Classifications

• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C21/00—Alloys based on aluminium
  • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C21/00—Alloys based on aluminium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C21/00—Alloys based on aluminium
  • C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
• • 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
• • 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
  • F16C33/14—Special methods of manufacture; Running-in
• • 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
  • F16C2204/00—Metallic materials; Alloys
  • F16C2204/20—Alloys based on aluminium
• • 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
  • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
  • F16C2240/06—Temperature
• • 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
  • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
  • F16C2240/40—Linear dimensions, e.g. length, radius, thickness, gap
  • F16C2240/48—Particle sizes
• • 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
  • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
  • F16C2240/90—Surface areas
• • 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
  • F16C2360/00—Engines or pumps
  • F16C2360/22—Internal combustion engines
• • 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
  • F16C3/00—Shafts; Axles; Cranks; Eccentrics
  • F16C3/04—Crankshafts, eccentric-shafts; Cranks, eccentrics
  • F16C3/06—Crankshafts

Definitions

• the present invention relates to aluminum-based alloy bearings], and is used in more detail as a bearing of an internal combustion engine, and is described in more detail.)) Tin and / or lead The present invention relates to an improvement in an aluminum alloy bearing containing the same.
• Aluminum alloys are used in automobiles and marine engines as bearings for internal combustion engines, for example, as control bearings and crankshaft bearings. These bearings have a corrosion resistance of 5 against corrosion in the engine environment, making them extremely suitable for the above applications.
• US Patent No. 4,153,756 discloses a t-.Sn-based bearing alloy having a low degree of softening under high-temperature conditions and therefore a high fatigue strength. 1 0-3 04 Basic weight of aluminum and balance of aluminum
• This alloy is made by adding manganese or zirconia to the alloy. It is also advisable to add copper or both copper and perimeter to this alloy.
• the above-mentioned aluminum-based alloys containing tin, Z or lead are generally used as bearings by being pressed against a backing steel sheet, but the bonding strength between the bearing alloy and the backing steel sheet is increased. In order to achieve this, it is essential to perform a step of annealing after pressure welding.] In general, this annealing is performed for a longer time at a temperature lower than the temperature at which the intermetallic compound of AA-Fe is formed. In the case of aluminum alloys containing tin and Z or lead, if exposed to high temperatures by the above-mentioned annealing, crystallization of aluminum crystal grains and tin etc. in the alloy structure There is a drawback that the material becomes coarse and the high-temperature hardness and fatigue resistance of the tin-containing aluminum-alloy are reduced. ⁇ Includes additional elements to eliminate the above-mentioned disadvantages of rubber bearing alloys
• the present invention is based on a completely different theory from the prior art as described above]), the bleeding property and the seizure load are dramatically increased and the overload is improved. It provided an aluminum alloy bearing that could be used as a bearing.
• the mating material (steel crankshaft, etc.) is directly polished to directly affect bleeding or compatibility.
• the particle size was controlled by applying the theory of uniformly dispersing fine hard particles in a soft matrix.] 3
• the theory itself is inherent in, for example, the applicant's earlier patent application], and is a well-known theory in the field of sliding materials.
• this technical means is the dimensional control of hard element particles such as silicon in an aluminum alloy. Silicon particles precipitate and crystallize in the alloy ( ⁇
• the silicon particles are divided, but not only the silicon particles are divided as shown in the figure, but in some cases, the silicon particles are coarsened to a predetermined size. It was found that when the number of silicon particles was controlled to a predetermined number, the bearing performance was significantly improved. By the way, the above public
• the aluminum alloy has a weight percentage of 0.5
• niob at least from the rheruru group Particles containing one type of hard element, and having a particle size of 5 to 40 ⁇ m, as measured from the length of the particle containing or containing the hard element. bonded to the back metal to ⁇ beam alloy - but a Le Mi being present .3 5 6 X 10- 2 dragon 2 equivalents 1 5 or more in any portion of the alloy.?
• the alloys of the present invention may optionally be composed of (1% to 35% by weight, (b) 0.1% to 10%! &, Cadmium, and , Talium and bismuth]? At least one selected species, and (c)
• a group consisting of 0.1 and 2 copper and magnesium] 3 at least one selected from any combination can be contained. Examples and main features are listed below.
• Hard element 0.5% to less than 5% of silicon
• Optional component Copper, magnesium
• Hard element 0.5 to less than 5% of silicon
• Soft element Suzu
• Hard element 0.5 to less than 5
• Silicon is an element that has a special bleeding action described below.
• the preferred silicon content for abrasion of the shaft is 2 to less than 5.
• manganese, iron, morip, den, nickel, nickel, konore, konore, antimon, chrom And -ops are elements that have a special conforming effect.
• the preferred content of manganese and the like is 1 to 9%.
• the lower limit of each element is preferably 0.1%.
• Manganese, etc. crystallize in the form of a single metal, or in the form of an intermetallic compound of manganese, etc. and aluminum, or analyze the components of the crystallized material It is not possible. However, by adding manganese or the like to the tin-containing aluminum alloy, hard particles other than soft particles such as tin crystallize out. Therefore, from or including manganese, etc.
• the special bleeding action as described above is particularly effective when the axis of the mating material is 'spheroidal graphite iron or flaky graphite iron'.
• Spheroidal graphite iron tends to be used in place of conventional forged shafts in order to reduce the cost of shafts such as crankshafts in internal combustion engines.
• Graphite particles are cut from the shaft surface!
• the traces of the spherical black & particles that have fallen off are many concaves or fossae, and the iron-based matrix around the periphery is work hardened. ]?
• the problem with conventional aluminum is that it causes abnormal wear on the bearing surface
• OMPI There were alloys for system bearings. According to the research of the present inventor, the soft aluminum matrix was found to be in the form of a cut-out]), cut into a recess, and put in the recess. Due to the lack of aluminum adaptability between the minium and bearing material.]? It was also found that seizure occurs immediately because it is very easy to adhere. However, in the aluminum alloy according to the present invention, the coarse particles cut the j?] And ??, and the periphery of the recess]? As a result, seizure does not occur up to a high load]), and seizure resistance is significantly improved.
• the silicon particles in the obtained A-Si alloy sheet are almost 5 micron or less].
• the number of units is less than 10 micron, rarely, the number of unit area is small, and it is needle-like or flat.
