WO2006114960A1 - Fe系焼結合金 - Google Patents
Fe系焼結合金 Download PDFInfo
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- WO2006114960A1 WO2006114960A1 PCT/JP2006/305907 JP2006305907W WO2006114960A1 WO 2006114960 A1 WO2006114960 A1 WO 2006114960A1 JP 2006305907 W JP2006305907 W JP 2006305907W WO 2006114960 A1 WO2006114960 A1 WO 2006114960A1
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- based sintered
- sintered alloy
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
- C22C33/0271—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5% with only C, Mn, Si, P, S, As as alloying elements, e.g. carbon steel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
Definitions
- the present invention relates to an Fe-based sintered alloy, and in particular, a mixing step of mixing Fe-Mn alloy powder, graphite powder, and Fe powder, a forming step of forming the mixed powder, and sintering the formed body. Relates to an Fe-based sintered alloy produced by a sintering process.
- Powder metallurgy technology is widely used because it has advantages such as easy dimensional control and complex shape molding, and low cost compared to parts manufacturing technology such as forging and forging.
- Fe-based sintered alloys are often used in sintered structural parts for automobiles.
- Fe-based sintered alloys Fe-Cu-based sintered alloys produced by mixing, forming, and sintering Fe powder, Cu powder, and graphite powder have been used.
- the Cu powder has the effect of increasing the mechanical strength of the sintered alloy by melting below the sintering temperature of the Fe powder and promoting the sintering with the Fe powder.
- the sintering temperature of Fe-Cu sintered alloy is generally 1100 ° C or higher and 1200 ° C or lower.
- Fe-Cu sintered alloys are applied to, for example, automotive clutch hubs and connecting ports.
- the Fe-based sintered alloy is improved in mechanical strength by adding various metal powders and alloy powders to the Fe powder.
- Fe-Mn-S produced by mixing Fe-Mn-Si alloy powder containing Mn and Si instead of Cu powder with Fe powder and graphite powder, forming, and sintering.
- the i-based sintered alloy is a sintered alloy with higher mechanical strength.
- This Fe-Mn-Si sintered alloy has a Fe-Mn-Si alloy powder whose liquidus is approximately 1200 ° C. In order to promote this, sintering is mainly performed at 1200 ° C or higher (for example, see Non-Patent Document 1).
- Patent Document 1 Zongy in Zhang, 1 outside, “Fe-Mn-Si master alloy steel by powder metal gear. powder metal lurgy proces s ing) "(Sweden), Journal of Alloys and Compounds, 2004, pp. 363, p.194-202
- Fe-Mn-Si alloy powder instead of Cu powder and sintering at the same sintering temperature as Fe-Cu based sintered alloy, Fe-Mn-Si alloy powder In the sintering of Fe and Fe powder, the diffusion of Mn and other elements between the powders may be suppressed by the acid film formed on the surface of the alloy powder by the Si in the alloy powder, and sintering may not be promoted There is.
- the addition of Si forms an intermetallic compound of Fe and Si in the Fe—Mn—Si alloy powder, so that the alloy powder becomes hard.
- the density of the compact is reduced, which in turn reduces the density of the sintered alloy, so that sufficient mechanical strength may not be obtained.
- an object of the present invention is to provide a mixing step of mixing Fe-Mn alloy powder, graphite powder, and Fe powder, a forming step of forming the mixed powder, and a sintering step of sintering the compact. It is to provide an Fe-based sintered alloy that is manufactured and has improved mechanical strength.
- the Fe-based sintered alloy according to the present invention includes a mixing step of mixing Fe-Mn alloy powder, graphite powder, and Fe powder, a forming step of forming the mixed powder, and a sintering step of sintering the compact.
- the mixing step includes Fe-Mn alloy powder of 5% by mass to 50% by mass, Graphite powder of 0.2% by mass to 2% by mass, and the balance. It is preferable to mix part of Fe powder.
- Fe 1 Mn alloy powder is used instead of Cu powder, it is the same as the conventional Fe-Cu-based 3 ⁇ 4fe bond gold.
- the mechanical strength can be further improved by the sintering temperature.
- FIG. 1 is a diagram showing a manufacturing process of an Fe-based sintered alloy in the embodiment of the present date.
- FIG. 2 shows the results of manufacturing the Fe—Mn alloy powder examples A to D, Fe—Mn alloy powder comparative examples E to F, and F e—Mn alloy »powder example G in the embodiment of the present invention.
