WO2014119720A1 - 耐摩耗性に優れた内燃機関用バルブシートおよびその製造方法 - Google Patents
耐摩耗性に優れた内燃機関用バルブシートおよびその製造方法 Download PDFInfo
- Publication number
- WO2014119720A1 WO2014119720A1 PCT/JP2014/052241 JP2014052241W WO2014119720A1 WO 2014119720 A1 WO2014119720 A1 WO 2014119720A1 JP 2014052241 W JP2014052241 W JP 2014052241W WO 2014119720 A1 WO2014119720 A1 WO 2014119720A1
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- Prior art keywords
- powder
- valve seat
- surface side
- internal combustion
- layer
- Prior art date
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- 238000002485 combustion reaction Methods 0.000 title claims abstract description 42
- 238000004519 manufacturing process Methods 0.000 title claims description 22
- 239000000843 powder Substances 0.000 claims abstract description 200
- 239000002245 particle Substances 0.000 claims abstract description 182
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 144
- 229910052742 iron Inorganic materials 0.000 claims abstract description 53
- 238000005245 sintering Methods 0.000 claims abstract description 40
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 24
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 23
- 239000012535 impurity Substances 0.000 claims abstract description 22
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 22
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 21
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 19
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 17
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 17
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 16
- 238000002156 mixing Methods 0.000 claims abstract description 9
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- 239000011812 mixed powder Substances 0.000 claims description 43
- 229910000765 intermetallic Inorganic materials 0.000 claims description 34
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- 238000000034 method Methods 0.000 claims description 31
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- 229910052748 manganese Inorganic materials 0.000 claims description 16
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- 238000000465 moulding Methods 0.000 claims description 7
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- 230000006835 compression Effects 0.000 claims 1
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- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 abstract 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 abstract 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 abstract 1
- 239000011651 chromium Substances 0.000 abstract 1
- 229910017052 cobalt Inorganic materials 0.000 abstract 1
- 239000010941 cobalt Substances 0.000 abstract 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 abstract 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract 1
- 239000011733 molybdenum Substances 0.000 abstract 1
- 239000010703 silicon Substances 0.000 abstract 1
- 239000011593 sulfur Substances 0.000 abstract 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 abstract 1
- 239000010937 tungsten Substances 0.000 abstract 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 74
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- 229910000851 Alloy steel Inorganic materials 0.000 description 2
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- -1 C: 0.5 to 1.5% Substances 0.000 description 2
- 229910004261 CaF 2 Inorganic materials 0.000 description 2
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- 238000010586 diagram Methods 0.000 description 2
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- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
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- 238000007088 Archimedes method Methods 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- 229910017061 Fe Co Inorganic materials 0.000 description 1
- 229910017116 Fe—Mo Inorganic materials 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 229910052785 arsenic Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000000748 compression moulding Methods 0.000 description 1
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- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
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- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
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- 238000007561 laser diffraction method Methods 0.000 description 1
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- 230000000717 retained effect Effects 0.000 description 1
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- 239000010959 steel Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 0.000 description 1
Images
Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
- F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
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Definitions
- the present invention relates to a one-layer or two-layer valve seat used for an internal combustion engine, and more particularly to further improvement of wear resistance.
- valve seat on which a valve for opening and closing an intake port and an exhaust port is seated can maintain the airtightness of a combustion chamber, and has wear resistance sufficient to withstand the wear caused by repeated contact of the valve. It is required to be retained. With the recent demand for higher output and improved fuel efficiency of internal combustion engines, valve seats are required to have further improved wear resistance. In particular, in gas engines such as CNG and LPG, and engines such as alcohol fuel, wear of valve seats is increased, and further improvement in wear resistance of valve seats is required.
- Patent Document 1 describes a method of manufacturing a valve seat made of an Fe-based sintered alloy that exhibits excellent wear resistance.
- the technique described in Patent Document 1 is mass% as a raw material forming raw material powder, C: 0.5 to 1.5%, Ni: 0.1 to 3%, Mo: 0.5 to 3%, Co: 3 to 8%, Cr: Fe-based alloy powder containing 0.2 to 3%, the balance being Fe and inevitable impurities, and having an average particle size of 20 to 50 ⁇ m as a raw material powder for forming a hard dispersed phase in mass%, Mo: 20 to Co base alloy powder containing 32%, Cr: 5 to 10%, Si: 0.5 to 3%, the balance consisting of Co and inevitable impurities and an average particle size of 20 to 50 ⁇ m is used.
- the alloy powder is mixed in an amount of 25 to 35% by mass with respect to the total amount of the Fe-based alloy powder, and the mixed powder press-molded body is solid-phase sintered in a vacuum atmosphere to obtain C: Containing 0.5 to 1.5%, Ni: 0.1 to 3%, Mo: 0.5 to 3%, Co: 13 to 22%, Cr: 1 to 5%, Si: 0.1 to 1%, the balance being Fe and inevitable impurities Composed of An Fe-based sintered alloy base having a 10-20% porosity is uniformly formed on the ground, and the Mo-Fe-Co alloy hard dispersion phase is uniformly distributed. This is a technology to make a combined gold valve seat.
- Patent Document 2 describes a method for manufacturing a wear-resistant sintered member.
- the base forming powder is made into a fine powder having a maximum particle size of 46 ⁇ m and 90% by mass or more.
- the formed powder is 40 to 70% by mass of the raw material powder.
- the base-forming powder is an iron-based alloy powder containing Cr: 11 to 13% by mass.
- Patent Document 3 describes a method for manufacturing a sintered valve seat.
- a base-forming powder having a maximum particle size of 74 ⁇ m, a maximum particle size of 150 ⁇ m, Mo: 20 to 60 mass%, Cr: 3 to 12 mass%, Si: 1 to 5 mass% , And sintering the powder after compacting the raw material powder obtained by adding 40 to 70% by mass of the hard phase forming powder composed of Co and inevitable impurities and graphite powder: 0.8 to 2.0% by mass. It is a manufacturing method of a valve seat.
- the base forming powder preferably has a particle size configuration in which a powder having a particle size of 46 ⁇ m or less is 90% or more and a powder having a particle size of 74 ⁇ m or less is the balance. Further, as the base forming powder, it is preferable to use a steel powder containing a relatively large amount of Mo, Cr, Ni, V, Co or the like alone or in combination. In the invention described in Patent Document 3, the pores are filled with copper, copper alloy, lead, or lead alloy. Thereby, it is said that even higher wear resistance can be exhibited even under severe environments.
- Patent Document 4 describes an iron-based sintered alloy material for a valve seat.
- the technique described in Patent Document 4 is an iron-based sintered alloy material in which two types of hard particles are dispersed and contained.
