US20120107168A1 - Iron-based sintered sliding member and manufacturing method thereof - Google Patents

Iron-based sintered sliding member and manufacturing method thereof Download PDF

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US20120107168A1
US20120107168A1 US13/381,874 US201013381874A US2012107168A1 US 20120107168 A1 US20120107168 A1 US 20120107168A1 US 201013381874 A US201013381874 A US 201013381874A US 2012107168 A1 US2012107168 A1 US 2012107168A1
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iron
sliding member
based sintered
sintered sliding
mass
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Yasuhiro Shirasaka
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Oiles Corp
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Oiles Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F3/26—Impregnating
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0207—Using a mixture of prealloyed powders or a master alloy
    • C22C33/0228—Using a mixture of prealloyed powders or a master alloy comprising other non-metallic compounds or more than 5% of graphite
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/05—Alloys based on copper with manganese as the next major constituent
    • 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
    • F16C33/10—Construction relative to lubrication
    • F16C33/1025—Construction relative to lubrication with liquid, e.g. oil, as lubricant
    • F16C33/103—Construction relative to lubrication with liquid, e.g. oil, as lubricant retained in or near the bearing
    • F16C33/104—Construction relative to lubrication with liquid, e.g. oil, as lubricant retained in or near the bearing in a porous body, e.g. oil impregnated sintered sleeve
    • 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
    • F16C33/121—Use of special materials
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • the present invention relates to an iron-based sintered sliding member having excellent tribological property and a manufacturing method thereof.
  • iron-based materials are iron-carbon type or iron-copper-carbon type bearing materials impregnated with liquid lubricant (lubricating oil) and iron-carbon type or iron-copper-carbon type sintered materials (See Non-Patent Document 1, for example).
  • liquid lubricant lubricating oil
  • iron-carbon type or iron-copper-carbon type sintered materials See Non-Patent Document 1, for example.
  • iron powder reacts with carbon powder in the course of sintering, causing the phenomenon of precipitation of free cementite (Fe 3 C) of high hardness in the sinter structure.
  • This precipitation of free cementite of high hardness in the structure raises a problem of damaging the opposite member, for example an axle in the event of sliding against the axle (the opposite member). In the sliding use, it is an important point to avoid this phenomenon as much as possible.
  • the following methods can provide a certain degree of solution: (1) mixing of a small amount, for example 0.82 mass percent or less, of carbon (graphite); and (2) sintering at a low temperature, for example 1000 degrees Celsius or less, at which free cementite does not precipitate.
  • the method (1) cannot be expected to provide the solid lubricating action of mixed carbon.
  • sinter alloying is not sufficient to give high mechanical strength, and thus it is difficult to apply the method to the sliding use.
  • iron-based sintered materials obtained by these methods can not realize sufficient solid lubricating action of the contained carbon.
  • an object of the present invention is to provide an iron-based sintered sliding member that has no precipitation of free cementite in its structure and has excellent tribological property such as friction and wear, and to provide its manufacturing method.
  • the present inventor focused the attention on copper and manganese as elements that promote generation of ferrite phase ( ⁇ phase) structure. And, when copper and manganese are mixed in the form of copper-iron-manganese master alloy into an iron-carbon-X (metallic element) type sintering material at a prescribed ratio, the inventor found that copper and manganese are sufficiently diffused into the ⁇ phase structure to be solid-state solution in it, and the copper-iron-manganese master alloy is contained and diffused in the ⁇ phase structure without no precipitation of free cementite in the ⁇ phase structure, thus providing excellent tribological property.
  • the iron-based sintered sliding member of the present invention has been invented on the basis of the above finding, and is made from iron powder, copper-iron-manganese alloy powder, and carbon powder.
  • the iron-based sintered sliding member is characterized in that: it comprises 2.67-18.60 mass % copper component, 0.12-1.20 mass % manganese component, 1.0-5.0 mass % carbon component, and iron component as a remaining part; the matrix presents pearlite structure or structure in which pearlite partially coexists with ferrite; no free cementite precipitates in the structure of the matrix; and copper-iron-manganese alloy is dispersedly contained in the structure of the matrix.
  • the copper-iron-manganese mother alloy dispersedly contained in the structure of the matrix may be dispersedly contained in net-like forms at grain boundary of the structure of the matrix.
  • the copper-iron-manganese mother alloy dispersedly contained in the structure of the matrix shows the hardness of 100-120 in terms of the micro Vickers hardness (HMV).