- FIG. 6 is a diagram showing the yarn composition ratio of Mn and the like for Fe-Mn—Si alloy powder comparative examples H to J.
- FIG. 3 shows Fe-based sintered alloy examples 1 to 4, Fe-based sintered alloy comparative examples 5 to 7, Fe-based sintered alloy example 8 and Fe-sintered alloy in the embodiment of the present invention. It is a figure which shows the raw material powder mixing ratio etc. about Comparative Examples 9-16.
- FIG. 4 is a diagram showing the shape of a molded body molded by the molding process in the embodiment of the present invention.
- FIG. 5 is a photomicrograph showing the metal structure of Fe-based sintered alloy example 2 in the embodiment of the present invention.
- FIG. 6 is a diagram showing the tensile strength and the like when a plurality of molding conditions and sintering conditions are set for Fe-based sintered alloy examples 17 to 25 in the embodiment of the present invention.
- FIG. 4 is a diagram showing the Mn content and the like contained in a sintered alloy for Fe-based sintered alloy examples 26 to 31 in the embodiment of the present invention.
- FIG. 1 is a diagram showing a manufacturing process of an Fe-based sintered alloy.
- the Fe-based sintered alloy consists of a Fe-Mn alloy powder production process (S10) containing 2% to 30% by mass of M: n (S10), graphite powder
- S10 Fe-Mn alloy powder production process
- SI 2 the Fe powder manufacturing process
- S 16 the mixing process
- S 18 the forming process
- S20 a sintering step for sintering the formed body.
- the Fe-Mn alloy powder is manufactured and used by a gas fusing method with a small oxide content in the powder.
- a gas fusing method with a small oxide content in the powder.
- it can be manufactured by mechanical manufacturing methods such as pulverization, manufacturing methods by electrolysis, chemical manufacturing methods by reduction or thermal decomposition of oxides, water atomization method in which powder is produced from molten metal by injection, etc. Good.
- Mn contained in the Fe—Mn alloy powder has a role of promoting the sintering between the Fe—Mn alloy powder and the Fe powder by the diffusion of Mn at the time of sintering.
- the reason why the Mn content of the Fe—Mn alloy powder is 2% by mass or more is that if the Mn content is less than 2% by mass, the diffusion promotion of Mn is insufficient.
- the reason why the Mn content is 30% by mass or less is that the formability in the molding step (S18) is reduced and the mechanical strength of the sintered bond cannot be improved. Accordingly, Mn in the Fe—Mn alloy powder is used in a content of 2% by mass to 30% by mass.
- the Fe-Mn alloy powder is a powder that has passed through a sieve having a predetermined mesh in order to adjust the particle size. This is because if the particle size of the Fe-Mn alloy powder is large, the filling rate when the Fe-Mn alloy powder is formed by the forming step (S 18) is lowered, which affects the mechanical strength of the sintered alloy. .
- the particle size of the Fe—Mn alloy powder is, for example, 5 m or more and 50 m or less. Of course, the particle size of the Fe-Mn alloy powder may be 5 111 to 200 111 and 5/111 to 100 m, and is not particularly limited to these particle sizes. .
- the graphite powder is manufactured and used by a mechanical manufacturing method such as pulverization. Of course, it may be manufactured and used by a chemical manufacturing method such as thermal decomposition. Fe powder is manufactured and used by the water atomization method. Of course, it may be manufactured and used by a mechanical manufacturing method such as powdered stone, a gas atomizing method, a reducing method or the like.
- the mixing step (S 16) for mixing the Fe—Mn alloy powder, the graphite powder, and the Fe powder will be described.
- the mixed powder is Fe-Mn alloy powder 5 mass% or more 50 mass% % Or less, 0.2% by mass or more and 2% by mass or less of graphite powder, and a powder mixed at the mixing ratio of Fe powder remaining.
- Fe-Mn alloy powder is added to promote element diffusion between the powders during sintering.
- the reason why the Fe-Mn alloy powder is 5% by mass or more is that when the mixing ratio of the Fe-n alloy powder is less than 5% by mass, the diffusion of Mn is hardly promoted, and the mechanical strength of the sintered bond is not sufficiently improved. Because there is.
