JP4582587B2 - Method for producing wear-resistant sintered member - Google Patents

Method for producing wear-resistant sintered member Download PDF

Info

Publication number
JP4582587B2
JP4582587B2 JP2005298017A JP2005298017A JP4582587B2 JP 4582587 B2 JP4582587 B2 JP 4582587B2 JP 2005298017 A JP2005298017 A JP 2005298017A JP 2005298017 A JP2005298017 A JP 2005298017A JP 4582587 B2 JP4582587 B2 JP 4582587B2
Authority
JP
Japan
Prior art keywords
powder
hard phase
wear
mass
amount
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
JP2005298017A
Other languages
Japanese (ja)
Other versions
JP2007107034A (en
Inventor
辰明 吉弘
英昭 河田
Original Assignee
日立粉末冶金株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 日立粉末冶金株式会社 filed Critical 日立粉末冶金株式会社
Priority to JP2005298017A priority Critical patent/JP4582587B2/en
Priority claimed from GB0620185A external-priority patent/GB2431166B/en
Publication of JP2007107034A publication Critical patent/JP2007107034A/en
Application granted granted Critical
Publication of JP4582587B2 publication Critical patent/JP4582587B2/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Description

  The present invention relates to a method for manufacturing a wear-resistant sintered member suitable for various sliding members, and particularly to a method for manufacturing a wear-resistant sintered member used for sliding under high surface pressure.
  Sintered parts by powder metallurgy are easy to disperse a desired hard phase in an alloy matrix, and are applied to various sliding members such as sliding members for internal combustion engines such as automobiles and bearings. However, in recent years, the use environment has become severe with the improvement in performance of equipment in which the sliding member is incorporated. To cope with this, the sintered sliding member is required to have higher wear resistance. It has become like this. Further, depending on the application site, wear resistance at high temperature and oxidation resistance are required, and as the application range is expanded, improvement in wear resistance in various environments is desired.
    Under such circumstances, a wear-resistant sintered member in which a Co—Mo—Si—Cr hard phase or a high-speed hard phase is dispersed has been proposed for various uses (Patent Documents 1 to 3, etc.). Also, wear-resistant sintered members in which various improved hard phases are dispersed have been proposed (Patent Documents 4 to 6 and the like).
JP-A-08-109450 Japanese Patent Laid-Open No. 02-270943 Japanese Patent Laid-Open No. 01-068447 JP 2002-356704 A JP 2003-119542 A JP 2005-154798 A
  The hard phases proposed in Patent Documents 1 to 6 each exhibit excellent characteristics. However, when a large amount of hard phase forming elements are added to further improve the wear resistance, the wear resistance is rather reduced. It has been shown that the strength decreases. Therefore, if the cause of the decrease in wear resistance due to the addition of a large amount of the hard phase forming element can be removed, the wear resistance can be greatly improved by effectively utilizing the hard phase. Therefore, an object of the present invention is to disperse the hard phase in a larger amount in the matrix without impairing the wear resistance and strength.
The method for producing a wear-resistant sintered member according to the present invention is a method for producing a wear-resistant sintered member by compacting and sintering a raw material powder containing a matrix-forming powder and a hard phase-forming powder. 90% by mass or more is a fine powder having a maximum particle size of 46 μm, and the addition amount of the hard phase forming powder is 40 to 70% by mass , and the hard phase forming powder is, by mass ratio, Mo: 20 to 60%, Cr : 3 to 12%, Si: 1 to 12%, the balance being a composition composed of Co and inevitable impurities .
  Since the hard phase forming powder is hard, if it is contained in a large amount in the raw material powder, the compressibility of the raw material powder is impaired, and the density of the green compact decreases. Even if such a low-density green compact is sintered, the density is not improved, and only a low-density sintered body can be obtained. As a result, strength and wear resistance are lowered. Also, even if you try to increase the density of the green compact by increasing the molding pressure during compacting, the hard hard phase forming powder has a high elastic modulus, so it will be compressed and elastically deformed when it is extracted from the mold after molding. The hard phase forming powder is elastically recovered. As a result, the adhesion state between the powders formed at the time of molding is destroyed, and even if sintered, the powders are not fused (neck growth), and the strength and wear resistance are reduced.
  On the other hand, when fine powder is used as the raw material powder, the surface area of the entire powder is increased, and the contact area between the powders is increased accordingly. The use of fine powder is also known to impair the filling and compressibility of the raw material powder. For this reason, the use of fine powder as a method for improving the green density has not been performed.
  The present inventors have focused on fine powders that are inferior in compressibility but become densified by sintering, and have come to think of using them together with hard phase forming powders. As a result, it was found that by adding a predetermined amount or more of fine powder, wear resistance and strength are greatly improved by densification even if a large amount of hard phase forming powder is added. The present invention has been made on the basis of such knowledge. In the manufacturing method of the wear-resistant sintered member, the raw material powder including the base forming powder and the hard phase forming powder is compacted and sintered. 90% by mass or more of the powder is a fine powder having a maximum particle size of 46 μm, and the ratio of the hard phase forming powder to the raw material powder is 40 to 70% by mass. In the present invention, the compressibility is inferior because a large amount of hard phase forming powder and fine base forming powder are used, but the compacting effect after sintering due to the increase in the surface area of the whole powder by the fine powder is compressible. There is more to compensate for the decline. Therefore, since a sintered body having a sufficient sintered density can be obtained, the characteristics of the hard phase forming powder can be sufficiently exhibited to improve the wear resistance and strength.
