[go: up one dir, main page]

WO2004092602A1 - Element de glissement - Google Patents

Element de glissement Download PDF

Info

Publication number
WO2004092602A1
WO2004092602A1 PCT/JP2004/005512 JP2004005512W WO2004092602A1 WO 2004092602 A1 WO2004092602 A1 WO 2004092602A1 JP 2004005512 W JP2004005512 W JP 2004005512W WO 2004092602 A1 WO2004092602 A1 WO 2004092602A1
Authority
WO
WIPO (PCT)
Prior art keywords
member according
sliding member
less
sliding
amorphous carbon
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.)
Ceased
Application number
PCT/JP2004/005512
Other languages
English (en)
Japanese (ja)
Inventor
Satoshi Takayanagi
Masahito Fujita
Takayuki Shibayama
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.)
Daido Metal Co Ltd
Original Assignee
Daido Metal Co 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 Daido Metal Co Ltd filed Critical Daido Metal Co Ltd
Priority to JP2005505486A priority Critical patent/JP4589229B2/ja
Priority to GB0521504A priority patent/GB2415753B/en
Priority to DE112004000651T priority patent/DE112004000651B4/de
Publication of WO2004092602A1 publication Critical patent/WO2004092602A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/10—Alloys containing non-metals
    • 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
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing

