient was more decreased, and the value thereof was equal to or less than 0.20.
  • Fig. 3 illustrates a relationship between the fatigue strength of each of the sliding components and the sliding distance when the frictional coefficient measured in the above descriptions reaches 0.20.
  • the value of the frictional coefficient which is "0.20" is an indicator of the frictional coefficient when the sliding component exhibits the synergistical self-lubricating property, in the test conditions of the example, as described above.
  • the fatigue strength is larger than 600 MPa.
  • the self-lubricating property was improved (the frictional coefficient was small) and the improved self-lubricating property was stably maintained at a long sliding distance, in comparison to the sliding components 1-A and 1-C.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)
  • General Details Of Gearings (AREA)
  • Lubricants (AREA)
EP16768870.4A 2015-03-26 2016-03-24 Élément coulissant et structure coulissante Withdrawn EP3276031A4 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015064365 2015-03-26
PCT/JP2016/059355 WO2016152967A1 (fr) 2015-03-26 2016-03-24 Élément coulissant et structure coulissante

Publications (2)

Publication Number Publication Date
EP3276031A1 true EP3276031A1 (fr) 2018-01-31
EP3276031A4 EP3276031A4 (fr) 2018-12-19

Family

ID=56978743

Family Applications (1)

Application Number Title Priority Date Filing Date
EP16768870.4A Withdrawn EP3276031A4 (fr) 2015-03-26 2016-03-24 Élément coulissant et structure coulissante

Country Status (5)

Country Link
EP (1) EP3276031A4 (fr)
JP (1) JP6424951B2 (fr)
KR (1) KR20170118904A (fr)
CN (1) CN107429356B (fr)
WO (1) WO2016152967A1 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6422044B2 (ja) * 2016-09-20 2018-11-14 日立金属株式会社 摺動構造体および摺動構造体の摺動方法
WO2019087562A1 (fr) * 2017-10-30 2019-05-09 Ｔｐｒ株式会社 Bague de pression, moteur à combustion interne, fil machine pour bague de pression, et procédé de fabrication de fil machine pour bague de pression
JP6472938B1 (ja) * 2017-10-30 2019-02-20 Ｔｐｒ株式会社 圧力リング、内燃機関、圧力リング用線材および圧力リング用線材の製造方法
CN115927967B (zh) * 2022-12-22 2024-10-01 美利林科技(攀枝花)有限公司 一种球磨机用高韧性钢锻的制备工艺

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0772330B2 (ja) * 1985-11-20 1995-08-02 日立金属株式会社 耐摩耗、摺動鉄系焼結材料
JP2709880B2 (ja) * 1992-06-11 1998-02-04 ニツコー熔材工業株式会社 過冷処理で硬化する鋼材
JP2003113443A (ja) * 2001-10-04 2003-04-18 Nkk Corp 表面粗さの方向性の少ない高加工性高強度熱延鋼板
WO2004059023A1 (fr) * 2002-12-25 2004-07-15 Hitachi Metals, Ltd. Acier a matrices froid presentant d'excellentes caracteristiques de suppression de la variation dimensionnelle
US20070006828A1 (en) * 2003-07-29 2007-01-11 Nippon Piston Ring Co., Ltd Cam lobe material, camshaft using the same and method for producing cam lobe member
JP4403875B2 (ja) * 2004-05-14 2010-01-27 大同特殊鋼株式会社 冷間工具鋼
JP4737606B2 (ja) * 2004-11-18 2011-08-03 日立金属株式会社 変寸抑制特性および耐カジリ性に優れた冷間ダイス鋼
RU2277135C1 (ru) * 2004-12-22 2006-05-27 Юрий Серафимович Булыгин Сталь
JP4844874B2 (ja) * 2005-05-26 2011-12-28 日立金属株式会社 プレス成形品の製造方法
CN100489141C (zh) * 2007-06-05 2009-05-20 北京钢研高纳科技股份有限公司 一种高温长寿自润滑耐磨合金材料
JP5076683B2 (ja) * 2007-06-29 2012-11-21 大同特殊鋼株式会社 高靭性高速度工具鋼
JP5276330B2 (ja) * 2008-01-10 2013-08-28 株式会社神戸製鋼所 冷間金型用鋼および冷間プレス用金型
CN101918605A (zh) * 2008-01-21 2010-12-15 日立金属株式会社 表面被覆处理用合金和滑动构件
WO2009119388A1 (fr) * 2008-03-27 2009-10-01 日立金属株式会社 Matériau de segment de piston pour moteur à combustion interne
CN102392199B (zh) * 2011-11-16 2013-05-29 钢铁研究总院 一种节材型耐热减摩自润滑材料