• Intermediate annealing is performed after rolling, but the temperature is selected to be about the recrystallization temperature, so that the silicon particles hardly become coarser by the intermediate annealing.
• the bearing alloy is pressed against a backing steel sheet, and the temperature is lower than the A-Fe intermetallic compound formation temperature .
• the conventional method of producing tin and / or lead-containing aluminum and aluminum alloy bearings is to perform annealing after pressing at 350 mm. Even at this temperature of 3501C, the silicon particles hardly coarsened, and as a result, most of the fine silicon particles less than 5 ⁇ were present in the final bearing product. On the other hand, 3.56 X 10 "" 2 thighs 2 or more of the coarse hard particles according to the present invention having a size of 5 to 40 m. As a result, it was found that heat treatment of the bearing alloy at a high temperature of 350 to 550C before the above-mentioned welding was most prominent.
• the heat treatment process before the welding is hard to control the size of the hard particles outside, for example, the control of the heating temperature and the rolling reduction in the rolling process, or the control of the cooling rate or the intermediate annealing in the manufacturing process.
• the formation of ⁇ -Fe intermetallic compounds or the bearing abutment just before completion Dissolution of low-melting components such as tin in the aluminum alloy may occur.]
• these have undesirable effects on bearing performance, especially on the familiarity of the general concept.
• the hard particles Judging from the phase diagram of a binary alloy such as A-Mn, the hard particles are considered to be as follows depending on the type of alloying element.
• Ni NiA ⁇ 5-
• Nb NbA 3
• the crystallization morphology during mirror fabrication which is considered to be the intermetallic compound, varies. These crystals are also dimensionally controlled.
• Table 1 shows how the number of crystallized hard particles changes according to the hard element content by the high-temperature heat treatment before welding as described above. Table 1 was calculated assuming that all hard elements were crystallized as cubic hard particles of the dimensions shown in the horizontal column. Actually, hard particles with a particle size of less than 5 micron are subjected to high-temperature heat treatment before pressure welding.] Most of hard particles with a particle size of 5 micron or more are coarsened. Therefore, Table 1 is useful as a material for controlling the hard particles in the aluminum alloy of the present invention. Hard particle count value
• the number of hard particles is 340. Even if some of the hard elements are crystallized as hard particles of less than 5 micron, it is difficult to secure more than 5 hard particles.
• the number of hard element particles of 5 micron ⁇ depends on the hard element content. This is the number of hard elements from 5 micron to 10 micron in the actual bearing alloy! ) Less, but due to high temperature heat treatment before crimping
• the ratio of coarse particles of 5 micron or more to fine particles of 5 micron or less is increased. Then, for example, in order to increase the ratio of the hard element of 5 to 10 micron coarse grains, a high temperature ripening treatment of 350 to 450 before welding can be used.
• OMPI V IP OMPI V IP .
• Table 1 if all the hard elements were precipitated as 40 micron particles, there would be four. If the number is one, it is possible to crystallize both hard element particles of 5 to 30 micron and hard element particles of 40 micron. Therefore, within the range of the hard element content of the aluminum alloy of the present invention, and within the range of the particle size of 50 to 40 micron.] 3 The specific number of coarse hard element particles It can be crystallized.
• the four preferred examples are:
• the hard particles in the rolled aluminum alloy have needle-like shapes, and the longitudinal direction is often coincident with the rolling direction, but the high-temperature heat treatment of the present invention is performed. And the hard particles have a relatively large width in the direction perpendicular to the rolling direction.]? These hard particles take on a substantially horizontal shape when viewed on the horizontal plane of the bearing, that is, the surface in contact with the mating member shaft. The preferred shape is massive when viewed in horizontal and vertical planes. Most of the hard particles of 5 micron or more are agglomerated.]
• the size of the hard particles is measured on the above horizontal plane.
• chromium intermetallic compounds, tin particles, and other particles are present in the alloy.
• a metallurgical microscope was used. It is good to see that chromium, soot, etc. are white and hard particles are gray (dark gray) regardless of the etching method.
• the area of 3.56 X 10 to 2 bulges 2 is chosen for convenience and is based on the field of view of the inventor's microscope device.
• the number of silicon particles per unit area can be corrected using an appropriate conversion factor.
• the above-described limitation of the number / area of particles corresponds to 1.4 ⁇ 10 8 particles Z ⁇ 2 .
• the cross-sectional area of the bearing alloy The number of particles is determined by the horizontal cross section of the metal plate. That is, a cross section parallel to the surface of the plate prepared by the method described below. The size of Si particles measured in the vertical section of the alloy plate was measured in the horizontal plane.]?
• the above numerical limitations may not be satisfied on the surface immediately after machining the alloy plate.
• Tin changes the properties of the aluminum alloy to soft, making it suitable as a bearing.
• OMPI It is an element that gives lubricating performance and adaptability.
• the familiarity is defined by the technical concept generally accepted in the art, and is hereinafter referred to as the familiarity of the general concept.
• the content of soot exceeds 35%, the bleeding and lubrication of the general concept are improved, but the hardness of the aluminum alloy is reduced and the strength as a bearing is reduced.
• the content of tin is less than 1, the bleeding of the general concept as a bearing alloy is degraded. How to add the amount of soot within the range of 1 to 35 should be determined appropriately according to the application, but in general, the load applied to the bearing, that is, the internal combustion Institution hi.
• the tin content is low; for example, 5 to 10%; if small, the tin content is high, while If bearing seizure is a concern due to high load and high speed rotation, the content of tin should be high, for example, 15 to 25%.
• the tin particles must be contained in the alloy. The applicant considers that it is important that the particles are finely dispersed, and in earlier patent applications, it is likely to occur when the content exceeds 1 to 15% due to fine particles such as chrome. A proposal was made to prevent the coarsening of tin particles. However, in the present invention, a special
• OMPI Since the bleeding effect substantially plays a role in bearing performance, miniaturization of soot particles is not so important, but the use of the bearing for internal combustion engines has been reduced.
• the preferred tin content is between 5 and 25.
• lead, etc. Complex, cadmium, indium, tallium, and bismuth change the properties of aluminum alloy to soft. It is an element that imparts lubrication performance suitable for bearings and familiarity with general concepts. When the content of lead and the like exceeds 10%, the familiarity and lubricity of the general concept are improved, but the hardness of the aluminum alloy decreases, and the content of the lead and the like becomes 0-1. Below this, the aluminum alloy is too hard as a bearing alloy, and therefore the familiarity of the general concept deteriorates. How to determine the content of lead, etc. in the range of 0.1 to 10 should be determined as appropriate according to the application, but it is generally added to bearings.