  The raw material powder having a maximum particle size of 46 μm is used, which can be obtained by classification with a 325 mesh sieve comb. At this time, in the case of a powder having a large aspect ratio (major axis / minor axis), the powder having a minor axis of 46 μm or less may pass through the sieve comb even if the major axis exceeds 46 μm. Corresponds to the “maximum particle size of 46 μm” of the present invention. In order to obtain the effects of the present invention as described above, it is necessary that 90% by mass or more of fine powder having a particle size of 46 μm or less is included in the base forming powder.
  Since the densification action during sintering can be sufficiently achieved by densifying the base-forming powder, it is not particularly necessary to use fine powder up to the hard-phase-forming powder, and the hard-phase has a particle size configuration that has been used conventionally. May be used. However, it is preferable that the hard phase forming powder contains a large amount of fine powder because a further densifying action can be obtained.
  It is known that the use of fine powder in the powder metallurgy method reduces the fluidity and filling ability of the raw material powder. As a countermeasure against this, a method of granulating the fine powder to a certain size has been adopted. In the present invention, such a granulation method may be applied.
Here, the hard phase forming powder is preferably silicide alloy phase by sintering and forms a hard phase comprising a tissue dispersed. Especially in a weight ratio of the hard phase forming powder in the present invention, Mo: 20~60%, Cr: 3~12%, Si: 1~12%, the remainder is assumed to have a composition consisting of Co and inevitable impurities. The hard phase formed by this type of hard phase forming powder has a metal structure in which precipitated particles mainly composed of molybdenum silicide providing wear resistance and lubricity are dispersed in a Co alloy phase having corrosion resistance and heat resistance. Very effective as a wearable sintered member.
  In addition, the base formation powder can use what was used conventionally, such as the said patent documents 1-6, for example. Further, for example, 0.1 to 1.2% by mass of graphite powder can be added to the raw material powder in order to strengthen the iron base and to form carbides. In addition, machinability improving powder for improving machinability such as manganese sulfide and magnesium silicate mineral can be added.
  Some sliding members of internal combustion engines place importance on corrosion resistance. For such applications, use of stainless steel powder as a base forming powder further improves corrosion resistance while ensuring wear resistance. A wear-resistant sintered member can be obtained. Any stainless steel powder can be used. For example, a ferritic stainless steel containing 11 to 32% by mass of Cr and having high corrosion resistance against an oxidizing acid can be used, and the strength containing 0.15 to 1.2% by mass of C and Martensitic stainless steel with improved wear resistance can be used. In addition, austenitic stainless steel containing 11 to 32% by mass of Cr and 3.5 to 22% by mass of Ni and having improved corrosion resistance against non-oxidizing acid can be used.
  Furthermore, by containing 0.3 to 7% by mass of Mo in the stainless steel, it is possible to improve creep resistance, acid resistance, corrosion resistance, and spot corrosion resistance and to improve free-cutting properties. Further, by containing 1 to 4% by mass of Cu, acid resistance, corrosion resistance, and spot corrosion resistance can be improved, and precipitation curability can be imparted. Moreover, by containing 0.1-5 mass% of Al, while improving weldability and heat resistance, precipitation hardenability can be provided. Further, by containing N in an amount of 0.3% by mass or less, crystal grains can be adjusted, and since N is an alternative element to Ni, the amount of expensive Ni can be reduced. Further, since Mn is an alternative element of Ni, it can be contained in an amount of 5.5 to 10% by mass for reducing the amount of Ni. By containing 0.15 to 5% by mass of Si, oxidation resistance, heat resistance, and sulfuric acid resistance can be improved. By containing Nb of 0.45% by mass or less, intergranular corrosion resistance Can be improved. Furthermore, weldability can be improved by containing 0.15 mass% or less of Se, and machinability is improved by containing 0.2 mass% or less of P and 0.15 mass% or less of S. Can be improved.
  According to the present invention, a wear-resistant sintered member containing a large amount of a hard phase and having a sufficient sintered body density can be obtained, so that the wear resistance and strength of a conventional wear-resistant sintered member can be improved. It can be improved further. Moreover, the use of stainless steel powder as the base forming powder improves the corrosion resistance of the base, and is suitable when the corrosion resistance is important as well as the wear resistance.
[Example 1]
As a base forming powder, a stainless steel powder corresponding to JIS standard SUS316 having a particle size constitution shown in Table 1 and a hard phase forming powder in terms of mass ratio, Mo: 28%, Si: 2.5%, Cr: 8% and the balance Prepared a Co-based alloy powder composed of Co and inevitable impurities, and 60 mass% of the hard phase forming powder was added to and mixed with the base forming powder to obtain a raw material powder. A green compact obtained by compacting this raw material powder into a disk shape with a molding pressure of 1.2 GPa and a diameter of 30 mm and a thickness of 10 mm was sintered at 1250 ° C. × 1 Hr in an ammonia gas atmosphere, and sample number Samples 01 to 05 were prepared. About these samples, while measuring the density ratio, the reciprocating sliding friction test was done and the amount of wear after a test was measured. These results are also shown in Table 1.