- the mixing ratio of the Fe_Mn alloy powder is set to 50 mass% or less because when the mixing ratio of the Fe—Mn alloy powder exceeds 50 mass 1 ⁇ 2, the formability in the molding step (S 18) decreases. This is because the mechanical strength of the sintered alloy cannot be improved. Therefore, the Fe—Mn alloy powder is used in a mixing ratio of 5 mass% or more and 50 mass% or less.
- Graphite powder is added to strengthen the Fe-based sintered alloy.
- the mixing ratio at the end of 13 ⁇ 4 is 0.2 mass% or more because if it is less than 0.2 mass%, the ferrite increases and the hardness of the sintered alloy decreases, so the mechanical strength decreases. Get it.
- the reason why the mixing ratio of the graphite powder is 2% by mass or less is that when the content exceeds 2% by mass, the cement content increases and the toughness of the sintered alloy decreases. Therefore, the graphite powder is used in a mixing ratio of 0.2% by mass or more and 2% by mass or less.
- the Fe—Mn alloy powder, the graphite powder, and the Fe powder are sufficiently dried, and then mixed in the mixer at the predetermined mixing ratio described above.
- a lubricant may also be mixed.
- a stearate salt for example, zinc stearate is used.
- the lubricant is not particularly limited to this, and other lubricants may be used.
- a mixer for mixing these powders for example, a V-type mixer is used, but it is not particularly limited thereto.
- the mixed powder is filled in a mold, for example, a mold or the like, to give a predetermined shape. Then, the mold filled with the mixed powder is pressed in the uniaxial direction to be molded.
- the pressurizing direction is not limited to the uniaxial direction, and pressurization may be performed in the same direction.
- the pressure for forming the mixed powder (for example, 80 OMpa is used. Of course, the pressure is 500 ⁇ ? & Or more and 15 O OMPa or less. The pressure may be lower, and is not particularly limited to these pressures.
- a press machine or the like is used when pressurizing in the uniaxial direction.
- a C IP (Cold Iso static Press in) device, a HIP (Hot I so attic pressing device), etc. are used. Any powder can be used as long as it can pressurize the pressure described above, and the present invention is not particularly limited to this, and the mixed powder is formed at room temperature, but is not limited to this. May be.
- the molded body formed with the mixed powder is taken out of the mold and sintered in a sintering furnace.
- a sintering atmosphere of the sintering furnace an inert gas such as argon gas or helium gas is used.
- the sintering atmosphere is not particularly limited to this, and ammonia decomposition gas, hydrogen, nitrogen gas, or the like may be used, or a vacuum atmosphere may be used.
- the sintering temperature may be 1100 ° C or higher and 1250 ° C or lower, and is not particularly limited to these temperatures.
- 30 minutes is used as the sintering time.
- the sintering time may be 10 minutes or more and 12 seconds or less, and is not particularly limited to these times.
- the sintering furnace used in the sintering step (S20) a general sintering furnace used in powder metallurgy can be used. There is no particular limitation as long as the sintering atmosphere, the sintering temperature, and the sintering time described above can be adjusted.
- Example 1 As described above, according to the Fe-based sintered alloy, sintering is promoted by diffusion of Mn in the Fe-Mn alloy powder into the Fe powder. The strength can be further improved. Accordingly, sintered structural parts for automobiles can be reduced in weight at low cost.
- Example 1 As described above, according to the Fe-based sintered alloy, sintering is promoted by diffusion of Mn in the Fe-Mn alloy powder into the Fe powder. The strength can be further improved. Accordingly, sintered structural parts for automobiles can be reduced in weight at low cost.
- Fig. 2 shows manufactured Fe-Mn alloy powder examples A to D, Fe-Mn alloy powder comparative examples E to F, Fe-Mn alloy powder example G, and Fe-Mn-Si alloy powder comparative examples It is a figure which shows the composition ratio etc. of Mn etc. about H to J.
- Alloy Powder Comparative Example H was manufactured by a gas atomizing method using an inert gas
- Alloy Powder Comparative Example I was manufactured by a pulverization method
- Alloy Powder Comparative Example J was manufactured by a water atomizing method.
- Alloy powder examples A to D are alloy powders having a Mn content of 2.5 mass%, 6 mass%, 18 mass%, and 28 mass%. Alloy Powder Examples A to D are Fe- ⁇ alloy powders containing 2% by mass to 30% by mass of Mn. In alloy powder comparative examples E and F, the Mn content is 1.5 mass% and 40 mass%, respectively. Alloy powder Examples A to D and alloy powder comparative examples E and F were classified using a 330 mesh sieve, and the particle size of the Fe-Mn alloy powder was adjusted to 50 m or less.