Definitions

  • the present invention relates to a sliding member having a sliding layer on a substrate.
  • a sliding member for example, a plain bearing for an engine in an automobile has a configuration in which a sliding layer (overlay) is provided on a base material.
  • Sn-based coating as the sliding layer is widely known as disclosed in Japanese Patent Application Laid-Open No. Sho 53-14614. It is well known that an overlay coating is formed using a soft metal base such as a Pb-based coating in addition to an Sn-based coating.
  • soft metals such as In and Bi have very low anti-seizure properties due to their low adhesion to mating materials such as Fe, so many conventional sliding members have been used. Has been used for sliding layers.
  • Abrasion resistance of the sliding layer ⁇ In order to improve the fatigue resistance, hard particles (for example, S i C, S i 3 N 4 ) were sometimes added by the composite plating technique. However, the hard particles to be added by the multiple plating technique have a large particle size from 0.1 m to several / zm. The distribution of hard particles often fluctuated in the overlay coating. In such a sliding layer, large hard particles or large hard particles are likely to damage the mating material, and the non-seizure property is reduced.
  • the A 1 -based coating is made of an Al—Sn alloy, with A 1 supporting the load, and soft Sn serving as conformability and non-seizure property.
  • the present invention has been made in view of the circumstances described above, and its purpose is to provide Sn,
  • the present invention provides a sliding layer on a substrate, wherein the sliding layer is made of any one of Sn, Pb, Bi, In, and A1 or an alloy based on the metal.
  • the substrate is characterized by adding amorphous carbon to the substrate.
  • the sliding layer can be formed by a dry plating method such as a sputtering method, an ion plating method, and a CVD method.
  • Sn, Pb, Bi, and In are extremely non-seizure due to their low adhesion to mating materials such as Fe. Are better.
  • the non-seizure property can be improved by using an alloy with another soft metal, for example, Sn. Even if the amount of Sn added is increased, A1 and Sn become finer due to the addition of amorphous carbon, resulting in high strength. For this reason, a defect such as a decrease in fatigue resistance does not occur, and a sliding layer excellent in both fatigue resistance and non-seizure properties can be obtained.
  • Amorphous carbon is high in hardness, so it increases mechanical strength and contributes to abrasion resistance and fatigue resistance. Also, the low coefficient of friction contributes to the improvement of non-seizure properties. Moreover, by adding amorphous carbon, the crystallites of the base material of the sliding layer are refined. With this, the mechanical strength of the sliding layer increases, and the wear resistance and fatigue resistance can be further improved.
  • the crystallite is a unit serving as a basis of particles in the sliding layer and a base containing the particles. Refinement of crystallites is, of course, the refinement of the substrate. In addition, as described later, crystallites can be confirmed by X-ray diffraction analysis, and particles can be confirmed by microscopic observation with a scanning electron microscope.
  • DLC diamond-like carbon
  • the crystallite diameter of the substrate measured by X-ray diffraction analysis is 100 nm or less.
  • Sn, Pb, Bi, Al, In, Cu, Sb, Ag, and Cd metals can be added to the base of the sliding layer.
  • Sn, Pb, Bi, In, and Al are metals that can also serve as a base material, and have a function of improving non-seizure, conformability, and corrosion resistance.
  • Cu, Sb, Ag, and Cd have the function of increasing the mechanical strength and hardness of the sliding layer. .
  • the additive metal is at least one of Sn, Pb, Bi, In, and A1
  • the content of each additive metal is 20% by mass or less
  • the total of these additive metals is Is preferably 30% by mass or less.
  • the base material is Sn and Al
  • the cases where the added metals are Al and Sn are excluded. If the content of each of these added metals exceeds 20% by mass or the total content of them exceeds 30% by mass, the melting point of the sliding layer is greatly reduced, and the non-seizure property tends to be reduced. There is.
  • the additional metal is at least one of Cu, Sb, Ag, and Cd
  • the content of each additional metal is 5% by mass or less, and the total content of these additional metals is Is preferably 10% by mass or less.
  • These added metals tend to form hard and brittle compounds with the base material of the sliding layer. Therefore, if the content of each of these added metals exceeds 5% by mass, or if the total content of them exceeds 10% by mass, the compound becomes large and easily falls off. Fatigue fracture and wear progress, and fatigue resistance and wear resistance tend to decrease.
  • A1 is used for the base material of the sliding layer, it is preferable to use an alloy with Sn, and the content thereof is 20 to 80% by mass for 1 and 20 to 80% by mass for Sn. 1.
  • the alloys of A1 and Sn that constitute the sliding layer include Si, Cu, Sb, In, and Ag. Any one or more of these metals can be added. In can improve non-seizure, conformability, and corrosion resistance.