• the load ie the power of the internal combustion engine.
• the content should be low, for example, 1 to 4%, and when it is small, the content of lead and the like should be high.
• the content of lead and the like should be high, for example, 4 to 8. ⁇ ⁇
• the fatigue strength and high-temperature hardness of an aluminum alloy containing lead and tin or tin, etc. shall be sufficient for the performance required for the bearing.
• it is desirable that particles such as lead are finely dispersed in the alloy.
• lead is an element that is difficult to finely disperse.
• the special bleeding action described later substantially plays a role in bearing performance, it can be used as a bearing for an internal combustion engine even if miniaturization of lead and tin particles is not so important. The above troubles have disappeared.
• the preferred content of lead and the like is 1 to 6.
• Lead improves lubricity in coexistence with copper without lowering fatigue resistance.
• lead or the like when lead or the like is added to an A-Sn binary alloy, these are alloyed into tin particles, so that the movement and melting of the tin particles whose melting point is lowered occur. Therefore, when the bearing was continuously operated under a high load, the A-Sn-Pb alloy was partially melted and separated from the bearing in some cases.
• the contribution of the special conformability to the improvement of the bearing performance is high, so lowering the melting point of a soft alloy such as tin-lead is not a serious drawback. If the lead content is less than 0.1%, the effect is not enough! If it exceeds 10%, the fatigue strength required for the bearing will be insufficient.
• Copper and the like increase the hardness of the aluminum alloy and contribute to the improvement of the fatigue strength of the bearing. If the content of copper or the like is less than 0.1, the effect of improving the hardness is small, and if it exceeds 2.0%, the aluminum alloy is hard.]? , Also reduces seizure resistance and corrosion resistance to lubricating oil You. This effect of improving the hardness of copper and the like becomes more remarkable when coexisting with chromium or manganese.] However, even at a temperature of more than 200 ° C., the hardness is hardly reduced.
• the hardness of the alloy which can contain 0.1 to 2 weight% of Cu and / or Mg increases with the amount of Cu and / or Z or Mg within the above range, but the seizure resistance does not increase. descend '. Therefore, the amounts of Cu and / or Mg are chosen so that the hardness and seizure resistance are the desired balance in the bearing alloy.
• An increase in the hardness of the alloy cannot be obtained if Cu and Z or Mg are less than 0.1% by weight. If the amount of these metals exceeds 2.0 weight, the rolling properties of the bearing alloy will deteriorate and the corrosion resistance will decrease.
• Mg exists as a solid solution in the aluminum matrix, and if its amount exceeds 2.0 weight, it is likely to precipitate during annealing. .
• Addition of chromium and chromium or manganese to 0.1-1% by weight of the bearing alloy of the present invention is effective in preventing the hardness of the aluminum alloy from decreasing at high temperatures. (However, the addition of copper and / or magnesium is also low.)).
• weight is less than 0.1 weight, improvement in high-temperature hardness can be expected. No effect is seen with the addition of more than 1.0 weight. Chromium and / or manganese form fine precipitates in the aluminum matrix. Chrome and / or manganese is copper and Z or magnesium-added WIFO Increase the effect of the addition.
• Chromium and manganese increase the hardness of aluminum-based alloys, prevent or reduce softening at high temperatures, and lead to coarsening of lead and other particles at high temperatures. This has the effect. Some of the chromium and manganese form a solid solution in the aluminum matrix, contributing to its solid solution strengthening, and the recrystallization softening temperature is shifted to a higher temperature side. And further increase the work hardenability.
• the increase in the recrystallization softening temperature indicates that the high-temperature strength of the bearing alloy can be maintained well even in the high-temperature region where the internal combustion engine's bearings are exposed (oil temperature: 130 to 150 C). In this regard, desirable results can be obtained in terms of fatigue strength and load capacity.
• A-Cr (Mn) intermetallic compounds The portions of Cr and Mn which are likely to form a solid solution in the aluminum matrix of chromium and manganese are extremely fine as A-Cr (Mn) intermetallic compounds. Precipitates and prevents the soot particles from becoming coarse due to annealing during the bonding of the bearing alloy to the backing metal or the high temperature in the internal combustion engine.] 5
• the hardness of the A-Cr (Mn) intermetallic compound is about 370 in Vickers hardness! ),
• the hardness of silicon particles is about 100,000, which is relatively small. Because of this difference in hardness, the A-Cr (Mn) intermetallic compound prevents the coarsening of the soot particles and improves the bleeding action of the general concept.
• the Vickers hardness of the matrix of the bearing alloy of the present invention is preferably 30-6 OHv. If the aluminum matrix is too soft, the load capacity of the bearing is inadequate. J particles are pushed into the surface when a J load is applied to the bearing. If the aluminum matrix is too hard, the silicon particles will be removed from the surface when the shaft comes into contact with the receiving surface and will not be re-embedded. Rolling causes excessive wear.
• the thickness of the bearing alloy mentioned above is O.I to IOT, especially 2 to
• bearing of the present invention is for the reasons described above.] It may or may not be overlaid to have excellent seizure resistance.
• bearing alloys have a base or base
• the aluminum bearing alloys of the present invention dissolve the aluminum in a gas furnace and add the desired amount of Si and in a conventional manner depending on the desired properties of the alloy. Pb, Sn, Cu, Mg, Mn and Pb were added to the molten aluminum.
• Control of the size and number of spherical hard particles in the bearing alloy has been disclosed in the prior art. It can be obtained by controlled annealing of mirror's alloy according to conditions.
• annealing is performed for 1.5-6 hours at a temperature of 280-550 X: between rolling and annealing of the mirror alloy.
• a temperature of 280-550 X between rolling and annealing of the mirror alloy.
• slitting 350 ° C.]? Annealed at a high temperature of less than 5501C for 1.5-6 hours, followed by 1 hour 200 ° C.] ?Low Controlled cooling at speed.
• Annealing is performed for 1-2 hours at a temperature of 300-400 C following pressure welding to the back metal plate.
