WO2021038878A1 - 焼結材、及び焼結材の製造方法 - Google Patents

焼結材、及び焼結材の製造方法 Download PDF

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Publication number
WO2021038878A1
WO2021038878A1 PCT/JP2019/034296 JP2019034296W WO2021038878A1 WO 2021038878 A1 WO2021038878 A1 WO 2021038878A1 JP 2019034296 W JP2019034296 W JP 2019034296W WO 2021038878 A1 WO2021038878 A1 WO 2021038878A1
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Prior art keywords
sintered material
pores
less
powder
iron
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.)
Ceased
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PCT/JP2019/034296
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English (en)
French (fr)
Japanese (ja)
Inventor
朝之 伊志嶺
繁樹 江頭
一誠 嶋内
敬之 田代
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sumitomo Electric Sintered Alloy Ltd
Sumitomo Electric Industries Ltd
Original Assignee
Sumitomo Electric Sintered Alloy Ltd
Sumitomo Electric Industries Ltd
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.)
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Publication date
Application filed by Sumitomo Electric Sintered Alloy Ltd, Sumitomo Electric Industries Ltd filed Critical Sumitomo Electric Sintered Alloy Ltd
Priority to US17/637,809 priority Critical patent/US20220281000A1/en
Priority to CN201980099601.3A priority patent/CN114269960A/zh
Priority to DE112019007667.1T priority patent/DE112019007667T5/de
Priority to JP2021541960A priority patent/JP7114817B2/ja
Priority to PCT/JP2019/034296 priority patent/WO2021038878A1/ja
Publication of WO2021038878A1 publication Critical patent/WO2021038878A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/11—Making porous workpieces or articles
    • B22F3/1103—Making porous workpieces or articles with particular physical characteristics
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F5/08—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of toothed articles, e.g. gear wheels; of cam discs
    • 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
    • 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%
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16H—GEARING
    • F16H55/00—Elements with teeth or friction surfaces for conveying motion; Worms, pulleys or sheaves for gearing mechanisms
    • F16H55/02—Toothed members; Worms
    • F16H55/06—Use of materials; Use of treatments of toothed members or worms to affect their intrinsic material properties
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/35—Iron
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16H—GEARING
    • F16H55/00—Elements with teeth or friction surfaces for conveying motion; Worms, pulleys or sheaves for gearing mechanisms
    • F16H55/02—Toothed members; Worms
    • F16H55/17—Toothed wheels

Definitions

  • the present disclosure relates to a sintered material and a method for manufacturing the sintered material.
  • Patent Document 1 discloses an iron-based sintered body having a relative density of 93% or more.
  • the first sintered material of the present disclosure is A matrix made of metal and With a plurality of pores present in the mother phase, The average cross-sectional area of the pores in any cross section is 500 ⁇ m 2 or less. The relative density is 93% or more and 99.5% or less.
  • the second sintered material of the present disclosure is A matrix made of metal and With a plurality of pores present in the mother phase, The average peripheral length of the pores in any cross section is 100 ⁇ m or less. The relative density is 93% or more and 99.5% or less.
  • the method for producing the sintered material of the present disclosure is A step of pressurizing and compressing the raw material powder to prepare a powder compact having a relative density of 93% or more and 99.5% or less.
  • the step of sintering the powder compact is provided.
  • the raw material powder contains a powder made of an iron-based material having a Vickers hardness Hv of 80 or more and 200 or less.
  • the sintering temperature in the step of sintering the powder compact is 1000 ° C. or higher and lower than 1300 ° C.
  • FIG. 1 is a perspective view showing an example of the sintered material of the embodiment.
  • FIG. 2A shows the sample No. 1 prepared in Test Example 1. It is a micrograph which shows the cross section of the sintered material of 1.
  • FIG. 2B shows the sample No. 1 prepared in Test Example 1.
  • 2 is a photomicrograph showing a cross section of the sintered material of 2.
  • FIG. 2C shows the sample No. 1 prepared in Test Example 1.
  • 3 is a photomicrograph showing a cross section of the sintered material of 3.
  • FIG. 3 is a graph showing the average cross-sectional area of pores of the sintered material of each sample prepared in Test Example 1.
  • FIG. 4 is a graph showing the average perimeter of pores of the sintered material of each sample prepared in Test Example 1.
  • FIG. 5 is a graph showing the average value of the maximum diameters of the pores of the sintered material of each sample prepared in Test Example 1.