- Alloy Powder Example G the Mn content is 6% by mass. Alloy Powder Example G has a particle size of 100 ⁇ or more, and is an alloy powder larger than the particle size of other alloy powders. Alloy Powder Comparative Example ⁇ to J is a comparison with Fe-Mn alloy powder. This is an alloy powder manufactured for the purpose. In the alloy powder comparative examples H to J, the Mn content is 6% by mass, which is the same as the Mn content in the alloy powder example B. Also, alloy powder comparative examples H to J contain 2% by mass of Si. Comparison of alloy powders JH to J differ in the amount of oxygen contained in the alloy powder because the method for producing the alloy powder is different as described above.
- the alloy powder produced by the gas atomization method compared to 0.2 mass% of the oxygen content of the alloy powder comparative examples I and J Comparative Example H has the least amount of oxygen contained in the alloy powder.
- Alloy powder comparative examples H to J were classified using a 330 mesh sieve, and the particle size of each alloy powder was adjusted to 50 / m or less.
- Fig. 3 shows Fe-based sintered alloy examples 1 to 4, Fe-based sintered alloy comparative examples 5 to 7, Fe-based sintered alloy example 8 and Fe-based sintered alloy comparative examples 9 to 16. Is a diagram showing the raw material powder mixing ratio and the like.
- the mixing ratio of the alloy powder example A is 45% by mass
- the mixing ratio of the alloy powder example B is 30% by mass
- the mixing ratio of the alloy powder example C is 1
- the mixing ratio of the alloy powder Example D is 6% by mass.
- Fe-based sintered alloy Examples The mixing ratio of the Fe-Mn alloy powders in Examples 1 to 4 is 5 mass% or more and 50 mass % Or less.
- the mixing ratio of the alloy powder comparative example E is 60 mass% and 99 mass%.
- the alloy powder comparative example F has a Kumming ratio of 2 mass%.
- the mixing ratio of the alloy powder example G is 30% by mass.
- the mixing ratio of the graphite powders in Fe-based sintered alloy examples 1 to 4, Fe-based sintered alloy comparative example 5 force 7 and Fe-based sintered alloy example 8 is 1 mass each.
- the mixing ratio of the black lead powder is 0.2 mass% or more and 2 mass% or less.
- the ratio of the alloy powder comparative examples H to J is 30% by mass, and the mixing ratio of the graphite powder is 1% by mass.
- the mixing ratio of the alloy powder example B is 30% by mass. Further, in Fe-based sintered alloy comparative example 12, the mixing ratio of graphite powder is 0.1%, and in Fe-based sintered alloy comparative example 13, the mixing ratio of graphite powder is 2.5%.
- the mixing ratio of the alloy powder example A is 55% by mass
- the mixing ratio of the alloy powder example D is 3% by mass. is there.
- the mixing ratio of the graphite powders in Fe-based sintered alloy comparative examples 14 to 15 is 1% by mass.
- the Fe-based sintered alloy comparative example 16 is a conventional Fe-based sintered alloy in which Cu powder specified in JIS S MF4050 is mixed.
- the raw material powder of each Fe-based sintered alloy was mixed in the mixing step (S16) described above at the mixing ratio shown in FIG.
- 0.8 mass% of zinc stearate was added as a lubricant, and mixing was performed using a V-type mixer.
- FIG. 4 is a diagram showing the shape of the molded body formed by the forming step (S 18).
- the formed body formed by the forming step (S 18) was sintered by the above-described sintering chamber 1: (S 20). Sintering was performed using a sintering furnace in a nitrogen gas atmosphere at a sintering temperature of 1150 ° C. and a sintering time of 30 minutes.
- JIS A tensile test was performed at room temperature with Z2241.
- the specimen shape of the bow I tension test is the same as that shown in Fig. 4.
- the tensile test speed is 0.5 mm / min at the crosshead speed of the bow 1 tension tester.
- the Fe-based sintered alloys Examples 1 to 4 have a tensile strength of 6 2 OMPa or more and 65 OMPa or less. It is shown that the tensile strength is improved as compared with Comparative Example 16 of the Fe-based sintered alloy. In addition, the tensile strength was larger than the other Fe-based sintered alloys shown in Fig. 3, especially Fe-Mn-Si alloy powder: From Fe-based sintered alloy comparative examples 9 to 11 High tensile strength was also obtained.