• the aluminum-based bearing component according to the present invention is obtained by always pressing the aluminum-based bearing alloy against the backing steel plate or by pressing the alloy at 300-400.
• the aluminum bearing parts according to the present invention obtained by annealing the parts obtained for 1-2 hours, were necessary with conventional aluminum-steel metal parts. It is used as a bearing for internal combustion engines under high load conditions without the need for forceps over, one layer or overlay plate.
• Steps ( 4 ) and (5) return D if necessary
• Fig. 1-Fig. 3 show the test results of A-Si based alloy
• FIG. 1 shows an aluminum-based bearing alloy of the present invention
• FIG. 2 is a graph showing the fatigue load (fatigue resistance) of the aluminum bearing alloy of the present invention as a function of the silicon content of the alloy.
• FIG. 3 shows the wear resistance of the aluminum-based bearing alloy of the present invention with respect to the Si content.
• A-Si-Cu (1) having less than 5 micron silicon particles is shown.
• 'O is the graph shown with the alloy
• Fig. 4-Fig. 17 show the A-Si-Sn-Pb alloy
• Fig. 4 is a graph showing the relationship between the seizure load and the maximum number of silicon element particles.
• Fig. 5 is a graph showing the relationship between the seizure load and the shaft surface roughness.
• Fig. -6 is a graph showing the relationship between seizure load and silicon content.
• Fig. 7 is a graph showing the relationship between the seizure load and the lubricating oil temperature.
• Fig. 8 is a graph showing the change in the seizure load depending on the soft metal content.
• Fig. 9 is a graph showing the relationship between fatigue strength and maximum size silicon particles.
• Fig. 10 is a graph showing the change over time in the amount of wear.
• Fig. 11 is a graph showing the relationship between the change in shaft roughness and the maximum number of silicon particles.
• Fig. 12 is a graph showing the relationship between seizure load and silicon content.
• Fig. 13 is a graph showing the relationship between wear and silicon content.
• Fig. 14 to Fig. 17 are micrographs of the test material aluminum alloy.
• Fig. 18-Fig. 23 show the test results for the A-Pb-Si alloy.
• Fig. 18 is a graph showing the relationship between the seizure load and the maximum number of silicon particles.
• Fig. 19 is a graph showing the relationship between seizure load and silicon content.
• Fig. 20 is a graph showing the change over time in the amount of wear.
• Fig. 21 shows the relationship between seizure load and silicon content.
• Fig. 22 shows the relationship between the amount of wear and the content of silicon.
• Figure 23 is a microscopic structural sketch of the aluminum-alloy test material.
• Fig. 24-Fig. 33 show the test results for the A-Si-Pb-Sn alloy.
• Fig. 24 is a graph showing the relationship between the seizure load and the maximum number of silicon element particles.
• Fig. 25 is a graph showing the relationship between seizure load and silicon content.
• Figure 26 is a graph showing the relationship between fatigue strength and silicon content.
• Fig. 27 is a graph showing the relationship between the amount of wear and the maximum size of silicon particles.
• Fig. 28 shows the graph showing the variation of the seizure load
• Fig. 29 shows the graph showing the time change of the wear amount
• Fig. 30 shows the relationship between the seizure load and the silicon content Graph
• Fig. 31 shows the relationship between the amount of wear and the content of silicon.
• Fig. 32 and Fig. 33 are microstructure sketches of the test material aluminum alloy.
• Fig. 34-Fig. 38 show the test results of the A-Si-Pb alloy.
• Fig. 3-4 shows the seizure load and the maximum number of silicon particles.
• Fig. 35 is a graph showing the relationship between seizure load and silicon content.
• Fig. 36 is a graph showing the relationship between fatigue strength and silicon content.
• Fig. 37 is a graph showing the relationship between the amount of wear and the maximum size of silicon particles.
• Fig. 38 is a graph showing the change over time in the amount of wear.
• Fig. 39 None Fig. 47 shows the test results of A-Sn-Pb-Mn alloys.
• Fig. 39 is a graph showing the relationship between the seizure load and the maximum number of silicon particles.
• Fig. 40 is a graph showing the relationship between seizure load and shaft surface roughness.
• Fig. 41 is a graph showing the relationship between the seizure load and the content of manganese, etc.
• Fig. 42 is a graph showing the relationship between fatigue strength and the content of manganese, etc.
• Fig. 43 is a graph showing the change over time in the amount of wear
• Fig. 44 is a graph showing the relationship between the seizure load and the content of manganese, etc.
• Fig. 45 shows the relationship between the amount of wear and the content of manganese, etc.
• FIG. 3 is a microscopic tissue sketch diagram of FIG.
• FIG. 48-Fig. 5 shows the test results of A-Pb-Mn alloys.
• Fig. 48 is a graph showing the relationship between the seizure load and the maximum number of silicon element particles.
• Fig. 49 is a graph showing the relationship between the seizure load and the content of manganese, etc.
• Figure 50 is a graph showing the relationship between fatigue strength and the content of manganese, etc.
• Fig. 51 is a graph showing the change over time in the amount of wear
• Fig. 52 is a graph showing the relationship between the amount of wear and the content of manganese.
• Each alloy contains 0.5 wt. Cu and 0.4 wt. Cr, in addition to aluminum, and the content of Si is as shown in Table 3 below.
• the cooling conditions after annealing were not controlled.
• OMPI 33-38 spherical Si particles with a size of 10 micron, 10-13 Si particles with a size between 10 and 20 micron, and 20 micron
• 2 to 4 Si spherical particles with a size of 40 micron or less were used, and the rest of Si was smaller than 5 micron.
• the seizure resistance of these alloys was measured using the conditions shown in Table 4 as the seizure tester A.
• an alloy of A-Si-Cu (1 wt :) was prepared according to the conventional method so that the size of the Si particles was less than 5 micron.
• A-Seizure tester Rotating disk material Spheroidal graphite iron
• Disk surface roughness 1.1 mz Rz Lubricating oil type: S AE 10 W-30 (1)
• B-Fatigue tester Shaft material AISI 1055 (forged)
• Lubricating oil type SAE 10 W-30
• C-Abrasion tester Shaft material Spheroidal graphite ⁇ 'iron
• Lubricating oil type Liquid c. Lafin
• the fatigue resistance of the alloys in Table 3 was measured under the conditions listed as fatigue tester B in Table 4.
• Figure 2 shows the fatigue load data.