- the first hard particles are hard particles having an average primary particle size of 5 to 20 ⁇ m
- the second hard particles As the hard particles having an average primary particle diameter of 20 to 150 ⁇ m, among the particle diameters corresponding to the peak top positions of the mixed hard particles when these particles are mixed, the difference in the particle diameters of the adjacent peak top positions is
- the first and second hard particles are selectively used so as to be in the range of 15 to 100 ⁇ m, and the first hard particles and the second hard particles are blended so as to occupy 10 to 60 area% in total. Yes. Thereby, it is said that it is possible to simultaneously achieve improved wear resistance when used as a valve seat, reduced counter valve attack, and improved mechanical strength.
- Patent Documents 1 to 3 use powder containing a relatively large amount of alloy elements such as Ni, Mo, Co, and Cr as the base forming powder. In addition, there was a problem that strength, machinability, density and the like were lowered. In addition, in the technique described in Patent Document 4, when a large amount of fine hard particles are contained for further improvement of wear resistance, the hard particles are aggregated, and it is difficult to uniformly disperse, and also aggregate. There was a problem that hard particles became the starting point of wear.
- the present invention solves such problems of the prior art, and provides a valve seat for an internal combustion engine having excellent wear resistance and crushing strength, in which hard particles are uniformly and finely dispersed in a matrix phase, and a method for producing the same.
- the purpose is to provide.
- the present inventors diligently studied various factors that affect the dispersion of hard particles in the matrix phase. As a result, it has been found that the properties of the powder other than the hard particle powder greatly influence the dispersion of the hard particles. Then, when trying to further improve the wear resistance by dispersing fine hard particles, if a large amount of fine hard particle powder is blended, the hard particles are likely to aggregate, and the dispersion of hard particles becomes rather rough. Found that there is a case. This was found to be prominent when iron-based powders for base formation such as pure iron powder and alloy steel powder were composed of coarse powders having a larger particle size than hard particle powders.
- the present inventors have determined that the hard particle powder blended in the mixed powder has an average particle diameter passing through a # 350 sieve. Is a fine powder (-# 350) having a particle size of 15-50 ⁇ m, and the average particle diameter of the base forming powder (iron-based powder) passing through the # 325 sieve is approximately the same as that of the hard particles described above. However, it was important to use a fine powder (-# 325) of 15 to 50 ⁇ m.
- Iron powder, hard particle powder, graphite powder, alloy element powder, and solid lubricant powder are used as raw material powders, mixed with various types of raw material powders, and mixed with a V-type mixer. A and C. These mixed powders are charged into a mold and compression-molded with a mechanical press to form a single-layer valve seat-shaped green compact with a green density of 7.0 g / cm 3. After the treatment and further pressure forming, a 2P2S process was performed in which a sintering treatment was performed at a sintering temperature of 1150 ° C. in a reducing atmosphere to obtain an iron-based sintered body.
- the mixed powder contains 100 parts by mass of the total amount of iron-based powder, alloy element powder, graphite powder, hard particle powder and solid lubricant powder as the lubricant particle powder, and 1.0 part by mass of zinc stearate. did.
- an iron-based powder, an alloy element powder, a graphite powder, a hard particle powder, and a solid lubricant powder are used, and the iron powder has an average particle size of 60 to 80 ⁇ m in mass% with respect to the total amount thereof.
- a total of 60% atomized pure iron powder and high-speed steel powder with an average particle size of 60-80 ⁇ m, Co-based intermetallic compound powder with an average particle size of 5-20 ⁇ m and Co with an average particle size of 20-150 ⁇ m as hard particle powder A total of 35% of the intermetallic compound powder, 1.0% of the graphite powder, 2.0% of the Ni powder as the alloy element powder, and 2.0% of the MnS powder as the solid lubricant powder were mixed to obtain a mixed powder.
- iron-based powder, alloy element powder, graphite powder, hard particle powder, and solid lubricant powder are used, and the # 325 sieve is used as the iron-based powder in mass% with respect to the total amount thereof.
- a total of 60% atomized pure iron powder (-# 325) with an average particle diameter of 15-50 ⁇ m and high-speed steel powder (-# 325) with an average particle diameter of 15-50 ⁇ m is used as a hard particle powder.
- a valve seat (size shape: ⁇ 30 ⁇ ⁇ 21 ⁇ 8 mm) was processed by cutting and grinding, and a single rig wear test was performed using a single rig wear tester.
- a valve seat was press-fitted into a jig equivalent to a cylinder head, and then the valve and the valve seat were heated by a heat source attached to the testing machine and the valve was moved up and down by a crank mechanism.
- the amount of wear was measured by the amount of valve sinking.
- the test conditions were as follows.
- Test temperature 300 ° C (sheet surface) Test time: 6h Cam rotation speed: 3000rpm Valve speed: 20rpm Spring load: 2940kgf (300N) (when set) Valve material: T400 overlay material Lift amount: 9mm The amount of LPG + Air and the amount of cooling water were constant.
- the obtained iron-based sintered body was processed into a valve seat (size and shape: ⁇ 28 ⁇ ⁇ 22 ⁇ 6.5 mm) by cutting and grinding, and the crushing strength was measured in accordance with JIS Z 2507. From the obtained results, the wear resistance and the crushing strength are compared based on the iron-based sintered body (reference material) using the mixed powder A as a reference (1.00), and are shown in Table 1.
- the iron-based sintered body using the mixed powder C has both increased wear resistance and crushing strength as compared to the reference material (iron-based sintered body using the mixed powder A).
- a specimen for observing the structure was collected from the obtained iron-based sintered body, the cross section was polished and corroded (corrosion liquid: marble liquid), and the structure was observed with an optical microscope.
- An example of the iron-based sintered body using the mixed powder A and the iron-based sintered body using the mixed powder C are shown in FIG. From FIG. 1, in the iron-based sintered body using the mixed powder A, the hard particles are aggregated to form a coarse hard particle phase. On the other hand, in the iron-based sintered body using the mixed powder C, hard particles are not aggregated, and the hard particle phase is relatively uniformly dispersed in the matrix.
- the hard particle powder to be mixed into the mixed powder was made into a fine hard particle powder (-# 350) with an average particle size of 15-50 ⁇ m
- the iron-based powder was made into a fine iron-based powder with an average particle size of 15-50 ⁇ m
- the mixed powder blended as ( ⁇ # 325) is used to form a sintered body, that is, both the iron-based powder and the hard particle powder are almost the same in average particle diameter, and the average particle diameter is 15 to 50 ⁇ m. It was found that the hard particle phase can be uniformly and finely dispersed in the matrix phase of the sintered body by blending it as a fine powder and further removing the large-diameter powder with a # 350 or # 325 sieve.
- a valve seat for an internal combustion engine made of an iron-based sintered body consisting of one layer or two integrated layers, wherein at least a layer on the valve contact surface side of the valve seat is C: 0.3 to 2.0.
- the hard particles comprise from 10 to 65% by mass% with respect to the layer the total amount of the valve contact surface side, and that it has a base portion structure comprising a rigid particles are dispersed 1000 / mm 2 or more
- a valve seat for an internal combustion engine with excellent wear resistance (2) The valve seat for an internal combustion engine according to (1), wherein the hard particles are Co-based intermetallic compound particles or Fe-based intermetallic compound particles having a Vickers hardness HV 0.1 of 500 to 1200 HV.