  • FIG. 6 is a graph showing the maximum value of the maximum diameter of the pores of the sintered material of each sample prepared in Test Example 1.
  • FIG. 7 is a graph showing the minimum value of the maximum diameter of the pores for the sintered material of each sample prepared in Test Example 1.
  • FIG. 8A shows the sample No. prepared in Test Example 1. It is a micrograph which shows the cross section of the sintered material of 101.
  • FIG. 8B shows the sample No. prepared in Test Example 1. It is a micrograph which shows the cross section of the sintered material of 102.
  • FIG. 8C shows the sample No. 1 prepared in Test Example 1. It is a micrograph which shows the cross section of the sintered material of 103.
  • one of the purposes of the present disclosure is to provide a sintered material having high strength and excellent productivity.
  • Another object of the present disclosure is to provide a method for producing a sintered material capable of producing a high-strength sintered material with high productivity.
  • the sintered material of the present disclosure has high strength and excellent productivity.
  • the method for producing a sintered material of the present disclosure can produce a high-strength sintered material with high productivity.
  • the sintered material according to one aspect of the present disclosure is A matrix made of metal and With a plurality of pores present in the mother phase, The average cross-sectional area of the pores in any cross section is 500 ⁇ m 2 or less. The relative density is 93% or more and 99.5% or less.
  • the sintered material according to one aspect of the present disclosure may be referred to as a first sintered material.
  • the first sintered material has high strength because cracks due to pores are unlikely to occur, and is also excellent in productivity.
  • the first sintered material has a relative density of 93% or more and is dense. If it is a dense sintered material, since there are few pores, the pores are unlikely to be the starting point of cracking. -Although the first sintered material contains a plurality of pores, each pore is unlikely to be the starting point of cracking. The reason for this is that if the average cross-sectional area of the pores is 500 ⁇ m 2 or less, it can be said that the cross-sectional area of many of the plurality of pores is small. Pore with a small cross-sectional area is unlikely to be the starting point of cracking.
  • the first sintered material is produced by, for example, sintering a dense powder compact having a relative density of 93% or more at a relatively low temperature.
  • the low sintering temperature makes it possible to reduce thermal energy.
  • a relatively low-density powder compact for example, a powder compact having a relative density of about 90% is sintered at a high temperature such that a liquid phase is generated, sintering having a relative density of 93% or more.
  • the material is obtained.
  • the pores tend to become large. For this point, it is advisable to refer to Test Example 1 described later. Large pores are likely to be the starting point for cracking. Since the pores serve as the starting point of cracking, the strength of the sintered material is reduced.
  • the dense powder compact is sintered at a relatively low temperature, a dense sintered material having small pores can be obtained. For this point, it is advisable to refer to Test Example 1 described later.
  • the above-mentioned high-temperature sintering is not performed, it is easy to obtain a sintered material having excellent shape accuracy and dimensional accuracy. Therefore, the yield tends to be high.
  • the above-mentioned dense powder compact has excellent machinability. Therefore, if the powder compact before sintering is subjected to a cutting process as needed, the processing time tends to be shortened. Further, it is easier to obtain a sintered material satisfying a predetermined size and shape. Therefore, the yield tends to be higher.
  • the sintered material according to another aspect of the present disclosure is A matrix made of metal and With a plurality of pores present in the mother phase, The average peripheral length of the pores in any cross section is 100 ⁇ m or less. The relative density is 93% or more and 99.5% or less.
  • the sintered material according to another aspect of the present disclosure may be referred to as a second sintered material.
  • the second sintered material has high strength because cracks due to pores are unlikely to occur. Further, the second sintered material is also excellent in productivity for the same reason as the first sintered material described above.
  • the second sintered material has a relative density of 93% or more and is dense. If it is a dense sintered material, since there are few pores, the pores are unlikely to be the starting point of cracking. -Although the second sintered material contains a plurality of pores, each pore is unlikely to be the starting point of cracking. The reason for this is that if the average peripheral length of the pores is 100 ⁇ m or less, it can be said that the peripheral length of many of the pores is short, and that the pores having a short peripheral length have a small cross-sectional area.
  • the first sintered material examples thereof include a form in which the average peripheral length of the pores in an arbitrary cross section is 100 ⁇ m or less.
  • first sintered material or the second sintered material examples thereof include a form in which the relative density is 96.5% or more.