• the fatigue resistance of the alloy of the present invention is relatively constant when the Si content changes in the range of 0.5-5.0 weight, but may decrease when the Si content exceeds 5 weight. Understand.
• the aluminum-based bearing alloy of the present invention in which the formation of Si particles is controlled has extremely good wear resistance.
• the annealing conditions in the eighth stage were as follows: Samples AA-1 to AA-3, AB-1 to AB-3, AC-1 to AC-3, and AD- 1 was changed to produce AD-3, and the distribution of spherical Si particles was changed in the alloys of these samples as shown in Table 5 c.
• Aluminum according to the present invention Hardness of the base alloy (3 ⁇ Si, 0.4 ⁇ Cr;) (25 is Cu content of about '0.1 ⁇ , 0.5 ⁇ , 1 ° h, 1.75 Hv was about 40, 48, 55, 60, respectively.
• the annealing conditions used in the preparation of the alloy (Table 1)
• the Cii content is 0.5 wt.%
• the Cr content is 0.5%.
• the amount is 0% by weight and the Si content is the value shown in Table 6.]
• the balance is aluminum alloy as described above.
• a bearing alloy of the present invention having the composition and spherical Si particles shown in Table 6 was prepared.
• the A-Si-Cu (1 wt ⁇ :) alloy was changed in the Si content to make the Si particles less than 5 micron (test forest LA21-A24).
• L-Si (20 wt) alloy (test material A25), whose particle formation was not controlled, was prepared in the same manner, and the results are shown in Table 7.
• Table 7 When the indicated table data Ru good in time, in addition to the S i, Cu, M g, A Le Mi Niu arm bearing alloy of the present invention containing at ⁇ single various combinations of ⁇ and Cr alone also have superior seizure resistance and wear resistance compared to the alloy of the comparative example.
• Table 8 shows the composition and silicon particle distribution of the test aluminum alloy. In the table and the following specified otherwise not limited]?, I solid number of Kei particles refers to 3.56 X 1 (J-2 exposure 2 equivalents]? Number of.
• an aluminum alloy having a predetermined composition was subjected to a discontinuous structure.
• a plate having a thickness of 15 baskets was used. After rolling, it was cold-rolled intermittently to a thickness of 6 cages. Next, intermediate annealing was performed at 350 C, followed by cold rolling.]) An aluminum alloy sheet was obtained. Subsequently, high-temperature heat treatment is performed to obtain silicon particles of a desired size in the range of 350 to 550 TC, and then the aluminum alloy thin plate is preheated to 100, and similarly preheated. We pressed the back metal plate and annealed it at 350 0 to complete the bearing. In order to test the performance of the bearing alloy itself, steps after the welding were omitted.
• the specimens in Table 8 were subjected to seizure load measurement under the following conditions.
• Fig. 4 shows the seizure load measurement results.
• the horizontal axis is the number of silicon particles with the largest dimensions in the test forest.
• the test specimens are divided into five groups from BA to BE according to the maximum particle size in the five ranges in Table 8) and shown in Fig. 4. The following facts are evident C
• the seizure load increases with the maximum size of the silicon particles. However, compared to the increase in the seizure load of the test materials in the group (1) and (2). The seizure load of the group is remarkably increased.
• the present invention is limited to that there are at least five or more silicon particles of at least 5 micron.
• Seizure load and fatigue strength of the test materials shown in Table 9 (1) were measured.
• the conditions for measuring the fatigue strength were as follows.
• Tester Alternating load tester
• Example 3 The same experiment as in Example 3 was performed on a test material having a silicon content of 1%, and similar results were obtained as shown in Table 10 (1) and (2).
• Table 11 (1) and () show the results of an experiment conducted in the same manner as in Example 3 with the test material having a silicon content of 3. The results are almost the same as in Example 3.
• Table 12 (1) and ( 2 ) show the results of an experiment conducted in the same manner as in Example 2 using the test material having a silicon content of 4.7. The result of this experiment is almost the same as in Example 3.
• Example 4 The specimen B12 of Example 4 and the specimen B19 of Example 5 were tested. Shown in the figure. 20% as a comparative example (COMP)
• the seizure load of the Sn-1 ⁇ Cu-A alloy was measured. It is clear that the seizure load of the material of the present invention is good irrespective of the surface roughness of the mating material.
• the comparative material has almost no crystallization of hard particles and imparts seizure resistance to the D-aluminum alloy due to the general concept of the soft solute phase. is there. Therefore, Fig. 5 shows the difference between the general concept and the effect of special breakthrough on seizure resistance.
• the counterpart material is spherical graphite-iron, it is understood that the high seizure resistance of the material of the present invention to the spherical graphite-iron is well understood.
• Fig. 6 shows the seizure load (condition A) when the silicon particle distribution was kept constant and the silicon content was varied, as in the test materials shown in Table 3, and Fig. 6 shows the results.
• the results of measuring the fatigue strength (Condition B) were as follows: Table 13
• the seizure load is maximized when the silicon content is about 453 ⁇ 4.
• the seizure load is governed by the number and size of the largest silicon particles in the silicon content range of the present invention. In this controlled embodiment, there is some effect due to the silicon content. This is thought to be due to fine silicon particles of less than 5 microns.
• the seizure load of the test materials B C1 to B C5 was measured under the following conditions.
• the measurement result is the test material BC 1 (5 0 , BC 3 (9 0 WO 2 ), BC 4 (11 O ⁇ an 2), BC 5 (170k ⁇ 1 ⁇ 2 2) was Tsu Der. This indicates that the seizure resistance against thrust load is improved with the maximum size (10 to 20 micron) of silicon particles.
• the seizure load was measured under the condition A (with an oil temperature of 140 TC) using the BC 2 test material and the 20 ° Sn-1 ⁇ Cu-alloy as comparative test materials.
• Fig. 8 shows the results of measuring the seizure load under condition A while changing the tin and lead contents of the B C 2 test material.
• Sn + Pb maintains Sn: Pb at the same ratio as BC2.
• the wear of the Cu-A alloy was measured under condition C]). wear The measurement results are shown in FIG.
• the wear of the comparative material progressed with time, but the wear amount of the material of the present invention almost increased after about one hour.
• the horizontal axis is zero, that is, the elementary particle force of 5 micron or more; 3.5 6 X 10-2! "
• the shaft is roughened by a sliding bearing.