  • Cu, Sb, and Ag increase the mechanical strength and hardness of the sliding layer. Since Si is a hard element, it increases the hardness of the sliding layer and improves fatigue resistance. In addition, Si functions as a hard material and has a function of removing metal adhered to a mating material, thereby improving non-seizure properties.
  • these Si, Cu, Sb, In, and Ag alone are 5% by mass or less, and the total content of the added metals is 10% by mass or less. .
  • each of In and Ag exceeds 5% by mass or the total content thereof exceeds 10% by mass, the melting point of the sliding layer is greatly reduced, and the non-seizure property is reduced.
  • Tend. Cu, Sb, and Ag form hard and brittle compounds with A1 and Sn, and the content of each of the added metals exceeds 5% by mass, or the total content thereof is 1%. If the content exceeds 0% by mass, the compound becomes large, so that it tends to fall off, and fatigue and wear tend to progress.
  • Si hardly forms a compound with A1 or Sn, and when Si is contained in a large amount, Si tends to easily fall off the sliding layer.
  • the Al-Sn alloy is refined by adding amorphous carbon.
  • the degree of the fineness is preferably 1 m or less in terms of the particle diameter of A1 or Sn. When the particle diameter is 1 zm or less, the effects of improving the fatigue resistance and the anti-seizure property are further improved.
  • the particle size is 0.05 or less.
  • the crystallite diameter can be 30 nm. When the crystallite diameter is so fine, more excellent fatigue resistance can be obtained.
  • Amorphous carbon hinders the growth of crystallites and crystallites are refined.
  • the substrate is a single metal such as Sn
  • the refinement can be confirmed by X-ray diffraction analysis, but the difference cannot be confirmed by the presence or absence of amorphous carbon in the cross-sectional structure observation with a scanning electron microscope.
  • Amorphous carbon also hinders growth of A 1 and Sn crystallites, and A 1 and Sn crystallites become finer Is done. This can be confirmed by X-ray diffraction analysis as described above.
  • a 1 and Sn can be observed as their respective phases. If there is a difference in the content of AIS n, the smaller is observed as particles. it can.
  • the crystallites of A1 and Sn become finer, and it becomes extremely difficult to capture the particles of A1 or Sn by cross-sectional structure observation with a scanning electron microscope.
  • a sliding layer made of any one of the above-mentioned metals of Sn, Pb, Bi, In, and A1 or an alloy based on the metal, and adding amorphous carbon to the substrate.
  • the content of amorphous carbon is preferably 0.1 to 8% by mass.
  • the content of the amorphous carbon is 0.1% by mass or more, the crystal of the substrate is sufficiently refined, and the hardness increases. Further, when the content is 8% by mass or less, the hardness is appropriately high, and the non-seizure property can be maintained without impairing the foreign matter embedding property.
  • FIG. 1 is a schematic sectional view of a sliding bearing according to an embodiment of the present invention.
  • Figure 2 is a schematic cross-sectional view showing the crystallites in the overlay
  • Fig. 3 shows the composition of the overlay used in the experiment to show the effect of the present invention and the experimental result.
  • Fig. 4 shows the condition of the fatigue test.
  • Figure 5 is a diagram for explaining the half width Figure 6 shows the measurement data of X-ray diffraction analysis of Comparative Example 1.
  • Figure ⁇ shows the measurement data of the X-ray diffraction analysis of Example 2.
  • FIG. 8 is a diagram showing an overlay configuration and an experimental result used in an experiment showing the effect of the present invention in another embodiment.
  • FIG. 9 shows the seizure test conditions
  • FIG. 10 is a schematic diagram of a structure observed by a scanning electron microscope of Example 12.
  • Fig. 11 is a schematic diagram of the structure observation by scanning electron microscope of Comparative Example 3 ... Best Mode for Carrying Out the Invention
  • FIG. 1 schematically shows a cross section of a sliding bearing as a sliding member.
  • the sliding bearing 1 includes a back metal 2 made of steel, a bearing alloy layer 3 provided on the upper surface of the back metal 2 in the drawing, and a sliding layer provided on the upper surface of the bearing alloy layer 3 in the drawing. It has a three-layer structure with the overlay 4.
  • the back metal 2 and the bearing alloy layer 3 constitute the base material 5, and the overlay 4 is provided on the base material 5.
  • the bearing alloy layer 3 an aluminum alloy or a copper alloy is generally used.
  • the overlay 4 is formed so as to have a thickness of 3 Om or less.
  • FIG. 3 shows the configurations of Examples 1 to 10 of the present invention and Comparative Example 1 for the overlay 4.
  • Sn of Sn, Pb, Bi, In, and Al was used as the base of the overlay 4, and an amorphous force (C) was used.
  • C amorphous force
  • Examples 4 and 8 a Sn-based Sn—Cu alloy is used as a base material, and amorphous carbon (C) is added to the Sn—Cu alloy.
  • a Pb-based Pb-Sn-Cu alloy and a Pb-Sn-In alloy were used, respectively, and amorphous carbon (C) was added to these alloys.
  • Bi and Al were used for the base material, respectively, and amorphous carbon (C) was added thereto.
  • Comparative Example 1 Sn was used alone, and amorphous carbon (C) was not added.