- valve seat for an internal combustion engine according to (2) wherein the Co-based intermetallic compound particles are Mo—Fe—Cr—Si Co-based intermetallic compound particles.
- the solid lubricant particles are contained in the base part structure in an amount of 0.5 to 2.0% by mass based on the total amount of the layer on the surface side per valve.
- the seating surface side layer integrated with the valve contact surface side layer contains, in mass%, C: 0.3 to 2.0%, and the balance Fe and Base part composition consisting of inevitable impurities, or C: 0.3-2.0% by mass%, one or more selected from Mo, Si, Ni, Cr, Mn, S, W, V
- a valve seat for an internal combustion engine comprising a total base content of 10% or less, the balance being Fe and inevitable impurities.
- the solid lubricant particles are included in the matrix phase of the layer on the seating surface side in an amount of 0.5 to 2.0% by mass based on the total amount of the layer on the seating surface side. Valve seat.
- an iron-based powder, a hard particle powder, a graphite powder, or an alloy element powder, or a solid lubricant particle powder is blended and mixed to obtain a mixed powder, and the mixed powder is used as a mold.
- An internal combustion engine in which a green compact having a predetermined shape and density is formed by compression molding and sintered, and the green compact is sintered to obtain a valve seat made of an iron-based sintered body composed of one layer or two layers.
- a composition comprising 70% or less in total of one or more selected from Co, Si, Ni, Mo, Cr, Mn, S, W, and V, the balance being Fe and inevitable impurities
- the composition of the base portion after being mixed and the sintered material hits the bulb with the hard particles Comprises 10 to 65% by mass% with respect to the layer the total amount of the surface side and the rigid particles such that 1000 / mm 2 or more distributed allowed comprising tissue, part or all of the hard particle powder, having an average particle size
- a method for producing a valve seat for an internal combustion engine having excellent wear resistance characterized in that the powder is 15 to 50 ⁇ m and the iron-based powder is blended as a powder having an average particle size of 15 to 50 ⁇ m.
- the valve seat has a seating surface side layer integrated with the valve contact surface side layer, and for forming the seating surface side layer, The base composition of the layer on the seating surface side after sintering the mixed powder, the iron-based powder and the graphite powder as the raw material powder, or the alloy element powder, or further the solid lubricant particle powder, %, C: 0.3 to 2.0%, balance Fe and inevitable impurities composition, or mass%, C: 0.3 to 2.0%, Mo, Si, Ni, Cr, Mn, S, W, 1 type or 2 types or more selected from V are contained in a total of 10% or less, and the composition is composed of the balance Fe and inevitable impurities, and the iron-based powder has an average particle size of 60 Manufacturing method
- the solid lubricant particle powder in the base of the layer on the seating surface side after sintering, may be 0.5 to 2.0% by mass based on the total amount of the layer on the seating surface side.
- a method of manufacturing a valve seat for an internal combustion engine comprising mixing.
- the wear resistance is remarkably improved as compared with the conventional, and the strength is high. It has a remarkable industrial effect.
- the raw material powder iron-based powder, graphite powder as alloy element powder, hard particle powder, or alloy element powder other than graphite, or further solid lubricant particle powder, or further lubricant Particle powder is blended and mixed to obtain a mixed powder. Then, the obtained mixed powder is inserted into a mold and compacted to obtain a compact having a predetermined shape and a predetermined density. Next, the green compact is sintered to obtain a valve seat made of an iron-based sintered body consisting of one layer or two upper and lower layers.
- the mixed powder includes, as a raw material powder, an iron-based powder, a graphite powder as an alloy element, a hard particle powder, or an alloy element powder other than graphite, or a solid lubricant particle powder, or a further lubricant.
- Blend with particle powder the valve contact surface side layer of the valve seat is made of an iron-based sintered alloy having a base portion in which hard particles are dispersed in the base phase. By dispersing hard particles in the matrix phase, the wear resistance of the valve seat is significantly improved. Therefore, the hard particle powder to be blended is preferably a powder having a Vickers hardness HV 0.1 of 500 to 1200 HV.
- Co-based intermetallic compound powder examples include Co-based intermetallic compound powder, Fe-based intermetallic compound powder, and Fe-Mo hard particle powder.
- the Co-based intermetallic compound particles are particles in which a high hardness intermetallic compound is dispersed in a relatively soft Co matrix, and are preferable because they have a feature of low partner attack.
- Co-based intermetallic compound powders are Si-Cr-Mo-based Co-based intermetallic compounds, Si-Ni-Cr-Mo-based Co-based intermetallic compounds, and Mo-Fe-Cr-Si-based Co-based intermetallic compounds.
- examples of the Fe-based intermetallic compound powder examples include Co—Ni—Cr—Mo-based Fe-based intermetallic compounds.
- Co-based intermetallic compound particles the hardness of the Fe-based intermetallic compound particles is preferably 500 ⁇ 1200 HV 0.1.
- Mo—Fe—Cr—Si-based Co-based intermetallic compound particles are particularly effective in improving wear resistance as hard particles.
- Mo-Fe-Cr-Si Co-based intermetallic compound particles are in mass%, Mo: 35-47%, Fe: 3-15%, Cr: 3-10%, Si: 2-5%, the balance Co and A composition comprising inevitable impurities is preferable.
- the base structure after sintering in the surface side layer per valve contains 10 to 65% of hard particles in mass% with respect to the total amount of the surface side layer per valve, and 1000 hard particles. / Mm 2 Hard particles are blended so as to have a dispersed structure. If the amount of hard particles dispersed is less than 10%, desired wear resistance cannot be ensured. On the other hand, if the dispersion exceeds 65%, the effect is saturated and an effect commensurate with the amount added cannot be expected. For this reason, the dispersion amount of the hard particles in the surface side layer per valve is limited to the range of 10 to 65% by mass% with respect to the total amount of the surface side layer per valve. More preferably, it is 30 to 40%.
- the number of dispersed hard particles is used as an index of fine and uniform dispersion of the hard particles.
- the number of hard particles dispersed as described above is limited to 1000 / mm 2 or more.
- the number of hard particles to be dispersed is less than 1000 / mm 2 , the hard particles are agglomerated and a significant improvement in wear resistance cannot be expected.
- the number of dispersed hard particles is limited to 1000 / mm 2 or more. It is preferably 1200 to 2000 pieces / mm 2 .
- the number of hard particles to be dispersed is determined by analyzing heavy metals contained in the hard particles using a scanning electron microscope equipped with an analyzer, taking an image of the image (COMP image), and determining the distribution of the hard particles. And the number per unit area is measured and obtained. In order to facilitate the measurement, the number is preferably binarized into a COMP image of heavy metal elements contained in the hard particles and a COMP image of other elements.
- the surface side layer per valve may further contain a solid lubricant in an amount of 0.5 to 2.0% by mass with respect to the total amount of the surface side layer per valve. If the content is less than 0.5%, a desired lubricating effect cannot be expected, and the machinability deteriorates. On the other hand, if the content exceeds 2.0%, the machinability improving effect is saturated and the strength is reduced. For this reason, when it is contained, it is preferably limited to the range of 0.5 to 2.0%.