• the smoothing of the axis is promoted as the maximum number of silicon particles increases and the particle size increases. This supports the fact that coarse silicon particles have the function of uniformly flattening the fine irregularities on the shaft surface.
• the sample material contains large silicon particles with a maximum size of about 20 micron, such as BC, the axis is smoothed and the effect is rather conspicuous. ⁇ indicates that the appropriate elementary particles are appropriate ⁇
• the seizure load of B42 is shown by the - ⁇ - line in Fig. 12.
• the wear amount of the present invention and the comparative material was measured under the following conditions.
• Fig. 13 shows the results of wear measurement. From this drawing,
• Figure 17 Figure 14 shows the structure of the comparative example.
• Most of the Ca particles are less than 5 micron. Although there are several silicon particles of 5 micron or more, they have needle-like or flat shapes extending in the rolling direction.
• Fig. 15 shows an example in which the size of the silicon particles is controlled to 5 to 10 microns. Comparing Fig. 14 and Fig. 15, there are few fine silicon particles less than 5 micron in Fig. 15! ), Coarse and massive silicon particles of 5 micron or more are observed. From this fact, it is presumed that the high-temperature heat treatment of the present invention causes the fine silicon particles to coalesce and change to coarse particles.
• Fig. 16 is over 10 micron and below 20 micron
• Fig. 17 is 20 micron
• the size of the silicon particles was controlled to a size exceeding 30 microns and less than 30 microns.
• the slender precipitate is a Sn + Pb alloy particle. Comparing Fig. 15 and Fig. 16, it can be seen that the alloy particles of Sn + Pb are coarser [9] due to the high temperature heat treatment]. However, the Sn + Pb alloy particles have changed to irregular shapes and the D-silicate particles have changed to regular shapes such as polygons. Clearly different. here,
• Table 16 shows the composition and silicon particle distribution of the test aluminum alloy.
• Fig. 18 shows the seizure load measurement results.
• the horizontal axis is the number of silicon particles with the maximum dimensions of the test material. The following facts are evident.
• the seizure load depends on the maximum size of the silicon particles.] 9 Dependent on the c, that is, in the BA, BB, BC, BD and BE groups, the latter seizure load is higher. Except for group A, the seizure load increases with the maximum size of the silicon particles. Seizure load is obtained at most 5 0 0 K 9 Z m 2 only reaches said 3 ⁇ 4 to weak Iga and Ru good to the present invention seizure load of 2 times in sample materials outside the range of the A group of the present invention .
• Seizure load and fatigue strength of the test materials shown in Table 17 (1) were measured.
• the measurement conditions for fatigue strength were the same as in B above)).
• the measurement results are shown in Table 17 ( 2 ). From this, it can be seen that according to the present invention, the seizure load is improved and the fatigue strength is not deteriorated i9 by the coarse silicon particles.
• the number of silicon particles less than 5 micron was measured.
• the shaft of the counterpart material is carbon steel for machine structural use (S55C)]), and the bearing alloy according to the present invention is also effective when the carbon of the counterpart material does not exist as graphite. You can see this.
• Table 19 (1) and (2) show the results of an experiment carried out in the same manner as in Example 13 with a test material having a silicon content of 3%. This result is almost the same as in Example 13.
• Table 20 (1) and ( 2 ) show the results of an experiment conducted in the same manner as in Example 13 using a test material having a silicon content of 4.7%. The experimental results are almost the same as those of Example 13 ⁇
• Fig. 19 shows the seizure load (condition A) when the silicon particle distribution was fixed and the silicon content was varied as in the test materials shown in Table 22. Also, the result of the measurement of the fatigue strength (condition B) $ ⁇ 22 ⁇ 7R f:.
• Table 22 Composition of aluminum-palladium alloy test material and distribution of silicon particles
• the seizure load becomes maximum when the silicon content is about 3%.
• the seizure load is governed by the number and size of the largest silicon particles in the silicon content range according to the present invention. In this example, which was controlled to be constant, a slight effect was observed depending on the silicon content. This is thought to be due to fine silicon particles of less than 5 microns.
• the seizure load was measured at an oil temperature of 80 ° C and an oil temperature of 10 TC under the condition A for the specimen C C 3. The same measurement was performed using a 4 Sn-1% Cn-A alloy as a comparative material. The results are shown in Table 24. Table 24
• test material of CC 3 and 41o Sn-1-5 Cn-A ⁇ alloy were used as comparative test materials, and the seizure load was measured under the condition A (oil temperature 1401C). It is shown in Table 25.
• condition A oil temperature 1401C
• Fig. 20 shows the measured wear.
• the wear of the comparative material progressed with time, but the wear of the material of the present invention increased almost after about one hour. The inventor considers such a difference as follows.
• coarse silicon particles existing on the bearing surface are formed at the initial stage of sliding, by the projection of the surface roughness of the mating shaft and the edge of the graphite or the like around the spherical graphite existing on the surface. (Sharpening) of the shaft to change the shaft surface to a better sliding condition for the bearing, to achieve a state close to fluid lubrication and to achieve direct shaft-bearing contact. Block me! ), This stopped the progress of bearing wear
• FIG. 21 shows the results of measuring the seizure load under condition 'A. 5 in Fig. 21 and Fig. 19? Comparing the same silicon content less than ⁇ , it can be seen that the test material of the present invention can obtain a much higher seizure load. .
• FIG. 22 shows the results of measuring the wear amount of the comparative material and the test material C33 to 38 of the present invention (Example 17) under the condition C. From this drawing, it can be seen that when the high-temperature heat treatment according to the present invention is performed to control the size of the silicon particles, the wear resistance of the lead-containing aluminum alloy is significantly improved.
• CMPI In the structure of the comparative example, most of the elementary particles are less than 5 micron.], And there are several elementary particles of 5 microns or more. It has an elongated needle shape or flat shape.
• Table 26 shows the composition and silicon particle distribution of the test aluminum alloy. Unless otherwise noted in the table and below, the number of silicon particles refers to the number of 3.56 X 10 " 2 » 2 equivalents ?? 2 to 5 micrometer after test material DB1 The number of elementary particles of silicon has not been measured.
• Figure 24 shows the seizure load measurement results.
• the horizontal axis is the number of silicon particles with the maximum dimensions of the test material.