  • the first sintered material or the second sintered material examples thereof include a form in which the average value of the maximum diameters of the pores is 5 ⁇ m or more and 30 ⁇ m or less.
  • the cross-sectional area of the pores is small, the circumference of the pores is short, and the average value of the maximum diameters of the pores is 30 ⁇ m or less, it can be said that many of the pores are short and small. Such pores are less likely to be the origin of cracks. Further, when the average value of the maximum diameter is 5 ⁇ m or more, the pores are not too small, so that the pressure when molding the powder compact is unlikely to be excessive. In this respect, the above-mentioned form is excellent in productivity.
  • the metal is an iron-based alloy and examples of the iron-based alloy include a form containing one or more elements selected from the group consisting of C, Ni, Mo, and B.
  • the method for producing a sintered material according to one aspect of the present disclosure is as follows.
  • the step of sintering the powder compact is provided.
  • the raw material powder contains a powder made of an iron-based material having a Vickers hardness Hv of 80 or more and 200 or less.
  • the sintering temperature in the step of sintering the powder compact is 1000 ° C. or higher and lower than 1300 ° C.
  • the method for producing the sintered material of the present disclosure can produce a high-strength sintered material with high productivity, as described below.
  • the powder compact before sintering is superior in cutting workability as compared with the sintered material after sintering. Therefore, in the above form, the processing time of the cutting process can be shortened. Further, since the cutting process can be performed satisfactorily, it is easy to obtain a sintered material having excellent shape accuracy and dimensional accuracy. Therefore, the above-mentioned form can further increase the yield.
  • the powder made of the iron-based material contains a powder made of an iron-based alloy and contains.
  • the iron-based alloy include a form containing at least one element of Mo of 0.1% by mass or more and 2.0% by mass or less and Ni of 0.5% by mass or more and 5.0% by mass or less.
  • the above form facilitates the production of an alloy powder having a Vickers hardness Hv of 80 or more and 200 or less.
  • the sintered material 1 of the embodiment will be described mainly with reference to FIG.
  • FIG. 1 shows an external gear as an example of the sintered material 1 of the embodiment.
  • the sintered material 1 of the embodiment is a dense sintered material mainly composed of metal. Further, the pores are small in an arbitrary cross section of the sintered material 1.
  • the sintered material 1 of the embodiment includes a matrix 10 made of metal and a plurality of pores 11 existing in the matrix 10 (see FIG. 2 described later).
  • the relative density of the sintered material 1 of the embodiment is 93% or more and 99.5% or less.
  • the average cross-sectional area of the pores 11 in an arbitrary cross section is 500 ⁇ m 2 or less.
  • the average peripheral length of the pores 11 in an arbitrary cross section is 100 ⁇ m or less.
  • the average cross-sectional area of the pores 11 here is an arbitrary cross section taken from the sintered material 1, and in this cross section, the cross-sectional area of each pore 11 is obtained for the plurality of pores 11, and the obtained cross-sectional areas are averaged. Is.
  • the average peripheral length of the pores 11 here is an arbitrary cross section taken from the sintered material 1, and in this cross section, the contour lengths of the pores 11 are obtained for the plurality of pores 11, and the obtained contour lengths are obtained. Is the average value.
  • Examples of the metal constituting the matrix 10 of the sintered material 1 of the embodiment include various pure metals or alloys.
  • Examples of pure metals include iron, nickel, titanium, copper, aluminum, magnesium and the like.
  • Examples of the alloy include iron-based alloys, titanium-based alloys, copper-based alloys, aluminum-based alloys, magnesium-based alloys, and the like. Alloys are generally stronger than pure metals. Therefore, the sintered material 1 in which the matrix 10 is an alloy is excellent in strength.
  • the iron-based alloy contains additive elements, the balance is composed of Fe (iron) and impurities, and is an alloy containing the largest amount of Fe.
  • the additive element include one or more elements selected from the group consisting of C (carbon), Ni (nickel), Mo (molybdenum), and B (boron).
  • Iron-based alloys containing the elements listed above in addition to Fe, such as steel, are excellent in strength such as having high tensile strength. Therefore, the sintered material 1 provided with the matrix 10 made of an iron-based alloy containing the above-mentioned additive element is excellent in strength.
  • the higher the content of each element the higher the strength tends to be. If the content of each element is not too high, the decrease in toughness and embrittlement are suppressed, and the toughness tends to increase.