  The reciprocating sliding friction test is a friction test in which the disc-shaped test piece is reciprocally slid while pressing the side surface of a roll (counter member) having a diameter of 15 mm and a thickness of 22 mm with a predetermined load. In this test, the surface of the steel made in accordance with JIS standard SUS316 as a roll material is chromized (the surface is coated with chromium and a hard iron-chromium intermetallic compound layer is formed to provide wear resistance, seizure resistance, corrosion resistance, etc. The load is 40 N, the frequency of reciprocating sliding is 20 Hz, the amplitude of reciprocating sliding is 1.5 mm, the test time is 20 min, and the test temperature is room temperature. A sliding friction test was conducted. The results are shown in Table 1 and shown in FIG.
  As can be seen from FIG. 1, in Sample No. 05 using the base forming powder with a fine powder ratio of 40% by mass, the amount of the hard phase forming powder is as large as 60% by mass, so the density of the green compact is reduced. Even with sintering due to this decrease in density, the density ratio is as low as 83%. For this reason, the base strength is reduced and the amount of wear is also increased. On the other hand, as the proportion of fine powder of 46 μm or less in the base forming powder increases, densification by sintering is promoted, and the density ratio of the sample increases linearly and the amount of wear decreases. And when the ratio of the fine powder of 46 micrometers or less in a base formation powder will be 90%, it turns out that a density ratio will be 90% and the amount of wear will fall rapidly.
[Example 2]
A stainless steel powder corresponding to JIS standard SUS316 in which the ratio of the powder of 46 μm or less used in sample number 02 of Example 1 as the base forming powder is 95%, and a Co-based alloy powder used in Example 1 as the hard phase forming powder Were prepared, and the raw material powders were mixed at the ratio shown in Table 2. Using this raw material powder, compacts were formed and sintered under the same conditions as in Example 1 to prepare samples Nos. 06-10. Table 2 and FIG. 2 show the results of performing the same tests as those of Example 1 on these samples, together with the test results of Sample No. 02 of Example 1.
  As can be seen from FIG. 2, in Sample No. 06 in which the addition amount of the hard phase forming powder is less than 40% by mass, the wear amount is large because the dispersion amount of the hard phase is small despite the high density ratio. . On the other hand, when the addition amount of the hard phase forming powder is 40% by mass or more, the wear amount is reduced and the wear resistance is improved. However, the density ratio tends to decrease as the addition amount of the hard phase forming powder increases, and in Sample No. 10 in which the addition amount of the hard phase forming powder exceeds 70% by mass, the density ratio is significantly decreased. The strength and wear resistance of the steel deteriorate and the amount of wear increases. From the above, it was confirmed that the addition amount of the hard phase forming powder has an effect of improving the wear resistance in the range of 40 to 70% by mass.
[Example 3]
A stainless steel powder corresponding to JIS standard SUS316 in which the ratio of the powder of 46 μm or less used in sample number 02 of Example 1 as the base forming powder is 95%, and a Co-based alloy powder having the composition shown in Table 3 as the hard phase forming powder Was prepared, and 60 mass% of the hard phase forming powder was added to the base forming powder and mixed to obtain a raw material powder. Using these raw material powders, compacts were formed and sintered under the same conditions as in Example 1 to prepare samples Nos. 11 to 16. Table 3 and FIG. 3 show the results of performing the same tests as those of Example 1 on these samples, together with the evaluation results of Sample No. 02 of Example 1.
  As can be seen from FIG. 3, in Sample No. 11 in which the amount of Mo in the Co-based alloy powder used as the hard phase is less than 20% by mass, the amount of wear of molybdenum silicide is small and the wear amount is large. On the other hand, in the sample in which the Mo amount in the Co-based alloy powder is 20% by mass or more, the precipitation amount of molybdenum silicide increases and the wear amount tends to decrease as the Mo amount increases. However, the density ratio tends to decrease as the amount of Mo in the Co-based alloy powder increases, and in Sample No. 16 where the amount of Mo exceeds 60% by mass, the density ratio falls below 90% and the amount of wear increases rapidly. is doing. From the above, it was confirmed that when the Co—Mo—Si—Cr alloy powder is used as the hard phase forming powder, the Mo amount is preferably 20 to 60% by mass.
[Example 4]
As the base forming powder, a stainless steel powder corresponding to JIS standard SUS316 in which the ratio of the powder of 46 μm or less used in the sample number 03 of Example 1 is 90% and a hard phase forming powder having the composition shown in Table 4 are prepared. The raw powder was obtained by adding and mixing 60% by mass of the hard phase forming powder to the forming powder. Using these raw material powders, compacts were formed and sintered under the same conditions as in Example 1 to prepare samples Nos. 17 to 23. Table 4 shows the results of performing the same test as Example 1 on these samples, together with the test result of Sample No. 03 of Example 1.
As can be seen from Table 4, even when the addition amount of the hard phase forming powder is as large as 60% by mass, if the ratio of the powder of 46 μm or less is 90% or more as the base forming powder, the base forming powder and It was confirmed that excellent wear resistance was obtained even if the type of the hard phase forming powder was changed, and the effect of the present invention was confirmed. Sample numbers 22 and 23 are reference examples.
It is a graph which shows the relationship between the ratio of the powder of the particle size of 46 micrometers or less in an Example of this invention, a density ratio, and the amount of wear. It is a graph which shows the relationship between the addition amount of a hard phase formation powder in the Example of this invention, a density ratio, and the amount of wear. It is a graph which shows the relationship between the amount of Mo in the hard phase formation powder in an Example of this invention, a density ratio, and the amount of wear.