  • the structure of the matrix i.e. the pearlite structure or the structure in which pearlite partially coexists with ferrite shows the hardness of 350-450 in terms of the micro Vickers hardness (HMV).
  • the pearlite structure of the matrix or the structure of the matrix in which pearlite partially coexists with ferrite dispersedly contains the copper-iron-manganese alloy having the lower hardness than the hardness of the structures. Accordingly, running-in ability of the sliding surface with the opposite member such as a rotating shaft is improved, and the tribological property are improved.
  • natural graphite or artificial graphite can be used as the carbon.
  • This carbon is dispersedly contained in the proportion of 1-5 mass % in the structure of the matrix, i.e. the pearlite structure or the structure of the matrix in which pearlite partially coexists with ferrite.
  • the carbon has a solid lubrication action in itself, and functions as a retaining agent for a lubricant oil later.
  • the mixing ratio of the carbon is 3 mass % or more, self-lubrication is realized due to the solid lubrication action of carbon.
  • lubricant oil is contained in the proportion of 10-15 volume %.
  • the lubricant oil gives a liquid lubrication action to the iron-based sintered sliding member. At the same time, together with the solid lubrication action of the carbon, the self-lubricating effect is increased.
  • An iron-based sintered sliding member manufacturing method of the present invention comprises:
  • alloy powder which comprises 4-6 mass % manganese, 3-5 mass % iron, and copper as a remaining part, and 1-5 mass % carbon powder to iron powder as a main component, and mixing the alloy powder and the carbon powder, to make powder mixture;
  • the iron-based sintered sliding member obtained by this manufacturing method comprises 2.67-18.6 mass % copper component, 0.12-1.2 mass % manganese, 1.0-5.0 mass % carbon component, and iron component as a remaining part.
  • the structure of the matrix presents pearlite structure or structure in which pearlite partially coexists with ferrite. No free cementite precipitates in the structure, and the copper-iron-manganese alloy is dispersedly contained in the structure of the matrix.
  • the copper-iron-manganese alloy powder as a component part becomes a liquid phase at a temperature of 1050 degrees Celsius.
  • the sintering becomes solid-phase sintering.
  • the sintering becomes liquid-phase sintering.
  • its matrix presents pearlite structure or structure in which pearlite partially coexists with ferrite. No free cementite precipitates in the structures.
  • the copper-iron-manganese alloy is dispersedly contained in the structure of the matrix.
  • the iron-based sintered sliding member obtained by liquid-phase sintering its matrix presents pearlite structure or structure in which pearlite partially coexists with ferrite, and no free cementite precipitates in the structures, densifying the sintered sliding member to improve its mechanical strength.
  • the copper-iron-manganese alloy is dispersedly contained in net-like forms at grain boundary of the structure of the matrix.
  • the iron-based sintered sliding member obtained by solid-phase sintering or liquid-phase sintering contains copper and manganese i.e. elements promoting generation of ferrite phase ( ⁇ phase) structure.
  • the matrix presents pearlite structure or structure in which pearlite partially coexists with ferrite, and no free cementite precipitates in the structures.
  • the present invention provides an iron-based sintered sliding member made from iron powder, copper-iron-manganese alloy powder, and carbon powder, and a manufacturing method thereof, the iron-based sintered sliding member comprising 2.67-18.6 mass % copper component, 0.12-1.2 mass % manganese component, 1.0-5.0 mass % carbon component, and iron component as a remaining part, wherein its matrix presents pearlite structure or structure in which pearlite partially coexists with ferrite and the copper-iron-manganese alloy is dispersedly contained in the structure of the matrix to shows good running-in ability and excellent tribological property.