  • Iron-based alloys containing C typically carbon steel, have excellent strength.
  • the content of C is, for example, 0.1% by mass or more and 2.0% by mass or less.
  • the content of C may be 0.1% by mass or more and 1.5% by mass or less, further 0.1% by mass or more and 1.0% by mass or less, and 0.1% by mass or more and 0.8% by mass or less.
  • the content of each element is a mass ratio with the iron-based alloy as 100% by mass.
  • Ni contributes to the improvement of toughness in addition to the improvement of strength.
  • the content of Ni is, for example, 0% by mass or more and 5.0% by mass or less.
  • the content of Ni may be 0.1% by mass or more and 5.0% by mass or less, further 0.5% by mass or more and 5.0% by mass or less, and further 4.0% by mass or less and 3.0% by mass or less. ..
  • Mo and B contribute to the improvement of strength.
  • Mo tends to increase the strength.
  • examples of the Mo content include 0% by mass or more and 2.0% by mass or less, 0.1% by mass or more and 2.0% by mass or less, and further 1.5% by mass or less.
  • the content of B includes, for example, 0% by mass or more and 0.1% by mass or less, and further 0.001% by mass or more and 0.003% by mass or less.
  • additive elements examples include Mn (manganese), Cr (chromium), Si (silicon) and the like.
  • the content of each of these elements is, for example, 0.1% by mass or more and 5.0% by mass or less.
  • the overall composition of the sintered material 1 can be analyzed by, for example, an energy dispersive X-ray analysis method (EDX or EDS), a high frequency inductively coupled plasma emission spectroscopic analysis method (ICP-OES), or the like.
  • EDX energy dispersive X-ray analysis method
  • ICP-OES high frequency inductively coupled plasma emission spectroscopic analysis method
  • the sintered material 1 of the embodiment includes a plurality of pores 11 in an arbitrary cross section, but each pore 11 is small. Therefore, each pore 11 is unlikely to be the starting point of cracking.
  • the sintered material 1 is excellent in strength because cracks due to the pores 11 are unlikely to occur.
  • ⁇ Cross-sectional area If the average cross-sectional area of the pores 11 is 500 ⁇ m 2 or less, it can be said that most of the pores 11 in the sintered material 1 are pores 11 having a small cross-sectional area. It can be said that the smaller the average cross-sectional area, the smaller the cross-sectional area of each pore 11. If each pore 11 is small, it is unlikely to be the starting point of cracking. From the viewpoint of reducing cracking due to pores 11, the average cross-sectional area is 480 .mu.m 2 or less, further 450 [mu] m 2 or less, particularly 430 m 2 or less.
  • the average cross-sectional area of the pores 11 tends to decrease as the relative density of the sintered material 1 increases. For example, if the molding pressure is increased in the manufacturing process of the sintered material 1 to increase the relative density of the powder compact, the relative density of the sintered material 1 is increased. As a result, the average cross-sectional area tends to be small. However, if the molding pressure is too high, the mold removal time tends to be long and the life of the mold tends to be shortened. At this point, productivity can be reduced. From the viewpoint of improving productivity, the average cross-sectional area may be, for example, 20 ⁇ m 2 or more, and further 30 ⁇ m 2 or more.
  • the average peripheral length of the pores 11 is 100 ⁇ m or less, it can be said that most of the pores 11 in the sintered material 1 are pores 11 having a short peripheral length.
  • the pore 11 having a short peripheral length has a small cross-sectional area. It can be said that the shorter the average peripheral length, the smaller the cross-sectional area of each pore 11. If each pore 11 is small, it is unlikely to be the starting point of cracking. From the viewpoint of reducing the occurrence of cracks caused by the pores 11, the average peripheral length is preferably 90 ⁇ m or less, more preferably 80 ⁇ m or less, and particularly preferably 70 ⁇ m or less.
  • the average peripheral length of the pores 11 tends to decrease as the relative density of the sintered material 1 increases. From the viewpoint of preventing the molding pressure from becoming excessive as described above and improving the productivity, the average peripheral length may be, for example, 10 ⁇ m or more, and further 15 ⁇ m or more.