Claims (5)

  1. In the manufacturing method of the wear-resistant sintered member that compacts and sinters the raw material powder including the base forming powder and the hard phase forming powder,
    90% by mass or more of the base forming powder is a fine powder having a maximum particle size of 46 μm, and the ratio of the hard phase forming powder to the raw material powder is 40 to 70% by mass ,
    The hard phase forming powder has a mass ratio of Mo: 20 to 60%, Cr: 3 to 12%, Si: 1 to 12%, and the balance of Co and inevitable impurities. Manufacturing method of a property sintered member.
  2. The method for producing a wear-resistant sintered member according to claim 1, wherein the hard phase forming powder forms a hard phase having a structure in which silicide is dispersed in an alloy phase by sintering.
  3. The method for producing a wear-resistant sintered member according to claim 1 or 2 , wherein the base forming powder is an iron-based alloy powder containing 11 to 35 mass% of Cr.
  4. The said base formation powder contains 3.5-22 mass% of Ni further, The manufacturing method of the wear-resistant sintered member of Claim 3 characterized by the above-mentioned.
  5. The base forming powder is, by mass ratio, Mo: 0.3 to 7%, Cu: 1 to 4%, Al: 0.1 to 5%, N: 0.3% or less, Mn: 5.5 to 10 %, Si: 0.15 to 5%, Nb: 0.45% or less, P: 0.2% or less, S: 0.15% or less, and Se: 0.15% or less The method for producing a wear-resistant sintered member according to claim 3 or 4 , further comprising:
JP2005298017A 2005-10-12 2005-10-12 Method for producing wear-resistant sintered member Active JP4582587B2 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP2005298017A JP4582587B2 (en) 2005-10-12 2005-10-12 Method for producing wear-resistant sintered member