  • Examples 1 to 10 of the present invention and Comparative Example 1 were formed using a magneto opening / closing device.
  • the film forming methods of Examples 1, 3 to 10 and Comparative Example 1 are the same as the film forming method of Example 2.
  • the base material 5 is set in the base material mounting portion of the above-mentioned apparatus, and each target of Sn, which is a raw material of the base material of the overlay, and Graphite (Gr), which is a raw material of the amorphous carbon, is placed in a predetermined position. Attach to the target attachment section of the above device at a ratio
  • a bias voltage of 1000 V is applied, Ar plasma is generated between the substrate 5 and the target, and reverse sputtering is performed for 15 minutes.
  • a voltage is applied so that a current of 2 to 5 A flows to the Sn target and a current of 4 to 7 A flows to the Gr target.
  • the Sn atoms are sputtered by the collision of Ar ions, and a film is formed on the surface of the substrate 5.
  • carbon atoms are sputtered from the Gr target by the collision of Ar ions, and are added as amorphous carbon during the overlay.
  • an overlay 4 in which amorphous carbon is uniformly dispersed is formed in the Sn base.
  • methane (CH 4 ) gas is supplied into the chamber without using a Gr target, thereby adding DLC, which is amorphous carbon containing hydrogen atoms, to the Sn base. be able to.
  • the gas flowing into the device is changed to Ar gas and methane gas,
  • the flow ratio of methane gas to the amount is set to 20 to 50%.
  • Sn atoms are sputtered by Ar ions from the Sn target, and a film is formed on the surface of the substrate 5.
  • the methane gas is decomposed in the plasma and added to the Sn substrate as DLC consisting of C atoms and H atoms.
  • FIG. 2 schematically shows a cross-sectional view of the overlay of Example 2 formed as described above.
  • reference numeral 6 denotes a crystallite of Sn
  • reference numeral 8 denotes DLC.
  • the crystallite diameter of the Sn substrate is 100 nm or less.
  • the half width is a range of 2% where the intensity is higher than 1 p / 2 when the maximum intensity of the peak is lp.
  • ⁇ X-ray wavelength used for measurement
  • the obtained peak is separated into K or 1 peak and ⁇ 2 peak.
  • FIG. 6 corresponds to Comparative Example 1, and is an example in which the half-value width is obtained from the peak of, for example, the (3 1 2) plane of the overlay of S ⁇ alone, and the crystallite size is obtained.
  • the half width measured and calculated from the ⁇ 1 peak obtained from the (3 12) plane peak was 0.070 °.
  • the crystallite size was 150 nm.
  • Fig. 7 shows a sample corresponding to Example 2 (an example in which 2% by mass of amorphous carbon was added to the Sn base material), in which the peak of the (312) plane of the overlay was observed.
  • This is an example in which the half-width is determined from the above to determine the crystallite size.
  • the half width measured and calculated from the K 1 peak obtained from the (3 12) plane peak was 0.307 °. As a result, the crystallite size was 34 nm.
  • Example 2 the same measurement was performed on Examples 1 and 3 to 10 other than Example 2.
  • the diameter of the crystallites of the base material was 1.0 O nm or less in each case.
  • the diameter of crystallite 1 was 3 O nm or less. chorus.
  • FIG. 3 also shows the measurement results of the hardness of the overlay (sliding layer). .
  • Comparative Example 1 is a case where the bare is Sn alone. In this case, it can be seen that the Vickers hardness is low and the fatigue resistance is poor. On the other hand, in Examples 1 to 10, the Beakers hardness was hardened to 20 or more in all cases, and it was found that the fatigue resistance was superior to that of Comparative Example 1.
  • Examples 1 to 10 will be examined in more detail.
  • Example 1 is relatively low in hardness and particularly excellent in foreign matter embedding property, and Examples 2 and 3 are non-fatigue maximum.
  • the surface pressure is 12 OMPa or more, and the fatigue resistance is particularly excellent.
  • the content of the amorphous carbon (C) is preferably from 0.1 to 8.0% by mass, more preferably from 0.5 to 6% by mass.
  • Example 2 and Example 4 will be compared. Although the content of the amorphous carbon (C) is the same, in Example 4, Cu was added, and the fatigue resistance was higher than in Example 2 in which Cu was not added. This is considered to be because the addition of Cu increases the mechanical strength and hardness of the sliding layer and increases the fatigue resistance.
  • Example 4 and Example 8 will be compared. The content of amorphous carbon (C) is the same, but in Example 4, the content of Cu was 2% by mass, and the content of Cu exceeded 5% by mass from Example 8 Also the fatigue resistance is improved.
  • Pb is used as a base material, and amorphous silicon, Sn. And In are added thereto.
  • A1 was used as a base material, and amorphous carbon was added thereto. Also in this case, it is excellent in fatigue resistance as in the other examples. From the above results, in Examples 1 to 10 of the present invention, any one of Sn, .Pb, Bi, In, and A1 or an alloy based on the metal was overlayed. It can be seen that a sliding member having particularly excellent fatigue resistance can be provided by using the base material.
  • FIG. 8 to 11 show another embodiment of the present invention. This embodiment is directed to a case where the base material of the single valley 4 shown in FIG. 1 is an A1-Sn alloy.