  • the average cross-sectional area of the pores 11 is 500 ⁇ m 2 or less and the average peripheral length of the pores 11 is 100 ⁇ m or less. It can be said that most of the pores 11 in the sintered material 1 are pores 11 having a small cross-sectional area and a short peripheral length. Therefore, each pore 11 is unlikely to be the starting point of cracking. From the viewpoint of reducing the occurrence of cracks caused by the pores 11, it is preferable that the average cross-sectional area and the average peripheral length are smaller as described above.
  • the average value of the maximum diameters of the pores 11 is also small.
  • the average value of the maximum diameters of the pores 11 here is an arbitrary cross section taken from the sintered material 1, and in this cross section, the maximum diameter of each pore 11 is obtained for the plurality of pores 11, and the obtained maximum diameters are averaged. It is the value that was set.
  • the average value of the maximum diameter of the pores 11 is 5 ⁇ m or more and 30 ⁇ m or less.
  • the average value is preferably 28 ⁇ m or less, more preferably 25 ⁇ m or less, and particularly preferably 20 ⁇ m or less.
  • the average value is 5 ⁇ m or more, the pores 11 are not too small.
  • the average value may be 8 ⁇ m or more, and further 10 ⁇ m or more. From the viewpoint of the balance between high strength and good productivity, the average value is, for example, 10 ⁇ m or more and 25 ⁇ m or less.
  • the maximum value of the maximum diameter of the pore 11 is also small. This is because each pore 11 is unlikely to be the starting point of cracking.
  • the maximum value is, for example, 30 ⁇ m or less, more preferably 28 ⁇ m or less, and particularly preferably 25 ⁇ m or less.
  • the minimum value of the maximum diameter of the pore 11 is, for example, 3 ⁇ m or more and 20 ⁇ m or less, and further 5 ⁇ m or more and 18 ⁇ m or less, it is preferable in terms of improving productivity as described above.
  • the shape of the pores 11 is typically a different shape (see also FIG. 2).
  • One of the reasons why the shape of the pores 11 is not a simple curved shape such as a circular shape or an elliptical shape but a deformed shape is that a dense powder compact is sintered at a relatively low temperature, as will be described later. Be done.
  • the dark-colored, mainly black, particulate region and the white-edged particulate region are pores 11, and the rest is the matrix 10.
  • the relative density of the sintered material 1 of the embodiment is 93% or more and 99.5% or less. That is, the sintered material 1 contains the pores 11 in the range of 0.5% or more and 7% or less. When the content of the pores 11 is in the above range, the pores 11 are small and the sintered material 1 is dense. Since the number of pores 11 is small, the pores 11 are unlikely to be the starting point of cracking. The higher the relative density, the smaller the number of pores 11. From the viewpoint of reducing the occurrence of cracks caused by the pores 11, the relative density is preferably 94% or more, more preferably 95% or more, 96% or more, and particularly preferably 96.5% or more. The relative density may be 97% or more, 98% or more, 99% or more.
  • the relative density of the sintered material 1 is 99.5% or less, the above-mentioned molding pressure is prevented from becoming excessive and the productivity is enhanced. From the viewpoint of improving productivity, the relative density may be 99% or less.
  • the relative density of the sintered material 1 is, for example, 94% or more and 99% or less.
  • the sintered material 1 of the embodiment can be used for various general structural parts such as mechanical parts.
  • mechanical parts include various gears including sprockets, rotors, rings, flanges, pulleys, bearings and the like.
  • the sintered material 1 of the embodiment is dense, has excellent strength, and can be made compact. Therefore, the sintered material 1 of the embodiment can be suitably used for gears for which high strength, small size and light weight are desired, for example, a transmission of an automobile.
  • the relative density is high, the pores 11 are small, and the pores 11 are small in an arbitrary cross section.
  • the sintered material 1 of such an embodiment is excellent in strength because the pores 11 are unlikely to be the starting points of cracks. Further, if at least one of the plurality of pores 11 is a pore that opens on the surface of the sintered material 1, that is, an open pore, the sintered material 1 is excellent in durability, as will be described below. It also has the effect of being excellent in quietness.
  • the open pores can hold the lubricant.
  • the sintered material 1 is a sliding member such as a gear, seizure with the mating member is reduced by the lubricant held in the open pores.
  • Such a sliding member made of the sintered material 1 can be used satisfactorily for a long period of time.
  • the open pores can absorb sound. If the open pores are small as described above, the sound absorbed by the open pores is likely to be attenuated.
  • the sintered material 1 of the embodiment may be manufactured by, for example, a method for manufacturing a sintered material including the following steps.