- solid lubricant MnS, CaF 2 can be exemplified.
- the mixed powder has a base part composition after sintering, for layer formation in the case of one layer or for layer formation on the valve contact surface side in the case of two integrated layers, Base phase and hard particles or solid lubricant particles as described above, C: 0.3-2.0%, further selected from Co, Si, Ni, Mo, Cr, Mn, S, W, V
- the raw material powder should be blended so as to contain 70% or less of one or two or more in total, and have a composition consisting of the remaining Fe and inevitable impurities.
- C 0.3-2.0%
- C is an element that increases the strength and hardness of the sintered body and facilitates the diffusion of metal atoms during sintering.
- C is preferably contained in an amount of 0.3% or more.
- the content exceeds 2.0%, cementite is likely to be generated in the matrix, and a liquid phase is likely to be generated during sintering, resulting in a problem that dimensional accuracy is lowered.
- C is limited to a range of 0.3 to 2.0%.
- the content is 0.9 to 1.1%.
- Co, Si, Ni, Mo, Cr, Mn, S, W, V 70% or less in total Co, Si, Ni, Mo, Cr, Mn, S, W , V is an element that increases the strength and hardness of the sintered body and further improves the wear resistance. In order to obtain such an effect, at least one type including hard particle origin must be added. It is desirable to select and contain 25% or more in total. On the other hand, when the content of these elements exceeds 70% in total, the moldability is lowered and the strength is also lowered. For this reason, one or more selected from Co, Si, Ni, Mo, Cr, Mn, S, W, and V are limited to 70% or less in total. The total amount is preferably 60% or less, and more preferably 40% or less.
- the balance of the valve-side surface layer other than the above components is composed of Fe and inevitable impurities.
- the hard particle powder blended as a raw material powder in the mixed powder is dispersed in the matrix phase in the sintered body and contributes to improvement in wear resistance.
- the hard particle powder to be blended is made finer, it tends to be finely dispersed in the matrix, and it is preferable to use as fine a powder as possible in order to improve wear resistance. Therefore, in the present invention, the hard particle powder is a fine hard particle powder having an average particle size of 15 to 50 ⁇ m (about-# 350) from the viewpoint of manufacturability, particularly fluidity.
- the average particle diameter measurement of powder shall use the value obtained using the laser diffraction method, for example.
- the iron-based powder that is blended into the mixed powder as one of the raw material powders and constitutes the matrix is a powder that is approximately the same as the average particle diameter of the hard particle powder or has a finer average particle diameter. It is preferable. If the iron-based powder forming the base is larger than the average particle size of the hard particle powder, the hard particle powder is likely to aggregate, and it is difficult to uniformly and finely disperse the hard particle powder. Therefore, in the present invention, the iron-based powder to be blended is a powder having an average particle diameter of 15 to 50 ⁇ m, which is a powder having an average particle diameter substantially the same as that of the hard particles. The average particle diameter is preferably 25 to 35 ⁇ m.
- iron-based powder to be blended examples include atomized pure iron powder, alloy steel powder having a total amount of alloy elements of 5% by mass or less, and high-speed steel powder. These powders are preferably blended alone or in combination so as to be compatible with the base composition after sintering.
- solid lubricant powder, iron-based powder, powder mixed in mixed powder for example, alloy element powder such as Ni powder, Co powder, graphite powder, from the viewpoint of finely dispersing hard particles, A powder having an average particle diameter of 15 to 50 ⁇ m is preferable. If the powder is larger than the average particle diameter, hard particles cannot be finely dispersed.
- the valve seat has a seating surface side layer (sitting surface side layer) integrated with the valve contact surface side layer
- the seating surface side layer is bonded to the valve contact surface side layer by sintering. And is made of an iron-based sintered alloy in the same manner as the valve-side surface side layer. It is preferable that the seating surface side layer has a composition that does not contact the valve, supports the valve contact surface side layer, and can simply secure a desired strength as a valve seat.
- a mixed powder obtained by mixing and mixing iron-based powder and graphite powder, or further alloying element powder, or further solid lubricant particle powder as raw material powder.
- the iron-based powder blended as the raw material powder any powder similar to the surface side layer per valve is suitable, but atomized iron powder is preferable, and the average particle size is 60 to 80 ⁇ m. It is preferable to use powder.
- the solid lubricant particle powder may be contained in an amount of 0.5 to 2.0% by mass% with respect to the total amount of the seating surface side layer. If the content is less than 0.5%, a desired lubricating effect cannot be expected, and the machinability deteriorates. On the other hand, if the content exceeds 2.0%, the machinability improving effect is saturated and the strength is reduced. For this reason, when it is contained, it is preferably limited to the range of 0.5 to 2.0%.
- solid lubricant MnS, CaF 2 can be exemplified.
- the mixed powder for layer formation on the seating surface side has a matrix phase composition after sintering (in addition, a matrix composition including the solid lubricant particles when dispersed): C: 0.3 to 2.0% Or further containing 10% or less in total of one or more selected from Mo, Si, Ni, Cr, Mn, S, W, and V, from the remaining Fe and inevitable impurities It is preferable to mix the raw material powder so that the composition becomes.
- the reason for limitation of the matrix phase composition after sintering of the seating surface side layer is as follows.
- C 0.3-2.0%
- C is an element that increases the strength and hardness of the sintered body, and in the present invention, in order to ensure the desired strength and hardness as a valve seat, it is desirable to contain 0.3% or more in the seating surface side layer
- C is preferably limited to a range of 0.3 to 2.0%. More preferably, it is 0.9 to 1.1%.
- the above-mentioned components are basic components of the seating surface side layer.
- one selected from Mo, Si, Ni, Cr, Mn, S, W, and V is further selected as a selective element. You may contain 10% or less of seed
- One or more selected from Mo, Si, Ni, Cr, Mn, S, W, V: 10% or less in total Mo, Si, Ni, Cr, Mn, S, W, V Is an element that increases the strength and hardness of the seating surface side layer, and can be selected as necessary and can contain one or more.
- valve seat composed of two layers of a valve contact surface side layer and a seating surface side layer will be described as an example.
- the lower punch is relatively lowered, and a filling space for the seating surface side layer is formed by the lower punch, the die, and the core rod, and the first feeder is moved into the filling space to Fill with mixed powder.
- the die and the core rod are raised relative to the lower punch to form a filling space for the valve contact surface side layer, and the second feeder is moved to the filling space to mix the valve contact surface side layer. Fill with powder.
- the upper punch is lowered, and the mixed powder for the surface side layer and the mixed powder for the seating surface side layer are pressed together to form a green compact.
- the pressurizing conditions may be appropriately determined according to the need and need not be particularly limited, but in relation to the desired valve seat characteristics, the green compact density in the range of 5.0 to 7.5 g / cm 3 It is preferable to adjust so that it becomes.