  • FIG. 1 is a microphotograph (at a magnification of 200 times) of an iron-based sintered sliding member obtained by solid-phase sintering at a temperature of 1000 degrees Celsius, comprising 85 mass % iron component, 12 mass % copper-iron-manganese alloy component, and 3 mass % carbon component;
  • FIG. 2 is a microphotograph (at a magnification of 200 times) of iron-based sintered sliding member obtained by liquid-phase sintering at a temperature of 1100 degrees Celsius, comprising 85 mass % iron component, 12 mass % copper-iron-manganese alloy component, and 3 mass % carbon component;
  • FIG. 3 is a microphotograph at a magnification of 400 times of FIG. 2 ;
  • FIG. 4 is an image taken with a scanning electron microscope (SEM) of a copper-iron-manganese alloy site (the site displayed as a rectangular in this figure) precipitated at a grain boundary of structure of the matrix of an iron-based sintered sliding member, where pearlite partially coexistent with ferrite, with the sliding member being obtained by liquid-phase sintering at a temperature of 1100 degrees Celsius and comprising 85 mass % iron component, 12 mass % copper-iron-manganese alloy component, and 3 mass % carbon component;
  • SEM scanning electron microscope
  • FIG. 5 is an image taken with a scanning electron microscope (SEM) of a site (the side displayed as a rectangular in this figure) of structure of the matrix of an iron-based sintered sliding member, where pearlite partially coexistent with ferrite, with the sliding member being obtained by liquid-phase sintering at a temperature of 1100 degrees Celsius and comprising 85 mass % iron component, 12 mass % copper-iron-manganese alloy component, and 3 mass % carbon component;
  • SEM scanning electron microscope
  • FIG. 6 is a perspective view showing a method of thrust test
  • FIG. 7 is a perspective view showing a method of journal oscillation test.
  • FIG. 8 is a perspective view showing a method of journal rotation test.
  • An iron-based sintered sliding member of the present invention is one containing iron component, copper-iron-manganese alloy component, and carbon component, and is characterized in that it comprises 2.67-18.60 mass % copper component, 0.12-1.20 mass % manganese component, 1.0-5.0 mass % carbon component, and iron component as the remaining part; its matrix presents pearlite structure or structure where pearlite partially coexists with ferrite; and the structure of the matrix dispersedly contains carbon component and copper-iron-manganese alloy component.
  • the iron-based sintered sliding member of the present invention it is favorable to use, as the main component iron, reduced iron powder or atomized iron powder (water atomized iron powder), each powder having a grain size (177 ⁇ m or less) that can sift through an 80 mesh sieve, and apparent density of about 2.4-3.0 Mg/m 3 .
  • Specific surface areas of these iron powders measured by the gas adsorption method are 60-80 m 2 /kg in the case of the atomized iron powder and 80-100 m 2 /kg in the case of the reduced iron powder.
  • the atomized iron powder has a relatively-small number of gas cavities within its powder particles, and thus its specific surface area is small.
  • the reduced iron powder has a relatively-large number of gas cavities, and their surfaces are hubbly.
  • the specific surface area of the reduced iron powder is larger than that of the atomized iron powder.
  • Copper component and manganese component which are blended with the main component iron at predetermined ratios, are used in the form of copper-iron-manganese alloy.
  • These copper and manganese components in this alloy are elements that promote generation of ferrite phase ( ⁇ phase) structure, and act so as to inhibit the below-described reaction between the iron component as the main component and the carbon component in the process of sintering, and thus to prevent precipitation of free cementite in the structure of the matrix of the sintered compact. Details of this action of the copper and manganese components of inhibiting the reaction between the iron component and the carbon component in the process of sintering have not been made clear. However, it is inferred that this is because previous alloying of these elements leads to preferential solid-state solution of the copper and manganese components into the iron component as the main component, and this prevents solid-state solution of the carbon component into the iron component largely.
  • the component composition of this copper-iron-manganese alloy component is 89-93 mass % copper component, 3-5 mass % iron component, and 4-6 mass % manganese component.
  • This copper-iron-manganese alloy powder is blended in the proportion of 3-20 mass % with the iron component as the main component.
  • the copper component is blended in the proportion of 2.67-18.6 mass %, the iron component in the proportion of 0.09-1.0 mass %, and the manganese component in the proportion of 0.12-1.2 mass % with the iron component.
  • the copper-iron-manganese alloy component mentioned above has its liquid phase point at a temperature of 1050 degrees Celsius, and its sintering is solid-phase sintering at a temperature lower than 1050 degrees Celsius and liquid-phase sintering at a temperature of 1050 degrees Celsius or higher.
  • the copper-iron-manganese alloy component is dispersedly contained in the pearlite structure of the matrix or the structure in which pearlite partially coexists with ferrite.
  • the copper-iron-manganese alloy component is dispersedly contained in net-like forms at grain boundaries of the pearlite structure of the matrix or the structure in which pearlite partially coexists with ferrite.
  • FIG. 1 is a microphotograph (at a magnification of 200 times) of an iron-based sintered sliding member obtained by solid-phase sintering at a temperature of 1000 degrees Celsius, comprising 85 mass % iron, 12 mass % copper-iron-manganese alloy, and 3 mass % carbon;
  • FIG. 2 is a micrograph (at a magnification of 200 times) of an iron-based sintered sliding member obtained by liquid-phase sintering at a temperature of 1100 degrees Celsius, comprising 85 mass % iron, 12 mass % copper-iron-manganese alloy, and 3 mass % carbon;
  • FIG. 3 is a microphotograph at a magnification of 400 times of FIG. 2 .