  • FIG. 8 shows the compositions of Examples 11 to 22 and Comparative Examples 2 and 3 of the present invention.
  • Examples 11 to 16 are obtained by adding amorphous carbon to an A1-Sn alloy based on A1, and Examples 17 to 20 are obtained based on Sn.
  • Example 21 is a sample in which Si and amorphous carbon are added to an A 1 -Sn alloy based on A 1
  • Example 22 is an A 1 -S n alloy based on A 1. It is made by adding Cu and amorphous carbon to an alloy.
  • the base material was an A1-Sn alloy based on A1 and no amorphous carbon was added.
  • Film formation of the overlay 4 of Examples 11 to 22 and Comparative Examples 2 and 3 was performed in the same manner as the film formation of Example 2 described above.
  • a single metal of Sn and A1 or an A1-Sn alloy preliminarily alloyed by a structure can be used as a target.
  • FIG. 10 is a schematic diagram of the cross section of the overlay of Example 12 observed with a scanning electron microscope
  • FIG. 11 is a schematic diagram of the cross section of the overlay of Comparative Example 3 observed with a scanning electron microscope. It is. .
  • the particles of Sn in A1 can be captured by a scanning electron microscope, and the particles of Sn have a small particle size, but are generally larger than 1 Atm.
  • Example 12 in which the amorphous carpon was added as shown in FIG. 1.0, the particles of A 1 and Sn were not visible.
  • the reason for this is that the particles in [81] [3] 1 were too small to be detected by the scanning electron microscope used, and similar results were obtained if no particles were present in the overlay.
  • the crystallite size of the overlay of the sample of Example 12 was measured by X-ray diffraction analysis, the crystallite size of A1 was 18 nm, and the crystallite size of Sn was ⁇ 5 nm. Met.
  • FIG. 9 shows the seizure test conditions.
  • the surface pressure was increased by 5 Pa after the running-in operation, and the maximum surface pressure without seizure was determined.
  • FIG. 8 also shows the measurement results of the Beakers hardness of the overlay.
  • DLC is a substance with a small coefficient of friction.As can be understood from the comparison between Example 11 and Comparative Example 2 where the Sn content is the same, if DLC is contained, non-seizure occurs. The performance is improved.
  • the anti-seizure property is improved as the added amount of Sn is increased.
  • the following two reasons are considered for the improvement of non-seizure property with the increase of Sn content.
  • Lubricating oil plays a very important role in sliding. Lubricating oil exists between the two sliding members, and seizure does not occur when an oil film is formed. For this reason, the overlay of the slide bearing is preferably made of a material that can easily form an oil film.
  • the wettability with lubricating oil which is a parameter that indicates the ease with which an oil film is formed, is higher for Sn than for A1. For this reason, the non-seizure property increases as the overlay contains more Sn. This is the first reason.
  • the second reason is as follows. If oil runs out between two sliding members, frictional heat is generated. When the oil film starts to partially break, frictional heat is generated only locally, but when the area ratio at which the oil film breaks increases, the frictional heat increases, and an adhesion reaction occurs between the two members. And burn. However, if a low melting point metal, Sn, is present in the overlay, it will locally melt when the oil slick begins to partially break. Since the latent heat at that time absorbs the frictional heat, the frictional heat is not accumulated, and as a result, seizure is prevented.
  • the improvement of the fatigue resistance and anti-seizure property by adding the Sn content when amorphous carbon is added is not limited to the Al-Sn alloy based on A1, but is shown in Examples 17 to 20.
  • the 8 1-31 1 alloy based on 3] is also improved in non-seizure properties while maintaining excellent fatigue resistance by increasing the Sn content in the same manner. be able to.
  • fatigue resistance can be improved by including Si and Cu, and in particular, Si is included. When it is included, the non-seizure property can be improved at the same time.
  • the overlay 4 is provided directly on the upper surface of the bearing alloy layer 3.However, an intermediate layer such as Ni--Cr or Ti is provided on the upper surface of the bearing alloy layer 3, and this intermediate layer is formed.
  • the overlay 4 may be provided on the upper surface. Further, the overlay 4 may be provided directly on the upper surface of the back metal 2. Further, a conformable layer of a soft metal such as pure Sn or a resin such as PAI may be provided on the upper surface of the overlay 4.
  • the base of the overlay 4 may be made of In. Further, the added metal for increasing the mechanical strength and hardness of the overlay 4 is not limited to 11, but may be any one of Sb, Ag, and Cd, or two or more of them may be used. . Industrial applicability
  • the sliding member according to the present invention is useful as a slide bearing in which a sliding layer having a thickness of 30 zm or less called an overlay is formed on a bearing alloy.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • General Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Sliding-Contact Bearings (AREA)
  • Physical Vapour Deposition (AREA)