- the obtained green compact is then subjected to a sintering treatment to obtain a sintered body having an upper and lower two-layer structure.
- the conditions for the sintering process may be determined as appropriate according to the desired properties, except for performing in a reducing atmosphere, and need not be particularly limited.
- the sintering temperature is preferably 1100 to 1200 ° C. from the viewpoint of sintering diffusion.
- the first sintering process is preferably presintering
- the second sintering process is preferably a sintered body having a desired density.
- a forging-sintering process or an FS process in which a sintering process is performed after forging may be used.
- the raw material powders shown in Table 2 were blended in the blending amounts shown in Table 2 and kneaded with a V-type mixer to obtain various mixed powders for the surface side layer and mixed powder for the seating surface side per valve.
- Table 3 collectively shows the used iron-based powder, the type of hard particle powder, and the average particle diameter.
- the mixed powder No. A1 is a conventional blending example (conventional example). These mixed powders were formed into a two-layered green compact using a press molding machine having a die, a core rod, an upper punch, a lower punch, and two types of feeders that can be driven independently of each other.
- the lower punch is moved down relatively to form a filling space for the seating surface side layer with the lower punch, the die and the core rod, and the first feeder is moved into the filling space to mix the seating surface side layer. Filled with flour.
- the die and the core rod are raised relative to the lower punch to form a filling space for the valve contact surface side layer, and the second feeder is moved to the filling space to mix the valve contact surface side layer. Filled with flour.
- the upper punch was lowered, and the mixed powder for the surface side layer and the mixed powder for the seating surface side layer were integrally pressure-molded to obtain a two-layered green compact. In one part, a single layer of green compact was used. In that case, the first feeder was not used.
- the obtained green compact is pre-sintered and further pressed with a powder molding machine (surface pressure: 6 to 10 ton / cm 2 ), followed by sintering (1100 to 1200 ° C in a reducing atmosphere) 2P2S process is performed to obtain a sintered body.
- a powder molding machine surface pressure: 6 to 10 ton / cm 2
- 2P2S process is performed to obtain a sintered body.
- a 1P1S process in which molding and sintering are performed once is used.
- an FS process in which a forging-sintering process is performed instead of the 2P2S process.
- the thickness of the sintered body was 8 mm, and in the case of two upper and lower layers, it was 1: 1. Samples for analysis were taken from each layer of the obtained sintered body, and the content of each element was determined by emission analysis. The measurement was a cross section inside the boundary surface between the two layers.
- the density was measured about the obtained sintered compact using the Archimedes method.
- the obtained valve seat (sintered body) was inserted into a single rig wear tester shown in FIG. 2 and the following test conditions were tested.
- Test temperature 300 ° C. (seat surface)
- Test time 6hr
- Cam rotation speed 3000rpm
- Valve speed 20rpm
- Spring load 2940kgf (300N) (when set)
- Lift amount 9mm
- Valve material T400 overlay material Note that the amount of LPG + Air and the amount of cooling water were constant.
- the amount of wear ( ⁇ m) was calculated by measuring the dent depth of the test piece (valve seat) after the test.
- the wear amount ratio of the sintered body was calculated based on the wear amount of the sintered body No. 1 as a reference (1.00).
- Abrasion resistance was evaluated by ⁇ when the amount of wear was less than the standard, and x otherwise.