Applications Claiming Priority (8)

Application Number Priority Date Filing Date Title
JP2005298017A JP4582587B2 (en) 2005-10-12 2005-10-12 Method for producing wear-resistant sintered member
GB0620185A GB2431166B (en) 2005-10-12 2006-10-12 Manufacturing method for wear resistant sintered member, sintered valve seat, and manufacturing method therefor
CN2006101318515A CN1947896B (en) 2005-10-12 2006-10-12 Method of manufacturing the anti-wear sintered member
KR20060099227A KR100850152B1 (en) 2005-10-12 2006-10-12 Method of manufacturing the anti-wear sintered member, sintered valve seat, and method of manufacturing the same
US11/546,462 US7892481B2 (en) 2005-10-12 2006-10-12 Manufacturing method for wear resistant sintered member, sintered valve seat, and manufacturing method therefor
DE200610048442 DE102006048442B4 (en) 2005-10-12 2006-10-12 A method of manufacturing a wear resistant sintered element, a sintered valve seat, and manufacturing methods therefor
CN 201110094067 CN102172775B (en) 2005-10-12 2006-10-12 Method of manufacturing sintered valve seat
GB0724036A GB2446911B (en) 2005-10-12 2007-12-10 Manufacturing method for wear resistant sintered member, sintered valve seat, and manufacturing method therefor

Publications (2)

Publication Number Publication Date
JP2007107034A JP2007107034A (en) 2007-04-26
JP4582587B2 true JP4582587B2 (en) 2010-11-17

Family

ID=38017578

Family Applications (1)

Application Number Title Priority Date Filing Date
JP2005298017A Active JP4582587B2 (en) 2005-10-12 2005-10-12 Method for producing wear-resistant sintered member

Country Status (2)

Country Link
JP (1) JP4582587B2 (en)
CN (1) CN1947896B (en)