  • First Step The raw material powder is pressure-compressed to produce a powder compact having a relative density of 93% or more and 99.5% or less.
  • Second Step The powder compact is sintered.
  • the sintering temperature shall be less than the liquidus temperature.
  • the relative density is 93% or more and 99.5% or less even at a relatively low temperature such as a sintering temperature of less than the liquid phase temperature.
  • a good sintered material that is, a sintered material having few pores can be obtained. The reason for this is that the sintered material typically maintains the relative density of the dust compact.
  • the powder compact has pores in the range of 0.5% or more and 7% or less. However, each pore is reduced by pressure compression.
  • a dense sintered material containing small pores can be obtained. So to speak, a sintered material in which the size and amount of pores in the powder compact is substantially maintained can be obtained. Since this sintered material has few pores and is small, the pores are unlikely to be the starting points of cracks and are excellent in strength.
  • the method for producing a sintered material of the embodiment includes the first step and the second step described above.
  • the raw material powder includes a powder made of an iron-based material having a Vickers hardness Hv of 80 or more and 200 or less.
  • the powder made of an iron-based material may be referred to as an iron-based powder.
  • the sintering temperature in the second step is 1000 ° C. or higher and lower than 1300 ° C.
  • the raw material powder includes a metal powder.
  • the metal powder is preferably made of a metal that is neither too soft nor too hard. Since the metal powder is not too hard, it is easily plastically deformed by pressure compression. Therefore, it is easy to obtain a dense powder compact having a relative density of 93% or more. Since the metal powder is not too soft, it is easy to obtain a powder compact having a relative density of 99.5% or less, that is, a powder compact containing pores.
  • the raw material powder may contain a metal powder having an appropriate composition depending on the composition of the parent phase of the sintered material. Further, the hardness of the metal powder may be adjusted according to the composition of the metal powder. Examples of adjusting the hardness of the metal powder include adjusting the above composition, heat-treating the metal powder, and adjusting the heat treatment conditions of the metal powder. For the composition of the metal powder, refer to the section (composition) of the above-mentioned [sintered material].
  • the raw material powder contains an iron-based powder.
  • the iron-based material is pure iron or an iron-based alloy. If the iron-based material is particularly an iron-based alloy, a high-strength sintered material can be obtained as described above.
  • the iron-based powder can be produced by, for example, a water atomizing method, a gas atomizing method, or the like.
  • the raw material powder includes a first alloy powder made of an iron-based alloy.
  • the iron-based alloy constituting the first alloy powder has the same composition as the iron-based alloy constituting the matrix of the sintered material.
  • the raw material powder includes a second alloy powder made of an iron-based alloy and a third powder made of a predetermined element.
  • the iron-based alloy constituting the second alloy powder contains some of the additive elements contained in the iron-based alloy constituting the matrix of the sintered material.
  • the element constituting the third powder is composed of each of the remaining additive elements among the above additive elements. That is, the third powder is composed of a single element.
  • the raw material powder includes pure iron powder and the above-mentioned second alloy powder and third powder.
  • the raw material powder includes pure iron powder and a third powder.
  • the third powder is composed of each of the additive elements in the iron-based alloy of the parent phase.
  • the matrix of the sintered material is an iron-based alloy containing one or more elements selected from the group consisting of Ni, Mo, and B and C, and the balance being Fe and impurities.
  • the second alloy powder may consist of the following iron-based alloys.
  • the iron-based alloy does not contain C, contains one or more elements selected from the above group, and the balance consists of Fe and impurities.
  • this iron-based alloy it is mentioned that it contains at least one element of Mo of 0.1% by mass or more and 2.0% by mass or less and Ni of 0.5% by mass or more and 5.0% by mass or less.
  • the iron-based alloy containing Mo and Ni in the above range has various compositions having a Vickers hardness Hv of 80 or more and 200 or less. Therefore, the powder made of the iron-based alloy is easy to produce.
  • the third powder include carbon powder and powder composed of one element selected from the above group.
  • a powder made of an iron-based material having a Vickers hardness Hv of 80 or more is not too soft.
  • a powder compact having pores in a specific range can be obtained as described above.
  • a powder made of an iron-based material having a Vickers hardness Hv of 200 or less is not too hard.
  • a dense powder compact can be obtained as described above.
  • the Vickers hardness Hv may be 90 or more and 190 or less, 100 or more and 180 or less, and 110 or more and 150 or less.