• the test materials are shown in Fig. 24, divided into five groups from DA to DE according to the maximum particle size in the five ranges shown in Table 26. This figure shows that the seizing load depends on the maximum size of the silicon particles.]? )
• the fact that the number of small-sized silicon particles is hardly affected by the fact that the present invention limits the number of silicon particles of at least 5 micron to at least 5 or more. is there.
• the seizure load (condition A), fatigue strength and wear resistance of the test materials shown in Table 27 (1) were measured.
• the measurement conditions of the fatigue strength were as follows.
• Tester Alternating load tester
• Tester Mixed lubrication tester
• Table 29 (1) and () show the results of an experiment conducted in the same manner as in Example 24 with the test material having a silicon content of 11. The results are almost the same as in Example 24. .
• Table 29 (1) shows the results of an experiment conducted in the same manner as in Example 24 with the test material having a silicon content of 11. The results are almost the same as in Example 24. .
• Table 29 (1) shows the results of an experiment conducted in the same manner as in Example 24 with the test material having a silicon content of 11. The results are almost the same as in Example 24. .
• Fig. 25 shows the seizure load (conditions) when the silicon particle distribution was fixed and the silicon content was varied, as in the test materials shown in Table 30.
• Fig. 26 shows the results (condition ⁇ ) for which the fatigue strength was measured. Table 30
• the seizure load is maximized when the silicon content is about 653 ⁇ 4.
• the seizure resistance of the present invention is brought about by the fact that the silicon particles exhibit a special conformability and a shaft supporting action.
• the distribution of silicon particles over 5 micron square was fixed, so that the contribution of special break-in to seizure resistance is considered to be constant regardless of the silicon content.
• the seizure load that is, the seizure resistance
• the aluminum-powder matrix lacks the reliability of the dynamic behavior particularly, and the fatigue phenomenon is remarkable.
• the overall seizure resistance decreases.
• Table 31 (1), ( 2 )-The results of measuring the seizure, seizure load, fatigue strength, and wear of the test specimens with different types and amounts of lead, copper, etc. and chromium added elements are shown.
• Table 33 shows (1) and (2). From these tables], it can be understood that excellent bearing performance can be obtained with respect to the aluminum alloy containing various additive elements.
• the abrasion resistance of the tin-containing aluminum alloy is primarily due to the large size of the C particles (that is, the size of the particles from DA to DE group). It can be seen that it is determined by the number of particles with the largest size.
• Fig. 6 shows the results of the measurement of the seizure load under the condition ⁇ (with the exception of oil 1401 TC) using the DC 2 test material and the 20 Sn-1 Cn-A-alloy as comparative test materials. Show. 3o
• FIG. 29 shows the measurement results.
• the wear of the comparative material progressed with time, but the wear of the material of the present invention almost increased after about 2 hours.
• the inventor considers such a difference as follows.
• the quality of the soot phase is mainly cut off by the mating material shaft.
• the constant 'comparative material is worn.
• the comparison material (with less than 5 micron of calcium particles) is notable for its wear resistance.
• Figure 31 shows the amount of wear measured under the conditions G of the comparative material and the test materials D29 to D36 (Table 31) of the present invention. 'From this drawing] 9, when the high-temperature treatment according to the present invention was performed to control the silicon particle size (D29-36)
• Table 36 shows the composition and silicon particle distribution of the test aluminum-alloy. The number of silicon particles of 2 to 5 micron after the test material EB 1 has not been measured.
• the specimens in Table 36 were subjected to seizure load measurement under the following conditions.
• low viscosity lubricating oil was used, and severe conditions P described above were used.
• Fig. 34 shows the seizure load measurement results.
• the horizontal axis is the number of silicon particles having the maximum size of the test material. Specimens are divided into four groups from J E A to E D according to the maximum particle size in the five ranges shown in Table 36, and are shown in Fig. 34. This figure shows that the seizure load that can be determined depends on the maximum size of the silicon particles, and is almost completely affected by the number of the small size silicon particles.])
• Example 3 limited to 5 or more elementary particles of lon
• Example 3 An experiment similar to that of Example 32 was performed on a test material having a silicon content of 7, and as shown in Table 38 (1) and (2), similar results were obtained. Obtained.
• Table 3 (1) and (2) show the results of an experiment performed in the same manner as in Example 32, except that the test sample had a silicon content of 9. This result is almost the same as that of Example 32.
• Example 35 Table 40 (1) and (2) show the results of an experiment carried out in the same manner as in Example 32 using the test material having a 5-silicon content of 11. This result is almost the same as in Example 32.
• Fig. 35 shows the seizure load (condition ⁇ ') when the silicon content was changed and the silicon particle distribution was fixed, as in the test materials shown in Table 41.
• Fig. 36 shows the results (conditions) for which the fatigue strength was measured.
• FIG. 35 shows that before heat-welding, an aluminum alloy containing 45 ⁇ Pb, 0.5% Cu, 0.4 Cr and 10% or less of Si was subjected to heat treatment at 350. The result is shown as a comparative example (COMP-E).
• Table 41 shows the seizure load (condition ⁇ ') when the silicon content was changed and the silicon particle distribution was fixed, as in the test materials shown in Table 41.
• Fig. 36 shows the results (conditions) for which the fatigue strength was measured.
• FIG. 35 shows that before heat-welding, an aluminum alloy containing 45 ⁇ Pb, 0.5% Cu, 0.4 Cr and 10% or less of Si was subjected to heat treatment at 350. The result is shown as a comparative example (COMP-E).
• the seizure load becomes maximum when the silicon content is 8%.
• the seizure resistance of the present invention is attributable to the fact that the silicon particles exhibit a special conformability and a shaft supporting action.
• the size and the distribution of the number of silicon particles of 5 micron or more were kept constant, so that the contribution of the special breakthrough to the sintering resistance depends on the silicon content. It is considered constant.
• the seizure load that is, the seizure resistance is about 6, which is the maximum. This is because the action of fine particles of less than 5 micron, which holds coarse C-elements firmly on aluminum ground, is most noticeable at about 6.
• the content exceeds about 6%, the aluminum material lacks particularly reliable dynamic behavior, and the fatigue phenomenon becomes remarkable. Has a reduced seizure resistance.
• Fig. 37 shows the measurement results of the amount of wear.