Abstract

L'invention concerne un élément de glissement comprenant un substrat ainsi qu'une couche de glissement (couche de recouvrement). La couche de recouvrement (couche de glissement) (4) comporte un matériau de base qui se présente sous la forme d'un métal sélectionné entre Sn, Pb, Bi, In, et Al ou d'un alliage à base dudit métal, ainsi qu'un carbone amorphe utilisé en tant qu'additif. La couche de recouvrement (4) est formée par pulvérisation cathodique. Les éléments Sn, Pb, Bi et In présentent d'excellentes propriétés anti-grippage dans la mesure où ils n'adhèrent que faiblement à un matériau auquel ils sont accouplés tel que Fe. Le carbone amorphe améliore la résistance à l'usure ainsi que la résistance à la fatigue grâce à son degré élevé de dureté et améliore en outre les propriétés anti-grippage de par son faible coefficient de frottement. En outre, l'addition de carbone amorphe permet de former un matériau de base présentant des grains cristallins plus fins, ce qui améliore la résistance mécanique et renforce la résistance à l'usure ainsi que la résistance à la fatigue de la couche de recouvrement (couche de glissement).
PCT/JP2004/005512 2003-04-17 2004-04-16 Element de glissement Ceased WO2004092602A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
JP2005505486A JP4589229B2 (ja) 2003-04-17 2004-04-16 摺動部材
GB0521504A GB2415753B (en) 2003-04-17 2004-04-16 Sliding member
DE112004000651T DE112004000651B4 (de) 2003-04-17 2004-04-16 Gleitelement

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2003-112803 2003-04-17
JP2003112803 2003-04-17

Publications (1)

Publication Number Publication Date
WO2004092602A1 true WO2004092602A1 (fr) 2004-10-28

Family

ID=33296067

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2004/005512 Ceased WO2004092602A1 (fr) 2003-04-17 2004-04-16 Element de glissement

Country Status (4)

Country Link
JP (1) JP4589229B2 (fr)
DE (1) DE112004000651B4 (fr)
GB (1) GB2415753B (fr)
WO (1) WO2004092602A1 (fr)

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007033709A1 (fr) * 2005-09-20 2007-03-29 Ks Gleitlager Gmbh Materiau composite de palier a glissement
JP2007270893A (ja) * 2006-03-30 2007-10-18 Daido Metal Co Ltd 摺動部材
JP2008540839A (ja) * 2005-05-13 2008-11-20 フエデラル―モーグル・ウイースバーデン・ゲゼルシヤフト・ミト・ベシユレンクテル・ハフツング 滑り軸受け複合材料、使用及び製造法
JP2008540838A (ja) * 2005-05-13 2008-11-20 フエデラル―モーグル・ウイースバーデン・ゲゼルシヤフト・ミト・ベシユレンクテル・ハフツング 滑り軸受け複合材料、使用及び製造法
JP2009264441A (ja) * 2008-04-23 2009-11-12 Daido Metal Co Ltd 摺動部材
WO2012005325A1 (fr) * 2010-07-09 2012-01-12 大同メタル工業株式会社 Élément de glissement
JP2012246945A (ja) * 2011-05-25 2012-12-13 Daido Metal Co Ltd Ａｌ合金軸受
JP2013119633A (ja) * 2011-12-06 2013-06-17 Toyota Motor Corp 摺動部材
JP2015527535A (ja) * 2012-06-13 2015-09-17 マーレ メタル レーベ ソシエダーデ アノニマＭＡＨＬＥ Ｍｅｔａｌ Ｌｅｖｅ Ｓ／Ａ 内燃機関用ベアリング
WO2015159842A1 (fr) * 2014-04-15 2015-10-22 大豊工業株式会社 Elément coulissant et palier coulissant