  • the size of the raw material powder can be selected as appropriate.
  • the average particle size of the above-mentioned alloy powder or pure iron powder is, for example, 20 ⁇ m or more and 200 ⁇ m or less, and further 50 ⁇ m or more and 150 ⁇ m or less.
  • the average particle size of the third powder excluding the carbon powder is, for example, about 1 ⁇ m or more and 200 ⁇ m or less.
  • the average particle size of the carbon powder is, for example, about 1 ⁇ m or more and 30 ⁇ m or less.
  • the average particle size of the powder here is the particle size (D50) at which the cumulative volume in the volume particle size distribution measured by the laser diffraction type particle size distribution measuring device is 50%.
  • the relative density of the powder compact may be 94% or more, further 95% or more, 96% or more, 96.5% or more, 97% or more, 98% or more.
  • the relative density of the powder compact may be 99.4% or less, and further 99.2% or less.
  • a typical example of producing a powder compact is to use a press device having a mold capable of uniaxial pressurization.
  • the shape of the mold may be selected according to the shape of the powder compact.
  • the shape of the dust compact may be a shape that follows the final shape of the sintered material or a shape that is different from the final shape of the sintered material. In the latter case, in the process after molding, processing such as cutting may be performed according to the final shape of the sintered material. The above cutting process is preferably performed on the powder compact before sintering, as will be described later.
  • Lubricant may be applied to the inner peripheral surface of the mold.
  • the lubricant tends to prevent the raw material powder from baking on the mold. Therefore, in addition to being excellent in shape accuracy and dimensional accuracy, it is easy to obtain a dense powder compact.
  • the lubricant include higher fatty acids, metal soaps, fatty acid amides, higher fatty acid amides and the like.
  • the molding pressure is, for example, 1560 MPa or more. Further, the molding pressure may be 1660 MPa or more, 1760 MPa or more, 1860 MPa or more, 1960 MPa or more.
  • the sintering temperature is lower than the liquidus temperature as described above and is relatively low. Therefore, the thermal energy can be reduced as compared with the case of sintering at a high temperature such that a liquid phase is generated. Further, as compared with the above-mentioned high-temperature sintering, it is less likely that the shape accuracy and the dimensional accuracy are lowered due to heat shrinkage. Therefore, it is easy to obtain a sintered material having excellent shape accuracy and dimensional accuracy, and the yield of the sintered material can be increased.
  • the method for manufacturing a sintered material which is to sinter a dense powder compact at a relatively low temperature, is a sintered material with few pores and small pores, and is also excellent in shape accuracy and dimensional accuracy. It can be said that the material can be manufactured with high productivity.
  • the sintering temperature and sintering time may be adjusted according to the composition of the raw material powder and the like.
  • the sintering temperature is 1000 ° C. or higher and lower than 1300 ° C.
  • the sintering temperature is preferably 1250 ° C. or lower, more preferably less than 1200 ° C.
  • the sintering temperature may be 1050 ° C. or higher, and further may be 1100 ° C. or higher.
  • the sintering temperature is, for example, 1100 ° C. or higher and lower than 1200 ° C.
  • the sintering time is, for example, 10 minutes or more and 150 minutes or less.
  • Examples of the atmosphere at the time of sintering include a nitrogen atmosphere and a vacuum atmosphere.
  • the pressure in the vacuum atmosphere is, for example, 10 Pa or less.
  • the oxygen concentration in the atmosphere is low, and the powder compact or the sintered material is difficult to oxidize.
  • the above-mentioned method for producing a sintered material may further include a step of performing a cutting process on the dust compact before sintering the dust compact.
  • the cutting process may be turning or rolling.
  • the powder compact before sintering is superior in cutting workability as compared with the sintered material and molten material after sintering.
  • a powder compact having a relative density of 93% or more is easier to perform cutting than a powder compact having a relative density of less than 93%.
  • the cutting process can be performed satisfactorily. Therefore, it is easy to obtain a sintered material having excellent shape accuracy and dimensional accuracy. In this respect, the yield tends to be high.
  • the cutting time is shortened due to the increase in the feed amount.
  • the dust compact when the dust compact is cut to obtain, for example, a final shape, the dust compact may be a simple shape such as a cylinder, a cylinder, or a rectangular parallelepiped.