- the Fe-based sintered alloy shown in Fig. 3 was subjected to a tightness measurement test according to JISZ 2501.
- the specimen shape for the density measurement test is the same as that shown in Fig. 4.
- the density of the Fe-based sintered alloy in Example 1 from 4, 7. 1 5 g / cm 3 or more 7. Atsubuko at 25 g / cm 3 or less . From this, the Fe-based sintered alloy Examples 1 to 4 have a higher density than the other Fe-based sintered alloys shown in FIG.
- Fig. 5 shows an example of Fe-based sintered alloy.
- the metallographic structure of Fig. 2 is shown by a micrograph.
- the analysis device used was an X-fountain micro-analysis device (model: MACHS 200, manufacturer: Shimadzu Corporation) Fe-based sintered alloy Examples 1 to 4 were formed from Fe powder
- the Mn concentration of the part to be produced was 1% by mass or more and 2% by mass or less Fe-based sintered alloy Examples 1 to 4 were made of Fe powder rather than the other Fe-based sintered alloys shown in FIG.
- the Mn concentration in the formed site is high, indicating that much Mn diffusion occurs from the Fe—Mn alloy powder to the Fe powder during sintering.
- FIG. 6 is a diagram showing the tensile strength and the like when a plurality of molding conditions and bonding conditions are set for the Fe-based sintered alloy examples 17 to 25.
- Fe-based sintered alloy Examples 17 to 25 were prepared by mixing 30% by mass of Alloy Powder Example B, 1% by mass of graphite powder, and the mixing ratio with Fe powder as the balance. Molding to add at S 18) This is an Fe-based sintered alloy produced by setting a plurality of pressures and sintering temperatures and sintering times in the sintering step (S20) described above.
- the sintering temperature 1 150 ° C and the sintering time 30 minutes are constant, and the molding pressure is set to 300 MPa, 500 MPa, and 1500 MPa.
- This is a manufactured Fe-based sintered alloy.
- Fe-based sintered alloy Examples 20 to 22 were manufactured by setting the forming pressure 80 OMPa and the sintering time 30 minutes constant, and setting the sintering temperature to 1050 ° C, 1 100 ° C and 1 250 ° C.
- Fe-based sintered alloy The Fe-type sintered gold examples 233 ⁇ 4 to 25 were produced by setting the molding pressure 80 OMPa and the sintering temperature 1 150 ° C., and setting the sintering time to 5 minutes, 10 minutes and 120 minutes. Fe-type sintered bond.
- Fe-based sintered alloy Examples 17 to 25 a tensile test and a density measurement test were performed by the test methods described above.
- an Fe-based sintered alloy with a tensile strength of 60 OMPa or more is molded at a molding pressure of 5 O OMPa or more and 150 OMPa or less, and the sintering temperature is 1 100 ° C or more and 1250 °.
- the density of the Fe-based sintered alloy having a tensile strength of 600 MPa or more was 7.2 g / cm 3 or more and 7.4 g / cm 3 or less.
- FIG. 7 is a diagram showing the Mn content and the like contained in the Fe-based sintered alloy for Fe-based sintered alloy Examples 26 to 31.
- Fe-based sintered alloy examples 26 and 29 are Fe-based sintered gold in which the alloy powder example A has a mixing ratio of 30% by mass and 15% by mass.
- Fe-based sintered alloy examples 27 and 30 are Fe-based sintered alloys in which the alloy powder example C has a mixing ratio of 25 mass% and 35 mass%.
- Fe-based sintered alloys 28 and 31 are Fe-based sintered alloys in which the alloy powder Example D has a mixing ratio of 15% by mass and 25% by mass. Further, Fe-based sintered alloy examples 26 and 31 have a mixing ratio force s 1 mass% of the graphite powder.
- Fe-based sintered alloy examples 26 to 31 powder was mixed at the raw material powder mixing ratio shown in FIG. It was molded by pressing at 80 OMPa, and the molded body was sintered by the above-described sintering step (S20), sintering temperature 1 150 ° C, sintering time 30 minutes.
- S20 sintering step
- sintering temperature 1 150 ° C sintering time 30 minutes.