Families Citing this family (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5122904B2 (en) * 2007-10-05 2013-01-16 日立粉末冶金株式会社 Manufacturing method of sintered composite sliding parts
JP5125488B2 (en) * 2007-12-26 2013-01-23 大同特殊鋼株式会社 Hard particle powder for sintered body and sintered body
JP5987284B2 (en) * 2011-09-07 2016-09-07 日立化成株式会社 Sintered alloy and method for producing the same
CN102517520B (en) * 2011-12-16 2013-06-12 欧阳文 Balancing block of nonmagnetic compressor motor
JP2013163854A (en) * 2012-02-13 2013-08-22 Diamet:Kk Sintered member
CN102660709A (en) * 2012-04-24 2012-09-12 邓湘凌 High-strength wear-resisting alloy and preparation method thereof
US10428700B2 (en) 2013-01-31 2019-10-01 Nippon Piston Ring Co., Ltd. Highly wear-resistant valve seat for use in internal combustion engine
CN103406535A (en) * 2013-07-02 2013-11-27 安徽瑞泰汽车零部件有限责任公司 Powder metallurgy brake caliper iron alloy and manufacturing method thereof
CN103602902B (en) * 2013-10-10 2016-03-09 铜陵新创流体科技有限公司 A kind of Powder metallurgy pressure-resistant composite metal material and preparation method thereof
CN103602900B (en) * 2013-10-10 2016-03-09 铜陵新创流体科技有限公司 A kind of Powder metallurgy flange and preparation method thereof
CN104819126B (en) * 2015-03-02 2018-04-10 广东美芝制冷设备有限公司 Bearing and preparation method and compressor and refrigeration plant for compressor
EP3156155A1 (en) * 2015-10-15 2017-04-19 Höganäs AB (publ) Iron based powders for powder injection molding
CN105603261A (en) * 2016-02-20 2016-05-25 胡清华 Plastic extrusion molding handpiece
CN105803265A (en) * 2016-03-20 2016-07-27 魏天 Engine cam
US10837087B2 (en) * 2016-09-28 2020-11-17 Tenneco Inc. Copper infiltrated molybdenum and/or tungsten base powder metal alloy for superior thermal conductivity
JP6536866B1 (en) * 2017-12-28 2019-07-03 日立化成株式会社 Sintered bearing, sintered bearing device and rotating device
JP2019143176A (en) 2018-02-16 2019-08-29 大同特殊鋼株式会社 Hard particle powder for sintered bodies

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS56139604A (en) * 1980-03-31 1981-10-31 Toshiba Corp Iron sintered parts
JPH0711377A (en) * 1993-06-24 1995-01-13 Daido Steel Co Ltd Production of sintered tool steel
JPH08134583A (en) * 1994-11-10 1996-05-28 Hitachi Metals Ltd Production of sintered hard alloy excellent in machinability
JPH1121659A (en) * 1997-06-30 1999-01-26 Nippon Piston Ring Co Ltd Wear resistant iron-base sintered alloy material
JP2004124162A (en) * 2002-10-02 2004-04-22 Mitsubishi Materials Corp Manufacturing method of iron-based sintered alloy valve seat exhibiting wear resistance under high surface pressure applied condition
JP2005154798A (en) * 2003-11-21 2005-06-16 Hitachi Powdered Metals Co Ltd Alloy powder for forming hard phase, iron-based mixed powder using the same, method for manufacturing abrasion-resistant sintered alloy, and abrasion-resistant sintered alloy

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5232642B2 (en) * 1973-06-04 1977-08-23
CN1058650C (en) * 1995-10-05 2000-11-22 电子工业部第二研究所 Manufacture method of powder metallurgy valve seat
JP3952344B2 (en) * 1998-12-28 2007-08-01 日本ピストンリング株式会社 Wear-resistant iron-based sintered alloy material for valve seat and valve seat made of iron-based sintered alloy
JP2001050020A (en) * 1999-05-31 2001-02-23 Nippon Piston Ring Co Ltd Valve device for internal combustion engine
CN1142307C (en) * 2000-05-24 2004-03-17 曾佑鑫 Iron-base powder metallurgy air valve base for internal combustion engine and its production process
JP3926320B2 (en) * 2003-01-10 2007-06-06 日本ピストンリング株式会社 Iron-based sintered alloy valve seat and method for manufacturing the same
US7074253B2 (en) * 2003-05-20 2006-07-11 Exxonmobil Research And Engineering Company Advanced erosion resistant carbide cermets with superior high temperature corrosion resistance

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS56139604A (en) * 1980-03-31 1981-10-31 Toshiba Corp Iron sintered parts
JPH0711377A (en) * 1993-06-24 1995-01-13 Daido Steel Co Ltd Production of sintered tool steel
JPH08134583A (en) * 1994-11-10 1996-05-28 Hitachi Metals Ltd Production of sintered hard alloy excellent in machinability
JPH1121659A (en) * 1997-06-30 1999-01-26 Nippon Piston Ring Co Ltd Wear resistant iron-base sintered alloy material
JP2004124162A (en) * 2002-10-02 2004-04-22 Mitsubishi Materials Corp Manufacturing method of iron-based sintered alloy valve seat exhibiting wear resistance under high surface pressure applied condition
JP2005154798A (en) * 2003-11-21 2005-06-16 Hitachi Powdered Metals Co Ltd Alloy powder for forming hard phase, iron-based mixed powder using the same, method for manufacturing abrasion-resistant sintered alloy, and abrasion-resistant sintered alloy