  • white-looking parts dispersed in the structure of the matrix in which pearlite partially coexists with ferrite are the copper-iron-manganese alloy component.
  • white-looking parts dispersed in net-like forms at grain boundaries of the structure of the matrix in which pearlite partially coexists with ferrite are the copper-iron-manganese alloy component.
  • FIGS. 4 and 5 are images taken with a scanning electron microscope (SEM) of an iron-based sintered sliding member obtained by liquid-phase sintering at a temperature of 1100 degrees Celsius, comprising 85 mass % iron component, 12 mass % copper-iron-manganese alloy component, and 3 mass % carbon component.
  • FIG. 4 is an image of a copper-iron-manganese alloy site (the site displayed as a rectangular in the figure) dispersed at a grain boundary of structure of the matrix in which pearlite partially coexists with ferrite.
  • the component composition of the site is shown to be 89.25 mass % copper component, 0.80 mass % manganese component, and 9.68 mass % iron component.
  • FIG. 5 is an image of a site (the site displayed as a rectangular in the figure) of structure of the matrix in which pearlite coexists partially with ferrite.
  • the component composition of the site is shown to be 93.56 mass % iron component, 5.09 mass % copper component, and 1.35 mass % manganese component.
  • hardness of the site of the structure of the matrix in which pearlite partially coexists with ferrite and the site of copper-iron-manganese alloy dispersedly contained in the structure is 350-450 in terms of the micro Vickers hardness (HMV) with respect to the site of the structure of the matrix in which the pearlite partially coexists with ferrite, and 100-120 in terms of the micro Vickers hardness with respect to the site of copper-iron-manganese alloy.
  • HMV micro Vickers hardness
  • the copper-iron-manganese alloy which is dispersedly contained in the structure of the matrix where the pearlite partially coexists with ferrite has lower hardness than that of the site of that structure, the running-in ability at the time of sliding on the opposite member becomes better, and the tribological property are improved.
  • powder mixture (10.86 mass % copper component, 0.65 mass % manganese component, 85.49 mass % iron, and 3 mass % carbon component). Then, this powder mixture was filled in a mold and compacted at a compacting pressure of 5 ton/cm 2 , to obtain a green compact of a rectangular shape.
  • This rectangular-shaped green compact was placed in a heating furnace whose inside was adjusted to be a hydrogen gas atmosphere, subjected to solid-phase sintering at a temperature of 1000 degrees Celsius for 60 minutes, and then taken out of the heating furnace, to obtain a rectangular-shaped iron-based sintered material.
  • This iron-based sintered material was machined to obtain an iron-based sintered sliding member measuring 30 mm in each side length and 5 mm in thickness.
  • the density of this iron-based sintered sliding member was shown to be 6.2 g/cm 3 , and, as for its structure, it was ascertained that it presented structure in which pearlite partially coexisted with ferrite as shown in FIG.
  • the iron-based sintered sliding member was subjected to oil impregnation processing, to obtain iron-based oil impregnated sintered sliding member having the oil content of 12 volume %.
  • Powder mixture (10.86 mass % copper component, 0.65 mass % manganese component, 85.49 mass % iron component, and 3 mass % carbon component) similar to that of the Example 1 was obtained, filled in a mold, and compacted at a compacting pressure of 5 ton/cm 2 , to obtain a green compact of a rectangular shape.
  • This rectangular-shaped green compact was placed in a heating furnace whose inside was adjusted to be a hydrogen gas atmosphere, subjected to liquid-phase sintering at a temperature of 1100 degrees Celsius for 60 minutes, and then taken out of the heating furnace, to obtain a rectangular-shaped iron-based sintered material.
  • This iron-based sintered material was machined to obtain an iron-based sintered sliding member measuring 30 mm in each side length and 5 mm in thickness.
  • the density of this iron-based sintered sliding member was shown to be 6.7 g/cm 3 , and, as for its structure, it was ascertained that it presented structure in which pearlite partially coexisted with ferrite as shown in FIGS. 2 and 3 , with no free cementite being generated in the structure and copper-iron-manganese alloy being dispersedly contained in net-like forms at grain boundaries of the structure.