- the tensile test, the density measurement test, and the analysis of the Mn concentration in the portion formed from the Fe powder were tested and analyzed by the above-described method.
- the Mn content in each Fe-based sintered alloy was measured and calculated using a high-frequency plasma analyzer (ICP).
- the Mn content in the sintered alloy is 0.8% by mass, 4.5% by mass, and 4.2% by mass. .
- the Mn content in the sintered alloy is 0.4 mass%, 6.3 mass%, and 7.0 mass%.
- the Fe-based sintered alloy has a tensile strength of 60 OMPa or more. Therefore, the content of Mn in the sintered alloy of Fe-based gold-bonded gold with a tensile strength of 600 MPa or more is 0.5 mass% or more and 5 mass% or less.
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Abstract
Description
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Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
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EP06729855A EP1873269A1 (en) | 2005-04-22 | 2006-03-17 | Iron-based sintered alloy |
US11/918,982 US20090064819A1 (en) | 2005-04-22 | 2006-03-17 | Fe-based sintered alloy |
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JP2005125202A JP2006299364A (ja) | 2005-04-22 | 2005-04-22 | Fe系焼結合金 |
JP2005-125202 | 2005-04-22 |
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WO2006114960A1 true WO2006114960A1 (ja) | 2006-11-02 |
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PCT/JP2006/305907 WO2006114960A1 (ja) | 2005-04-22 | 2006-03-17 | Fe系焼結合金 |
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US (1) | US20090064819A1 (ja) |
EP (1) | EP1873269A1 (ja) |
JP (1) | JP2006299364A (ja) |
KR (1) | KR20070112875A (ja) |
CN (1) | CN101163809A (ja) |
WO (1) | WO2006114960A1 (ja) |
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JP5308123B2 (ja) * | 2008-11-10 | 2013-10-09 | 株式会社神戸製鋼所 | 高強度組成鉄粉とそれを用いた焼結部品 |
CN106282742A (zh) * | 2015-05-26 | 2017-01-04 | 东南大学 | 一种高效率块状合金渗碳体的制备方法 |
JP6352959B2 (ja) * | 2016-02-04 | 2018-07-04 | トヨタ自動車株式会社 | 耐摩耗性鉄基焼結合金の製造方法、焼結合金用成形体、および耐摩耗性鉄基焼結合金 |
JP6431012B2 (ja) * | 2016-09-16 | 2018-11-28 | トヨタ自動車株式会社 | 耐摩耗性鉄基焼結合金の製造方法および耐摩耗性鉄基焼結合金 |
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JP2000509440A (ja) * | 1996-05-03 | 2000-07-25 | スタックポール リミテッド | 焼結、球状化及び温間成形による金属粉末品の製造方法 |
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US2489839A (en) * | 1946-04-30 | 1949-11-29 | Isthmian Metals Inc | Process for carburizing compacted iron articles |
US2903354A (en) * | 1956-10-16 | 1959-09-08 | Republic Steel Corp | Process for improving parts formed by powder metallurgy by addition of spiegeleisen to metal powders |
US5834640A (en) * | 1994-01-14 | 1998-11-10 | Stackpole Limited | Powder metal alloy process |
SE9404110D0 (sv) * | 1994-11-25 | 1994-11-25 | Hoeganaes Ab | Manganese containing materials having high tensile strength |
-
2005
- 2005-04-22 JP JP2005125202A patent/JP2006299364A/ja not_active Withdrawn
-
2006
- 2006-03-17 KR KR1020077024043A patent/KR20070112875A/ko not_active Application Discontinuation
- 2006-03-17 EP EP06729855A patent/EP1873269A1/en not_active Withdrawn
- 2006-03-17 CN CNA2006800134851A patent/CN101163809A/zh active Pending
- 2006-03-17 WO PCT/JP2006/305907 patent/WO2006114960A1/ja active Application Filing
- 2006-03-17 US US11/918,982 patent/US20090064819A1/en not_active Abandoned
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JP2000509440A (ja) * | 1996-05-03 | 2000-07-25 | スタックポール リミテッド | 焼結、球状化及び温間成形による金属粉末品の製造方法 |
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JP2006299364A (ja) | 2006-11-02 |
KR20070112875A (ko) | 2007-11-27 |
EP1873269A1 (en) | 2008-01-02 |
CN101163809A (zh) | 2008-04-16 |
US20090064819A1 (en) | 2009-03-12 |
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