- the obtained iron-based sintered body was processed into a valve seat (size and shape: ( ⁇ 28 ⁇ ⁇ 22 ⁇ 6.5 mm) by cutting and grinding, and the crushing strength was measured in accordance with JIS Z 2507.
- the crushing strength ratio of the sintered body was calculated using the crushing strength of the No. 1 as a reference (1.00), and the crushing strength was evaluated by ⁇ when the crushing strength was higher than the reference, and x otherwise.
- the examples of the present invention are all valve seats (iron-based sintered bodies) that are superior in wear resistance and exhibit high crushing strength compared to the conventional example (sintered body No. 1). On the other hand, in comparative examples that are outside the scope of the present invention, the wear resistance is reduced, the crushing strength is reduced, or both are reduced.
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Abstract
Description
また、特許文献4に記載された技術では、更なる耐摩耗性の向上のために、微細な硬質粒子を多量に含有すると、硬質粒子が凝集して、均一に分散しにくくなり、しかも凝集した硬質粒子が摩耗の起点になるという問題があった。
そして、微細な硬質粒子を分散させて更なる耐摩耗性の向上を図ろうとして、微細な硬質粒子粉末を多量に配合すると、硬質粒子同士が凝集しやすくなり、かえって硬質粒子の分散が粗くなる場合があることを見出した。これは、純鉄粉や合金鋼粉などの基地形成のための鉄系粉末を、硬質粒子粉末に比べて粒径が大きい粗い粉末で構成した場合に顕著になることを知見した。
鉄系粉末と、硬質粒子粉末と、黒鉛粉末と、合金元素粉末と、固体潤滑剤粉末を原料粉として、原料粉の種類を種々変化させて配合し、V型混合機で混練して混合粉A,Cとした。これらの混合粉を金型に装入しメカニカルプレス機で圧縮成形して、圧粉密度:7.0g/cm3の1層のバルブシート形状の圧粉体とし、この圧粉体に仮焼結処理を施し、さらに加圧成形したのち、還元雰囲気中で焼結温度:1150℃で焼結処理を施す、2P2S工程を施し、鉄基焼結体とした。なお、混合粉には、潤滑剤粒子粉末として、鉄系粉末と合金元素粉末と黒鉛粉末と硬質粒子粉末と固体潤滑剤粉末との合計量を100質量部として、ステアリン酸亜鉛を1.0質量部配合した。
試験時間:6h
カム回転数:3000rpm
バルブ回転数:20rpm
スプリング荷重:2940kgf(300N)(セット時)
バルブ材:T400肉盛材
リフト量:9mm
なお、LPG+Air量、冷却水量は一定とした。
得られた結果から、混合粉Aを用いた鉄基焼結体(基準材)を基準(1.00)にして、耐摩耗性および圧環強度を比較し、表1に示す。
ついで、得られた鉄基焼結体から組織観察用試験片を採取し、断面を研磨し腐食(腐食液:マーブル液)して、光学顕微鏡で組織を観察した。その一例を混合粉Aを用いた鉄基焼結体および混合粉Cを用いた鉄基焼結体について、模式図とともに図1に示す。図1から、混合粉Aを使用した鉄基焼結体では、硬質粒子が凝集して粗大な硬質粒子相を形成している。これに対し、混合粉Cを使用した鉄基焼結体では、硬質粒子の凝集は認められず、硬質粒子相は基地中に比較的均一に分散している。
(1)1層または一体化した2層からなる鉄基焼結体製内燃機関用バルブシートであって、前記バルブシートの少なくともバルブ当たり面側の層が、質量%で、C:0.3~2.0%を含み、Co、Si、Ni、Mo、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で70%以下含有し、残部Feおよび不可避的不純物からなる基地部組成と、硬質粒子を前記バルブ当たり面側の層全量に対する質量%で10~65%含み、かつ該硬質粒子を1000個/mm2以上分散させてなる基地部組織とを有することを特徴とする耐摩耗性に優れた内燃機関用バルブシート。
(2)(1)において、前記硬質粒子が、ビッカース硬さHV0.1で500~1200HVであるCo基金属間化合物粒子またはFe基金属間化合物粒子であることを特徴とする内燃機関用バルブシート。
(3)(2)において、前記Co基金属間化合物粒子が、Mo-Fe-Cr-Si系Co基金属間化合物粒子であることを特徴とする内燃機関用バルブシート。
(4)(1)ないし(3)のいずれかにおいて、固体潤滑剤粒子を、前記基地部組織中に、前記バルブ当たり面側の層全量に対する質量%で0.5~2.0%含有することを特徴とする内燃機関用バルブシート。
(5)(1)ないし(4)のいずれかにおいて、前記バルブ当たり面側の層と一体化された着座面側の層が、質量%で、C:0.3~2.0%を含み、残部Feおよび不可避的不純物からなる基地部組成または、質量%でC:0.3~2.0%を含み、Mo、Si、Ni、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で10%以下含有し、残部Feおよび不可避的不純物からなる基地部組成を有することを特徴とする内燃機関用バルブシート。
(6)(5)において、固体潤滑剤粒子を、前記着座面側の層の基地相中に、前記着座面側の層全量に対する質量%で0.5~2.0%含むことを特徴とする内燃機関用バルブシート。
(7)原料粉末として、鉄系粉末と硬質粒子粉末と黒鉛粉末と、あるいはさらに合金元素粉末と、あるいはさらに固体潤滑剤粒子粉末とを配合し混合して混合粉とし、該混合粉を金型に挿入し圧縮成形して所定形状、密度の圧粉体とし、該圧粉体を焼結して、1層または一体化した2層からなる鉄基焼結体製バルブシートとする、内燃機関用バルブシートの製造方法であって、前記バルブシートの少なくともバルブ当たり面側の層形成用として、前記原料粉末を、焼結後の基地部組成が、質量%で、C:0.3~2.0%を含み、Co、Si、Ni、Mo、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で70%以下含有し、残部Feおよび不可避的不純物からなる組成となるように配合し、かつ焼結後の基地部の組織が、前記硬質粒子を前記バルブ当たり面側の層全量に対する質量%で10~65%含み、かつ該硬質粒子を1000個/mm2以上分散させてなる組織となるように、硬質粒子粉末の一部または全部を、平均粒径で15~50μmの粉末とし、かつ前記鉄系粉末を平均粒径が15~50μmの粉末として配合する、ことを特徴とする耐摩耗性に優れた内燃機関用バルブシートの製造方法。
(8)(7)において、前記硬質粒子粉末が、ビッカース硬さHV0.1で500~1200HVであるCo基金属間化合物粉末またはFe基金属間化合物粉末であることを特徴とする内燃機関用バルブシートの製造方法。
(9)(8)において、前記Co基金属間化合物粉末が、Mo-Fe-Cr-Si系Co基金属間化合物粉末であることを特徴とする内燃機関用バルブシートの製造方法。
(10)(7)ないし(9)のいずれかにおいて、前記固体潤滑剤粒子粉末を、焼結後の前記バルブ当たり面側の層の基地相中に、前記バルブ当たり面側の層全量に対する質量%で0.5~2.0%となるように混合することを特徴とする内燃機関用バルブシートの製造方法。
(11)(7)ないし(10)のいずれかにおいて、前記焼結後、さらに成形と焼結とを少なくとも1回以上繰返すことを特徴とする内燃機関用バルブシートの製造方法。
(12)(7)ないし(11)のいずれかにおいて、前記バルブシートが前記バルブ当たり面側の層と一体化された着座面側の層を有し、該着座面側の層形成用として、前記混合粉を、前記原料粉末として鉄系粉末と黒鉛粉末と、あるいはさらに合金元素粉末と、あるいはさらに固体潤滑剤粒子粉末とを、焼結後の着座面側の層の基地部組成が、質量%で、C:0.3~2.0%を含み、残部Feおよび不可避的不純物からなる組成、または質量%で、C:0.3~2.0%を含み、Mo、Si、Ni、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で10%以下含有し、残部Feおよび不可避的不純物からなる組成、となるように配合し、かつ前記鉄系粉末を平均粒径が60~80μmの粉末として配合した混合粉とすることを特徴とする内燃機関用バルブシートの製造方法。