  • the hardness of the site of the structure in which pearlite partially coexisted with ferrite was 400 in terms of the micro Vickers hardness (HMV), and the hardness of the site of the copper-iron-manganese alloy dispersedly contained in net-like forms at the grain boundaries of the structure was 110 in terms of the micro Vickers hardness.
  • this iron-based sintered sliding member was subjected to oil impregnation processing, to obtain an iron-based oil impregnated sintered sliding member having the oil content of 10 volume %.
  • This cylindrical-shaped green compact was placed in a heating furnace whose inside was adjusted to be a hydrogen gas atmosphere, subjected to liquid-phase sintering at a temperature of 1100 degrees Celsius for 60 minutes, and then taken out of the heating furnace, to obtain a cylindrical-shaped iron-based sintered material.
  • This iron-based sintered material was machined to obtain an iron-based sintered sliding member having an inside diameter measuring 20 mm, an outside diameter measuring 28 mm, and a length measuring 15 mm.
  • the density of this iron-based sintered sliding member was shown to be 6.6 g/cm 3 , and, as for its structure, it was ascertained that it presented structure in which pearlite partially coexisted with ferrite as shown in FIG.
  • Powder mixture (10.86 mass % copper component, 0.65 mass % manganese component, 85.49 mass % iron, and 3 mass % carbon component) similar to that in the Example 2 was obtained, filled in a mold, and compacted at a compacting pressure of 5 ton/cm 2 , to obtain a green compact of a cylindrical shape.
  • This cylindrical-shaped green compact was placed in a heating furnace whose inside was adjusted to be a hydrogen gas atmosphere, sintered at a temperature of 1100 degrees Celsius for 60 minutes, and then taken out of the heating furnace, to obtain a cylindrical-shaped iron-based sintered material.
  • This iron-based sintered material was machined to obtain an iron-based sintered sliding member having an inside diameter measuring 20 mm, an outside diameter measuring 28 mm, and a length measuring 15 mm.
  • the density of this iron-based sintered sliding member was shown to be 6.7 g/cm 3 , and, as for its structure, it was ascertained that it presented structure in which pearlite partially coexisted with ferrite as shown in FIG. 5 , with no free cementite being generated in the structure and copper-iron-manganese alloy being dispersedly contained in net-like forms at grain boundaries of the structure.
  • the hardness of the site of the structure in which pearlite partially coexisted with ferrite was 450 in terms of the micro Vickers hardness (HMV), and the hardness of the site of the copper-iron-manganese alloy dispersedly contained in the structure was 120 in terms of the micro Vickers hardness.
  • this iron-based sintered sliding member was subjected to oil impregnation processing, to obtain an iron-based oil impregnated sintered sliding member having the oil content of 10 volume %.
  • An iron-based sintered material similar to the iron-based sintered material of the SMF class 4 prescribed in Japanese Industrial Standards JIS Z2550 was prepared. That is to say, to atomized iron powder having an average particle size of 70 ⁇ m (the same iron powder as in the Example 1), were blended: 3 mass % electrolyte copper powder having an average particle size of 100 ⁇ m and, as a carbon component, 0.7 mass % natural graphite powder (the same graphite powder as in the Example 1). These powders were mixed by a V-type mixer for 20 minutes, to obtain powder mixture (3 mass % copper component, 0.7 mass % carbon component, and the residual iron component). Then, this powder mixture was filled in a mold and compacted at a compacting pressure of 4 ton/cm 2 , to obtain a green compact of a cylindrical shape.
  • This rectangular-shaped green compact was place in a heating furnace whose inside was adjusted to be a hydrogen gas atmosphere, sintered at a temperature of 1120 degrees Celsius for 60 minutes, and then taken out of the heating furnace, to obtain a cylindrical-shaped iron-based sintered material.
  • This iron-based sintered material was machined to obtain an iron-based sintered sliding member having an inside diameter measuring 20 mm, an outside diameter measuring 28 mm, and a length measuring 15 mm. The density of this iron-based sintered member was shown to be 6.5 g/cm 3 .
  • This iron-based sintered sliding member was subjected to oil impregnation processing, to obtain an iron-based oil impregnated sintered sliding member having the oil content of 15 volume %.
  • Opposite member carbon steel for machine structural use (S45C)
  • a plate-like bearing test piece (iron-based oil impregnated sintered sliding member) 10 was put in a fixed state.