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06108229A (ja) * 1992-09-28 1994-04-19 Daido Metal Co Ltd 非焼付性に優れたオーバーレイを有するすべり軸受材料
JP2000119791A (ja) * 1998-10-09 2000-04-25 Taiho Kogyo Co Ltd すべり軸受用アルミニウム合金及びその製造方法
JP2000129280A (ja) * 1998-10-26 2000-05-09 Toyota Central Res & Dev Lab Inc 硬質非晶質炭素分散複合材料
JP2004018979A (ja) * 2002-06-19 2004-01-22 Toyota Motor Corp 複合めっき皮膜

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5220336A (en) * 1975-08-08 1977-02-16 Daido Metal Co Ltd Multilayer sliding material and its production method
GB1523665A (en) * 1976-06-23 1978-09-06 Daido Metal Co Ltd Bearing materials
GB8808323D0 (en) * 1988-04-08 1988-05-11 T & N Technology Ltd Improvements in/relating to coating of metal substrates
JPH07252693A (ja) * 1994-03-17 1995-10-03 Daido Metal Co Ltd 複合めっき皮膜を有するすべり軸受
DE19963385C1 (de) * 1999-12-28 2001-01-25 Federal Mogul Wiesbaden Gmbh Schichtverbundwerkstoff für Gleitlager

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06108229A (ja) * 1992-09-28 1994-04-19 Daido Metal Co Ltd 非焼付性に優れたオーバーレイを有するすべり軸受材料
JP2000119791A (ja) * 1998-10-09 2000-04-25 Taiho Kogyo Co Ltd すべり軸受用アルミニウム合金及びその製造方法
JP2000129280A (ja) * 1998-10-26 2000-05-09 Toyota Central Res & Dev Lab Inc 硬質非晶質炭素分散複合材料
JP2004018979A (ja) * 2002-06-19 2004-01-22 Toyota Motor Corp 複合めっき皮膜

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008540839A (ja) * 2005-05-13 2008-11-20 フエデラル―モーグル・ウイースバーデン・ゲゼルシヤフト・ミト・ベシユレンクテル・ハフツング 滑り軸受け複合材料、使用及び製造法
JP2008540838A (ja) * 2005-05-13 2008-11-20 フエデラル―モーグル・ウイースバーデン・ゲゼルシヤフト・ミト・ベシユレンクテル・ハフツング 滑り軸受け複合材料、使用及び製造法
WO2007033709A1 (fr) * 2005-09-20 2007-03-29 Ks Gleitlager Gmbh Materiau composite de palier a glissement
JP2007270893A (ja) * 2006-03-30 2007-10-18 Daido Metal Co Ltd 摺動部材
JP2009264441A (ja) * 2008-04-23 2009-11-12 Daido Metal Co Ltd 摺動部材
US9051967B2 (en) 2010-07-09 2015-06-09 Daido Metal Company Ltd. Sliding member
GB2500974A (en) * 2010-07-09 2013-10-09 Daido Metal Co Sliding member
WO2012005325A1 (fr) * 2010-07-09 2012-01-12 大同メタル工業株式会社 Élément de glissement
GB2500974B (en) * 2010-07-09 2016-07-27 Daido Metal Co Sliding Bearing
JP2012246945A (ja) * 2011-05-25 2012-12-13 Daido Metal Co Ltd Ａｌ合金軸受
JP2013119633A (ja) * 2011-12-06 2013-06-17 Toyota Motor Corp 摺動部材
JP2015527535A (ja) * 2012-06-13 2015-09-17 マーレ メタル レーベ ソシエダーデ アノニマＭＡＨＬＥ Ｍｅｔａｌ Ｌｅｖｅ Ｓ／Ａ 内燃機関用ベアリング
WO2015159842A1 (fr) * 2014-04-15 2015-10-22 大豊工業株式会社 Elément coulissant et palier coulissant
JP2015203461A (ja) * 2014-04-15 2015-11-16 大豊工業株式会社 摺動部材およびすべり軸受