(13)(12)において、前記固体潤滑剤粒子粉末を、焼結後の前記着座面側の層の基地中に、前記着座面側の層全量に対する質量%で0.5~2.0%となるように混合することを特徴とする内燃機関用バルブシートの製造方法。
(14)(7)ないし(13)のいずれかに記載の内燃機関用バルブシートの製造方法により製造されてなることを特徴とする内燃機関用バルブシート。
本発明におけるバルブシートのバルブ当り面側層は、基地相中に硬質粒子が分散した基地部を有する、鉄系焼結合金製とする。基地相中に硬質粒子を分散させることにより、バルブシートの耐摩耗性が顕著に向上する。このため、配合する硬質粒子粉末は、ビッカース硬さHV0.1で500~1200HVの粉末とすることが好ましい。このような粉末としては、Co基金属間化合物粉末またはFe基金属間化合物粉末、あるいはFe-Mo系硬質粒子粉末が例示できる。なかでも、Co基金属間化合物粒子は、比較的軟らかなCo基地中に硬さの高い金属間化合物が分散した粒子であり、相手攻撃性が低いという特徴があり好ましい。また、Co基金属間化合物粉末は、Si-Cr-Mo系Co基金属間化合物、Si-Ni-Cr-Mo系Co基金属間化合物、Mo-Fe-Cr-Si系Co基金属間化合物粉末が、また、Fe基金属間化合物粉末は、Co-Ni-Cr-Mo系Fe基金属間化合物が、それぞれ例示できる。なお、Co基金属間化合物粒子、Fe基金属間化合物粒子の硬さは500~1200HV0.1であることが好ましい。
Co基金属間化合物粒子の中では、Mo-Fe-Cr-Si系Co基金属間化合物粒子が、硬質粒子としてとくに耐摩耗性を向上する作用が顕著である。Mo-Fe-Cr-Si系Co基金属間化合物粒子は質量%で、Mo:35~47%、Fe:3~15%、Cr:3~10%、Si:2~5%、残部Coおよび不可避的不純物からなる組成とすることが好ましい。
硬質粒子の分散量が、10%未満では、所望の耐摩耗性が確保できない。一方、65%を超える分散は、効果が飽和し、添加量に見合う効果が期待できなくなる。このため、バルブ当り面側層における硬質粒子の分散量をバルブ当り面側層全量に対する質量%で、10~65%の範囲に限定した。なお、より好ましくは30~40%である。
C:0.3~2.0%
Cは、焼結体の強度、硬さを増加させ、焼結時に金属原子の拡散を容易にする元素であり、本発明では、0.3%以上含有させることが好ましい。一方、2.0%を超える含有は、基地中にセメンタイトが生成しやすくなるとともに、焼結時に液相が発生しやすく、寸法精度が低下するという問題がある。このため、Cは0.3~2.0%の範囲に限定した。なお、好ましくは0.9~1.1%である。
Co、Si、Ni、Mo、Cr、Mn、S、W、Vはいずれも、焼結体の強度、硬さを増加させ、さらには耐摩耗性を向上させる元素であり、このような効果を得るためには、硬質粒子起因を含め、少なくとも1種を選択し合計で25%以上含有することが望ましい。一方、これらの元素の含有量が合計で70%を超えると、成形性が低下し、強度も低下する。このため、Co、Si、Ni、Mo、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で、70%以下に限定した。なお、好ましくは合計で60%以下、さらに好ましくは40%以下である。
また、混合粉に原料粉末として配合される硬質粒子粉末は、焼結体中で基地相中に分散し耐摩耗性向上に寄与する。配合する硬質粒子粉末を微細な粉末とするほど、基地中に微細に分散する傾向があり、耐摩耗性の向上のためには、できるだけ微細な粉末を使用することが好ましい。このため、本発明では、硬質粒子粉末は、製造性、とくに流動性の観点から、微細な硬質粒子粉末である、平均粒径が15~50μm(-#350程度)の粉末とした。なお、粉末の平均粒径測定は、例えば、レーザー回析法を用いて得られた値を用いるものとする。
硬質粒子粉末、固体潤滑剤粉末、鉄系粉末以外に、混合粉に配合される粉末、例えばNi粉、Co粉、黒鉛粉等の合金元素粉末も、硬質粒子を微細に分散させるという観点から、平均粒径が15~50μmを有する粉末とすることが好ましい。上記した平均粒径を超えて大きな粉末では、硬質粒子を微細に分散させることができなくなる。
なお、着座面側層の焼結後の基地相組成(なお、固体潤滑剤粒子が分散している場合にはそれを含む基地部組成)の限定理由はつぎのとおりである。
Cは、焼結体の強度、硬さを増加させる元素であり、本発明では、バルブシートとして所望の強度、硬さを確保するために、着座面側層では0.3%以上含有することが望ましいが、2.0%を超える含有は、基地中にセメンタイトが生成しやすくなるとともに、焼結時に液相が発生しやすく、寸法精度が低下するという問題がある。このため、Cは0.3~2.0%の範囲に限定することが好ましい。なお、より好ましくは0.9~1.1%である。
Mo、Si、Ni、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上:合計で10%以下
Mo、Si、Ni、Cr、Mn、S、W、Vはいずれも、着座面側層の強度、硬さを増加させる元素であり、必要に応じて選択して1種または2種以上を含有できる。このような効果を得るためには、合計で1%以上含有することが望ましいが、これら元素の含有量が合計で10%を超えて含有しても効果が飽和し含有量に見合う効果が期待できなくなり経済的に不利となる。このため、含有する場合には合計で10%以下に限定することが好ましい。なお、より好ましくは5~6%である。
なお、上記した以外の着座面側層の残部は、Feおよび不可避的不純物からなる。
本発明では、ダイ、コアロッド、上パンチ、下パンチと、互いに独立して駆動可能な2種のフィーダーとを有するプレス成形機を用いることが好ましい。以下、バルブ当り面側層と着座面側層との2層からなるバルブシートを例にして説明する。
そして、得られた圧粉体に、ついで焼結処理を施して上下2層構造の焼結体とする。焼結処理の条件としては、還元雰囲気中で行なうこと以外は、所望の特性に応じて適宜、決定すればよく、とくに限定する必要はない。なお、焼結温度は、1100~1200℃とすることが焼結拡散の観点から好ましい。
以下、実施例に基づいて、さらに本発明について説明する。
これら混合粉を、ダイ、コアロッド、上パンチ、下パンチと、互いに独立して駆動可能な2種のフィーダーと、を有するプレス成形機を用いて、上下2層の圧粉体とした。
得られた焼結体の各層から分析用試料を採取し、発光分析により各元素の含有量を求めた。測定は、2層の境界面より内側の断面とした。
また、得られたバルブシート(焼結体)を、図2に示す単体リグ摩耗試験機に装入し、下記の試験条件
試験温度:300℃(シート面)
試験時間:6hr
カム回転数:3000rpm
バルブ回転数:20rpm
スプリング荷重:2940kgf(300N)(セット時)
リフト量:9mm
バルブ材質:T400肉盛材
なお、LPG+Air量、冷却水量は一定とした。
で運転し、試験後の試験片(バルブシート)の凹み深さを測定し、摩耗量(μm)を算出した。焼結体No.1の摩耗量を基準(1.00)として、当該焼結体の摩耗量比を算出した。基準より摩耗量が少ない場合を○、それ以外を×として耐摩耗性を評価した。
2 セティングプレート
3 熱源(LPG+Air)
4 バルブ
Claims (14)
- 1層または一体化した2層からなる鉄基焼結体製内燃機関用バルブシートであって、前記バルブシートの少なくともバルブ当たり面側の層が、質量%で、C:0.3~2.0%を含み、Co、Si、Ni、Mo、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で70%以下含有し、残部Feおよび不可避的不純物からなる基地部組成と、硬質粒子を前記バルブ当たり面側の層全量に対する質量%で10~65%含み、かつ該硬質粒子を1000個/mm2以上分散させてなる基地部組織とを有することを特徴とする耐摩耗性に優れた内燃機関用バルブシート。
- 前記硬質粒子が、ビッカース硬さHV0.1で500~1200HVであるCo基金属間化合物粒子またはFe基金属間化合物粒子であることを特徴とする請求項1に記載の内燃機関用バルブシート。
- 前記Co基金属間化合物粒子が、Mo-Fe-Cr-Si系Co基金属間化合物粒子であることを特徴とする請求項2に記載の内燃機関用バルブシート。
- 固体潤滑剤粒子を、前記基地部組織中に、前記バルブ当たり面側の層全量に対する質量%で0.5~2.0%含有することを特徴とする請求項1ないし3のいずれかに記載の内燃機関用バルブシート。
- 前記バルブ当たり面側の層と一体化された着座面側の層が、質量%で、C:0.3~2.0%を含み、残部Feおよび不可避的不純物からなる基地部組成または、質量%でC:0.3~2.0%を含み、Mo、Si、Ni、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で10%以下含有し、残部Feおよび不可避的不純物からなる基地部組成を有することを特徴とする請求項1ないし4のいずれかに記載の内燃機関用バルブシート。
- 固体潤滑剤粒子を、前記着座面側の層の基地相中に、前記着座面側の層全量に対する質量%で0.5~2.0%含むことを特徴とする請求項5に記載の内燃機関用バルブシート。