  • a cylindrical body 12 to be used as the opposite member was rotated in the direction of the arrow B under a prescribed load applied on the surface 11 of the plate-like bearing test piece 10 from above the plate-like bearing test piece 10 (from the direction of the arrow A), to measure the friction coefficient between the plate-like bearing test piece 10 and the cylindrical body 12 and wear loss of the plate-like bearing test piece 10 after the elapse of the prescribed test time.
  • Opposite member bearing steel (SUJ2 quenched)
  • Test method As shown in FIG. 7 , in a state that a load was applied on a cylindrical-shaped bearing test piece (iron-based oil impregnated sintered sliding member) 10 a to fix the bearing test piece 10 a , a rotating shaft 12 a as the opposite member was oscillatedly rotated at a given sliding speed, to measure the friction coefficient between the cylindrical-shaped bearing test piece 10 a and the rotating shaft 12 a and wear loss of the cylindrical-shaped bearing test piece 10 a after the elapse of the prescribed test time.
  • a rotating shaft 12 a as the opposite member was oscillatedly rotated at a given sliding speed
  • Opposite member bearing steel (SUJ2 quenched)
  • Test method As shown in FIG. 8 , in a state that a load was applied on a cylindrical-shaped bearing test piece (iron-based oil impregnated sintered sliding member) 10 a to fix the bearing test piece 10 a , a rotating shaft 12 a as the opposite member was rotated at a given sliding speed, to measure the friction coefficient between the cylindrical-shaped bearing test piece 10 a and the rotating shaft 12 a and wear loss of the cylindrical-shaped bearing test piece 10 a after the elapse of the prescribed test time.
  • a cylindrical-shaped bearing test piece iron-based oil impregnated sintered sliding member
  • the present invention provides an iron-based sintered sliding member made from iron powder, copper-iron-manganese alloy powder and carbon powder, comprising 2.67-18.60 mass % copper component, 0.12-1.20 mass % manganese component, 1.0-5.0 mass % carbon component, and iron component as the remaining part.
  • the matrix presents pearlite structure or structure in which pearlite partially coexists with ferrite, and the copper-iron-manganese alloy is dispersedly contained in the structure of the matrix.
  • the copper-iron-manganese alloy having lower hardness than the hardness of the structure of the matrix is dispersed in the structure, and thus, as for sliding on the opposite member, the iron-based sintered sliding member of the present invention shows good running-in ability and excellent excellent tribological property.
  • the iron-based sintered sliding member of the present invention can be applied to a sliding use including for example a bearing, a sliding plate, a washer, and the like.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Manufacturing & Machinery (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Powder Metallurgy (AREA)
  • Sliding-Contact Bearings (AREA)
US13/381,874 2009-08-19 2010-05-24 Iron-based sintered sliding member and manufacturing method thereof Abandoned US20120107168A1 (en)

Applications Claiming Priority (3)

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JP2009190176A JP5367502B2 (ja) 2009-08-19 2009-08-19 鉄系焼結摺動部材及びその製造方法
JP2009-190176 2009-08-19
PCT/JP2010/058741 WO2011021418A1 (ja) 2009-08-19 2010-05-24 鉄系焼結摺動部材及びその製造方法

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JP (1) JP5367502B2 (ja)
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US10710155B2 (en) 2015-09-18 2020-07-14 Jfe Steel Corporation Mixed powder for powder metallurgy, sintered body, and method of manufacturing sintered body

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JP5786755B2 (ja) * 2012-02-16 2015-09-30 トヨタ自動車株式会社 鉄系焼結材料の製造方法
JP6253134B2 (ja) * 2012-09-03 2017-12-27 ポーライト株式会社 焼結軸受
KR102137424B1 (ko) * 2014-03-04 2020-07-24 포라이트 가부시키가이샤 소결 베어링
KR102449381B1 (ko) * 2014-03-04 2022-10-05 포라이트 가부시키가이샤 소결 베어링
CN105090246B (zh) * 2015-08-04 2017-05-10 华中科技大学 一种用于制造含油轴承的浸渗模具及含油轴承的制造方法
JP6267294B2 (ja) * 2016-08-12 2018-01-24 ポーライト株式会社 焼結軸受の製造方法
WO2019059248A1 (ja) 2017-09-20 2019-03-28 株式会社ダイヤメット 焼結含油軸受
JP7111484B2 (ja) * 2018-03-27 2022-08-02 大同メタル工業株式会社 摺動部材

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JP2011042817A (ja) 2011-03-03
CN102471853A (zh) 2012-05-23
CN102471853B (zh) 2013-07-17
JP5367502B2 (ja) 2013-12-11

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