• Tables 4 and 4 show (1) and (2). From these tables], it can be seen that excellent bearing performance can be obtained with aluminum alloy containing various additive elements and aluminum alloy containing various additive elements according to the present invention.
• the asterisk in Table 7 means manga.
• the seizure load was measured at the oil temperature of 80 TC and 140 under the conditions of the test material of E C 2. The same measurement was performed using a 4 ⁇ Pb-1 ⁇ Cu-A alloy as a comparative material (COMP). The results are shown in Table 45
• FCD70 shows a large difference
• coarse silicon particles existing on the bearing surface are formed at the initial stage of sliding, by the projection of the surface roughness of the mating shaft and the edge of the graphite or the like around the spherical graphite existing on the surface.
• Table 47 shows the composition and hard particle distribution of the test aluminum alloy. In the table and below
• ba 3 Approx. 4 4 2 0 0 0 0 1 5 3 0.5 0.4
• Figure 39 shows the seizure load measurement results.
• the horizontal axis is the number of hard particles of the maximum size of the test material.
• the test specimens are shown in Fig. 39, divided into five groups, from FA to FE, according to the maximum particle size in the five ranges in Table 47. The following facts are clear from this figure.
• the seizure load depends on the number of hard particles of the maximum size.]? It is almost affected by the number of hard particles of smaller size.
• Example 41-48 The seizure load and fatigue strength of the test materials shown in Table (1) were measured. The measurement conditions of the fatigue strength were the same as those of B described above. The measured results are shown in Table 48. According to the present invention, the seizure load was improved and the fatigue strength was increased due to the coarse hard particles.] 3 The deterioration was found to be c- and ⁇ . Call ⁇ ⁇ In Table 48 (1), the number of hard particles less than 5 micron was measured.
• the shaft of the counterpart material is carbon steel for machine structural use (S55C :)]), and the tin-containing aluminum alloy according to the present invention is an iron-based alloy in which carbon does not exist as graphite. It turns out that it is also effective for the partner material
• Example 41 The same test as in Example 41 was performed on the test material having a manganese content of 1. 1 Experiments were performed. As shown in Table 49 (1) and (), the results were obtained in the same manner. Was done. Table 4.9 (1) Aluminum alloy sample material composition and hard particle distribution
• Table 50 (1) and () show the results of an experiment conducted in the same manner as in Example 42 using the test material having a manganese content of 3. The results are shown in Examples 42 and 43. It is almost the same.
• Table 51 (1) and ( 2 ) show the results of an experiment conducted in the same manner as in Example 41 using a test material with a manganese content of ⁇ ⁇ 11. This experimental result is almost the same as that of Example 41.
• Table 51 Composition of test sample of aluminum alloy and distribution of hard particles
• Fig. 4.0 shows the results of measuring the seizure load under condition A while changing the surface roughness of the spherical graphite-iron shaft of the test material FC2 Nikki mating material of Example 40.
• a comparative example C0MP
• the seizure load of the 20 Sn-1C-A alloy was measured. It is clear from FIG. D that the seizure load of the material of the present invention is good regardless of the surface roughness of the mating material.
• the comparative material does not precipitate hard particles and is due to the swelling of the general concept of a soft tin phase.
• Aluminum alloy It imparts seizure resistance to gold. Therefore, from Fig.
• condition A the seizure load was measured when the hard particle distribution was constant and the content was changed for all elements such as manganese (Condition A) (condition A). It is shown in Fig. 41, and Fig. 42 shows the results of the measurement of the fatigue strength (condition B).
• Fig. 41 3. It can be seen that the seizure load reaches a maximum when the content of manganese and the like is about 4%. As described above, the seizure load is governed by the number and size of the largest hard particles in the content range of the present invention. ?? In the examples, there is a slight effect due to the content of manganese and the like. This is thought to be due to fine hard particles of less than 5 microns.
• the seizure load was measured at an oil temperature of 80 ⁇ and 140 ⁇ under the condition A for the specimen of FC 2. The same measurement was performed using a 20% Sn-l% Cu-A alloy as a comparative material. The results are shown in Table 54.
• test material of FC 2 and the 20% Sn-1 Cu-A alloy were used as comparative test materials.
• Consdition A However, the seizure load measured at an oil temperature of 140 is shown in Table 55.
• DCI spheroidal graphite mirror iron
• the wear amount was measured under the following conditions for the test specimen of FC2.
• the wear amount of the 20 Sn-1 ⁇ Ctt-A alloy containing no manganese was measured under the conditions ( ⁇ .
• the measured wear amount is shown in Fig. 43. Wear progresses over time, but the material of the present invention Almost no wear has increased.
• the inventor considers such a difference as follows. -In the comparative material, the soft tin phase is mainly cut by the mating material shaft.] 3) The comparative material is constantly worn. Departure
• the amount of wear of the present invention and the comparative material was determined under the condition C described above.
• Fig. 45 shows the results of wear measurement. It can be seen that when the high-temperature heat treatment according to the present invention is performed to control the hard particle size, the wear resistance of the tin-containing aluminum alloy is significantly improved. .
• Table 56 shows the composition and hard particle distribution of the test aluminum alloy.
• the number of hard particles refers to the number of 3.56 XI 0 _2 exposure 2 equivalents. 5 6
• Tester Journal type baking test machine
• Fig. 48 shows the seizure load measurement results.
• the horizontal axis is the number of hard particles of the maximum size of the test material.
• the test materials are shown in Fig. 48, divided into five groups from GA to GD according to the maximum particle size in the five ranges shown in Table 56. From this figure, the following facts become clear.
• W Seizure load depends on the number of hard particles of the maximum size.] 5 Left and right. ( «) The seizure load increases with the number of hard particles of the maximum size. However, the seizure load of the test materials of the GA group was almost negligible, and the seizure loads of the other groups including hard particles having a large D size were significantly increased.
• the present invention is limited to the case where there are five or more hard particles having a minimum of 5 micron ⁇ .
• the measurement results are shown in Table 57 (2). From this, it can be seen that according to the present invention, the seizure load is improved and the fatigue strength is deteriorated by coarse hard particles. In Table 57 (1), the number of hard particles less than 5 micron was not measured.
• the shaft of the mating material in the fatigue test is carbon steel for machine structural use (S55C :), and the material of the present invention is effective even when the carbon in the mating iron-based material is present as graphite. I understand.
• Example of a test material containing manganese Example of a test material containing manganese.

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