Also Published As

Publication number Publication date
JPWO2004092602A1 (ja) 2006-07-06
JP4589229B2 (ja) 2010-12-01
GB0521504D0 (en) 2005-11-30
DE112004000651T5 (de) 2006-02-16
GB2415753A (en) 2006-01-04
DE112004000651B4 (de) 2012-05-31
GB2415753B (en) 2006-09-13

Similar Documents

Publication Publication Date Title
KR101953634B1 (ko) 내마모 무연 합금 슬라이딩 요소 및 제조 방법
JP4961073B2 (ja) 滑り軸受用複合層材料
CN1312304C (zh) 轴承部件
CN101873928B (zh) 制造具有含铋滑动层的滑动轴承元件的方法
US20010021353A1 (en) Copper alloy sliding material
KR100814656B1 (ko) Ｐｂ 를 함유하지 않은 구리 합금 접동 재료
WO2004092602A1 (fr) Element de glissement
Wang et al. Microstructure and properties of laser-cladded FeCoCrNiMnSix high-entropy alloy coatings with varying Si contents
JP6249533B2 (ja) ナノ複合固体潤滑被膜
KR100413721B1 (ko) 다층재료
JP2003156045A (ja) 摺動部材
CN103492737B (zh) 轴承衬、制造轴承衬的方法、车辆用发动机以及粒度降低添加剂的用途
KR102174328B1 (ko) 저마찰 코팅막이 형성된 타펫 및 그 제조방법
JP4224338B2 (ja) 摺動部材
Sharma et al. Dry sliding wear behavior of Sn and NiSn overlays on Cu connectors
KR102154823B1 (ko) 저마찰 코팅막이 형성된 피스톤 링 및 그 제조방법
Ilie et al. Tribological properties of solid lubricant nanocomposite coatings obtained by magnetron sputtered of MoS2/metal (Ti, Mo) nanoparticles
Sharma et al. Microstructure–wear resistance correlation and wear mechanisms of spark plasma sintered Cu-Pb nanocomposites
KR102174327B1 (ko) 저마찰 코팅막이 형성된 피스톤 핀 및 그 제조방법
JP7693498B2 (ja) 滑り軸受及びその製造方法
Sanchez et al. Wear Properties of an In-Situ Processed TiC-Reinforced Bronze
Ono et al. Lead-free bearing material for highly loaded engines
EP0571481A1 (fr) Paliers.
An et al. The formation of reacted film and its influence on tribological properties of extruded Al-Si-Cu-20-25Pb alloy under dry sliding
Kato et al. The lubricating properties of tribo-coating films of Pb-Sn alloys in high vacuum

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BW BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE EG ES FI GB GD GE GH GM HR HU ID IL IN IS JP KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NA NI NO NZ OM PG PH PL PT RO RU SC SD SE SG SK SL SY TJ TM TN TR TT TZ UA UG US UZ VC VN YU ZA ZM ZW

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): BW GH GM KE LS MW MZ SD SL SZ TZ UG ZM ZW AM AZ BY KG KZ MD RU TJ TM AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LU MC NL PL PT RO SE SI SK TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG

121 Ep: the epo has been informed by wipo that ep was designated in this application
WWE Wipo information: entry into national phase

Ref document number: 2005505486

Country of ref document: JP

WWE Wipo information: entry into national phase

Ref document number: 0521504

Country of ref document: GB

RET De translation (de og part 6b)

Ref document number: 112004000651

Country of ref document: DE

Date of ref document: 20060216

Kind code of ref document: P

WWE Wipo information: entry into national phase

Ref document number: 112004000651

Country of ref document: DE

DPEN Request for preliminary examination filed prior to expiration of 19th month from priority date (pct application filed from 20040101)
122 Ep: pct application non-entry in european phase
REG Reference to national code

Ref country code: DE

Ref legal event code: 8607

REG Reference to national code

Ref country code: DE

Ref legal event code: 8607