Also Published As

Publication number Publication date
WO2016152967A1 (fr) 2016-09-29
CN107429356A (zh) 2017-12-01
JP6424951B2 (ja) 2018-11-21
KR20170118904A (ko) 2017-10-25
CN107429356B (zh) 2019-09-20
JPWO2016152967A1 (ja) 2017-11-02
EP3276031A4 (fr) 2018-12-19

Similar Documents

Publication Publication Date Title
WO2014196614A1 (fr) Segment de piston, matériau brut pour celui-ci, et procédé de production pour les deux
US9849511B2 (en) Method of producing a Cu-based sintered sliding member
EP2101090B2 (fr) Segment de piston
EP3276031A1 (fr) Élément coulissant et structure coulissante
EP2209927B1 (fr) Revêtement résistant à la corrosion
EP3325194B1 (fr) Système tribologique comprenant un siège de soupape et une soupape
RU2674177C2 (ru) Высокотеплопроводное поршневое кольцо для двигателя внутреннего сгорания
EP3026141A1 (fr) Guide de soupape en alliage fritté et son procédé de production
EP3327320A1 (fr) Segment de piston et procédé de fabrication pour ce dernier
DE102013221687A1 (de) Wälzlagerring
PT2895639T (pt) Camada de proteção contra o desgaste para anéis de pistão
JPH02277764A (ja) 転がり軸受
JP5385039B2 (ja) 摺動性と表面圧縮残留応力を同時に付与するショットピーニング用粉末およびそれを用いた摺動性部材の製造方法
JP6422044B2 (ja) 摺動構造体および摺動構造体の摺動方法
JP6784869B2 (ja) ピストンリング
JP2021006659A (ja) 鋼部品およびその製造方法
DE102011080681A1 (de) Mediengeschmierte Lageranordnung zur Anwendung in einem korrosiven Medium, insbesondere Meerwasser
JP6587570B2 (ja) 内燃機関用ピストンリング線材及び内燃機関用ピストンリング
JP2021006660A (ja) 鋼部品およびその製造方法
HK1217312A1 (zh) 基於鐵的合金及其製備和使用方法

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20170906

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20181119

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/02 20060101ALI20181113BHEP

Ipc: C21D 6/00 20060101ALI20181113BHEP

Ipc: C22C 38/06 20060101ALI20181113BHEP

Ipc: C22C 38/58 20060101ALI20181113BHEP

Ipc: C21D 1/18 20060101ALI20181113BHEP

Ipc: C22C 38/48 20060101ALI20181113BHEP

Ipc: C22C 38/34 20060101ALI20181113BHEP

Ipc: C22C 38/60 20060101AFI20181113BHEP

Ipc: C22C 38/04 20060101ALI20181113BHEP

Ipc: C22C 38/00 20060101ALI20181113BHEP

Ipc: C22C 38/46 20060101ALI20181113BHEP

Ipc: C22C 38/42 20060101ALI20181113BHEP

Ipc: C22C 38/44 20060101ALI20181113BHEP

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20190521

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 9/40 20060101AFI20190729BHEP

Ipc: C22C 38/34 20060101ALI20190729BHEP

Ipc: C22C 38/48 20060101ALI20190729BHEP

Ipc: C22C 38/46 20060101ALI20190729BHEP

Ipc: C22C 38/44 20060101ALI20190729BHEP

Ipc: C22C 38/58 20060101ALI20190729BHEP

Ipc: C22C 38/60 20060101ALI20190729BHEP

Ipc: C22C 38/42 20060101ALI20190729BHEP

Ipc: C22C 38/06 20060101ALI20190729BHEP

Ipc: C22C 38/02 20060101ALI20190729BHEP

Ipc: C22C 38/00 20060101ALI20190729BHEP

Ipc: C21D 6/00 20060101ALI20190729BHEP

Ipc: C22C 38/04 20060101ALI20190729BHEP

Ipc: C21D 1/18 20060101ALI20190729BHEP

INTG Intention to grant announced

Effective date: 20190821

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20200103