Also Published As

Publication number Publication date
CN1947896A (en) 2007-04-18
CN1947896B (en) 2012-01-11
JP2007107034A (en) 2007-04-26

Similar Documents

Publication Publication Date Title
KR100795273B1 (en) An abrasion resistant sintered member and method for manufacturing thereof
JP5902091B2 (en) Nitrogen-containing low nickel sintered stainless steel
US4734968A (en) Method for making a valve-seat insert for internal combustion engines
JP4213060B2 (en) Ferrous sintered alloy material for valve seats
US7089902B2 (en) Sintered alloy valve seat and method for manufacturing the same
JP3928782B2 (en) Method for producing sintered alloy for valve seat
JP2957180B2 (en) Wear-resistant iron-based sintered alloy and method for producing the same
US5273570A (en) Secondary hardening type high temperature wear-resistant sintered alloy
CN100374605C (en) Power-matallurgy valve seat inserts
KR100850152B1 (en) Method of manufacturing the anti-wear sintered member, sintered valve seat, and method of manufacturing the same
ES2646789T3 (en) Prealloyed Iron Powder
US9212572B2 (en) Sintered valve guide and production method therefor
JP2010500474A (en) Improved powder metallurgy composition
CA2172029C (en) A metal sintered body composite material and a method for producing the same
JP4183346B2 (en) Mixed powder for powder metallurgy, iron-based sintered body and method for producing the same
KR101316474B1 (en) Valve seat of engine and manufacturing method therof
JP5504278B2 (en) Method for producing diffusion-alloyed iron or iron-based powder, diffusion-alloyed powder, composition comprising the diffusion-alloyed powder, and molded and sintered parts produced from the composition
JP5858921B2 (en) Ferrous sintered powder metal for wear resistant applications
CA2528698C (en) Mixed powder for powder metallurgy
WO2009122985A1 (en) Iron-base sintered alloy for valve sheet and valve sheet for internal combustion engine
CN101124058B (en) Stainless steel powder
JP5939384B2 (en) Sintered alloy and method for producing the same
US6712871B2 (en) Sintered alloy for valve seat having excellent wear resistance and method for producing the same
US8038761B2 (en) Iron-based sintered material and production method thereof
US5312475A (en) Sintered material

Legal Events

Date Code Title Description
A621 Written request for application examination

Free format text: JAPANESE INTERMEDIATE CODE: A621

Effective date: 20080403

A977 Report on retrieval

Free format text: JAPANESE INTERMEDIATE CODE: A971007

Effective date: 20100209

A131 Notification of reasons for refusal

Free format text: JAPANESE INTERMEDIATE CODE: A131

Effective date: 20100212

A521 Written amendment

Free format text: JAPANESE INTERMEDIATE CODE: A523

Effective date: 20100402

TRDD Decision of grant or rejection written
A01 Written decision to grant a patent or to grant a registration (utility model)

Free format text: JAPANESE INTERMEDIATE CODE: A01

Effective date: 20100825

A01 Written decision to grant a patent or to grant a registration (utility model)

Free format text: JAPANESE INTERMEDIATE CODE: A01

A61 First payment of annual fees (during grant procedure)

Free format text: JAPANESE INTERMEDIATE CODE: A61

Effective date: 20100825

R150 Certificate of patent or registration of utility model

Ref document number: 4582587

Country of ref document: JP

Free format text: JAPANESE INTERMEDIATE CODE: R150

Free format text: JAPANESE INTERMEDIATE CODE: R150

FPAY Renewal fee payment (event date is renewal date of database)

Free format text: PAYMENT UNTIL: 20130910

Year of fee payment: 3

S111 Request for change of ownership or part of ownership

Free format text: JAPANESE INTERMEDIATE CODE: R313111

R350 Written notification of registration of transfer

Free format text: JAPANESE INTERMEDIATE CODE: R350