- 原料粉末として、鉄系粉末と硬質粒子粉末と黒鉛粉末と、あるいはさらに合金元素粉末と、あるいはさらに固体潤滑剤粒子粉末とを配合し混合して混合粉とし、該混合粉を金型に挿入し圧縮成形して所定形状、密度の圧粉体とし、該圧粉体を焼結して、1層または一体化した2層からなる鉄基焼結体製バルブシートとする、内燃機関用バルブシートの製造方法であって、前記バルブシートの少なくともバルブ当たり面側の層形成用として、前記原料粉末を、焼結後の基地部組成が、質量%で、C:0.3~2.0%を含み、Co、Si、Ni、Mo、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で70%以下含有し、残部Feおよび不可避的不純物からなる組成となるように配合し、かつ焼結後の基地部の組織が、硬質粒子を前記バルブ当たり面側の層全量に対する質量%で10~65%含み、かつ該硬質粒子を1000個/mm2以上分散させてなる組織となるように、硬質粒子粉末の一部または全部を、平均粒径で15~50μmの粉末とし、かつ前記鉄系粉末を平均粒径が15~50μmの粉末として配合する、ことを特徴とする耐摩耗性に優れた内燃機関用バルブシートの製造方法。
- 前記硬質粒子粉末が、ビッカース硬さHV0.1で500~1200HVであるCo基金属間化合物粉末またはFe基金属間化合物粉末であることを特徴とする請求項7に記載の内燃機関用バルブシートの製造方法。
- 前記Co基金属間化合物粉末が、Mo-Fe-Cr-Si系Co基金属間化合物粉末であることを特徴とする請求項8に記載の内燃機関用バルブシートの製造方法。
- 前記固体潤滑剤粒子粉末を、焼結後の前記バルブ当たり面側の層の基地相中に、前記バルブ当たり面側の層全量に対する質量%で0.5~2.0%となるように混合することを特徴とする請求項7ないし9のいずれかに記載の内燃機関用バルブシートの製造方法。
- 前記焼結後、さらに成形と焼結とを少なくとも1回以上繰返すことを特徴とする請求項7ないし10のいずれかに記載の内燃機関用バルブシートの製造方法。
- 前記バルブシートが前記バルブ当たり面側の層と一体化された着座面側の層を有し、該着座面側の層形成用として、前記混合粉を、前記原料粉末として鉄系粉末と黒鉛粉末と、あるいはさらに合金元素粉末と、あるいはさらに固体潤滑剤粒子粉末とを、焼結後の着座面側の層の基地部組成が、質量%で、C:0.3~2.0%を含み、残部Feおよび不可避的不純物からなる組成、または質量%で、C:0.3~2.0%を含み、Mo、Si、Ni、Cr、Mn、S、W、Vのうちから選ばれた1種または2種以上を合計で10%以下含有し、残部Feおよび不可避的不純物からなる組成、となるように配合し、かつ前記鉄系粉末を平均粒径が60~80μmの粉末として配合した混合粉とすることを特徴とする請求項7ないし11のいずれかに記載の内燃機関用バルブシートの製造方法。
- 前記固体潤滑剤粒子粉末を、焼結後の前記着座面側の層の基地相中に、前記着座面側の層全量に対する質量%で0.5~2.0%となるように混合することを特徴とする請求項12に記載の内燃機関用バルブシートの製造方法。
- 請求項7ないし13のいずれかに記載の内燃機関用バルブシートの製造方法により製造されてなることを特徴とする内燃機関用バルブシート。
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WO2016141154A1 (en) * | 2015-03-03 | 2016-09-09 | Materion Corporation | Light weight high stiffness metal composite |
CN109570509A (zh) * | 2018-12-18 | 2019-04-05 | 宁波申禾轴承有限公司 | 一种高强度轴承的制备方法 |
WO2024154811A1 (ja) * | 2023-01-19 | 2024-07-25 | 日本ピストンリング株式会社 | 内燃機関用鉄基焼結合金製バルブシートおよびその製造方法 |
WO2024154812A1 (ja) * | 2023-01-19 | 2024-07-25 | 日本ピストンリング株式会社 | 内燃機関用鉄基焼結合金製バルブシートおよびその製造方法 |
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JP7143356B2 (ja) | 2020-03-10 | 2022-09-28 | 大同メタル工業株式会社 | 摺動部材及びその製造方法並びに硬質物の製造方法 |
CN112301255B (zh) * | 2020-10-27 | 2021-07-30 | 上海交通大学 | 一种模具用高导热高强Co-Fe-Ni合金及其增材制造方法 |
US11988294B2 (en) | 2021-04-29 | 2024-05-21 | L.E. Jones Company | Sintered valve seat insert and method of manufacture thereof |
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JP4716366B2 (ja) | 2005-10-24 | 2011-07-06 | 日立粉末冶金株式会社 | 焼結バルブシートの製造方法 |
JP4582587B2 (ja) | 2005-10-12 | 2010-11-17 | 日立粉末冶金株式会社 | 耐摩耗性焼結部材の製造方法 |
US7757396B2 (en) | 2006-07-27 | 2010-07-20 | Sanyo Special Steel Co., Ltd. | Raw material powder for laser clad valve seat and valve seat using the same |
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2014
- 2014-01-31 WO PCT/JP2014/052241 patent/WO2014119720A1/ja active Application Filing
- 2014-01-31 JP JP2014559770A patent/JP6290107B2/ja active Active
- 2014-01-31 BR BR112015018090A patent/BR112015018090A2/pt not_active Application Discontinuation
- 2014-01-31 US US14/764,299 patent/US10428700B2/en active Active
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JPH05202451A (ja) * | 1992-01-28 | 1993-08-10 | Teikoku Piston Ring Co Ltd | バルブシート用焼結合金 |
JP2005248234A (ja) * | 2004-03-03 | 2005-09-15 | Nippon Piston Ring Co Ltd | バルブシート用鉄基焼結合金材 |
JP2008030071A (ja) * | 2006-07-27 | 2008-02-14 | Sanyo Special Steel Co Ltd | レーザー肉盛バルブシート用原料粉末およびこれを用いたバルブシート |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2016141154A1 (en) * | 2015-03-03 | 2016-09-09 | Materion Corporation | Light weight high stiffness metal composite |
CN109570509A (zh) * | 2018-12-18 | 2019-04-05 | 宁波申禾轴承有限公司 | 一种高强度轴承的制备方法 |
WO2024154811A1 (ja) * | 2023-01-19 | 2024-07-25 | 日本ピストンリング株式会社 | 内燃機関用鉄基焼結合金製バルブシートおよびその製造方法 |
WO2024154812A1 (ja) * | 2023-01-19 | 2024-07-25 | 日本ピストンリング株式会社 | 内燃機関用鉄基焼結合金製バルブシートおよびその製造方法 |
Also Published As
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JPWO2014119720A1 (ja) | 2017-01-26 |
US10428700B2 (en) | 2019-10-01 |
US20150369090A1 (en) | 2015-12-24 |
JP6290107B2 (ja) | 2018-03-07 |
BR112015018090A2 (pt) | 2017-07-18 |
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