  • a simple shape even if the molding pressure is low to some extent, a dense powder compact is easily molded with high accuracy. If the molding pressure is not too high, the life of the mold tends to be long. Moreover, if the shape is simple, the mold cost can be reduced. For these reasons, cutting the powder compact before the sintering process contributes to mass production of the sintered material.
  • the above-mentioned method for producing a sintered material may include a step of heat-treating the sintered material produced in the second step.
  • the heat treatment includes carburizing treatment and quenching tempering, carburizing quenching and tempering, and the like.
  • the heat treatment conditions may be appropriately adjusted according to the composition of the sintered material.
  • known conditions may be referred to.
  • the above-mentioned method for manufacturing a sintered material may include a step of finishing the sintered material after sintering.
  • the finishing process include polishing and the like.
  • the method for producing the sintered material of the embodiment has high relative density, few pores, and a sintered material having small pores in an arbitrary cross section, typically, the sintered material 1 of the above-described embodiment has high productivity. Can be manufactured.
  • the sintered material was prepared as follows. A powder compact is produced using the raw material powder. The obtained powder compact is sintered. After sintering, carburizing and quenching and tempering are performed in order.
  • the raw material powder is a mixed powder containing an alloy powder composed of the following iron-based alloys and carbon powder.
  • the iron-based alloy contains 2% by mass of Ni, 0.5% by mass of Mo, and 0.2% by mass of Mn, and the balance is composed of Fe and impurities.
  • the Vickers hardness Hv of this iron-based alloy is 120, which satisfies 80 or more and 200 or less.
  • the content of the carbon powder is 0.3% by mass, where the total mass of the mixed powder is 100% by mass.
  • the average particle size (D50) of the alloy powder is 100 ⁇ m.
  • the average particle size (D50) of the carbon powder is 5 ⁇ m.
  • the raw material powder was pressure molded to produce a columnar powder compact.
  • the size of the dust compact is 75 mm in outer diameter and 20 mm in thickness.
  • the molding pressure was selected from the range of 1560 MPa to 1960 MPa so that the relative density (%) of the powder compact of each sample was about 85% to 99%, and the powder compact was prepared.
  • the higher the molding pressure the higher the relative density of the powder compact.
  • Table 1 shows the density (g / cm 3 ) and relative density (%) of the powder compact of each sample.
  • the density of the dust compact (g / cm 3 ) was determined by measuring the mass of the dust compact and dividing this mass by the volume of the dust compact. The obtained density is the apparent density of the powder compact.
  • the relative density (%) of the dust compact was determined by dividing the apparent density of the dust compact by the true density of the dust compact, here 7.8 g / cm 3. The true density was determined from the composition of the raw material powder used.
  • the produced powder compact was sintered under the following conditions. After sintering, carburizing and quenching was performed under the following conditions, and then tempering was performed to obtain a sintered material for each sample.
  • the sintering temperature (° C.) is any one of 1130 ° C., 1450 ° C., and 1480 ° C. Table 1 shows the sintering temperatures of each sample.
  • the holding time is 20 minutes.
  • the atmosphere is a nitrogen atmosphere.
  • (Carburizing and quenching) 930 ° C x 90 minutes, Carbon potential: 1.4% by mass ⁇ 850 ° C x 30 minutes ⁇ Oil cooling (tempering) 200 ° C x 90 minutes
  • the matrix of this sintered material consists of the following iron-based alloys.
  • This iron-based alloy contains 2% by mass of Ni, 0.5% by mass of Mo, 0.2% by mass of Mn, and 0.3% by mass of C, and the balance is composed of Fe and impurities.
  • the component analysis of the sintered material was performed using ICP.
  • Sample No. 1 to No. 3 The sintered material of No. 3 is obtained by sintering a powder compact having a relative density of 93% or more at 1130 ° C., that is, below the liquidus temperature.
  • 2A to 2C show the sample Nos. 1 to No. 3 is an SEM image obtained by observing an arbitrary cross section of the sintered material of No. 3 with a scanning electron microscope (SEM).
  • the sintered material of 103 is a powder compact having a relative density of less than 93%, which is sintered at a liquid phase temperature of 1450 ° C. or 1480 ° C.
  • 8A to 8C show the sample Nos. 101-No. It is an SEM image which observed an arbitrary cross section by SEM about the sintered material of 103. In FIGS. 8A and 8B, the upper black area is the background.
  • the density of the sintered material was determined according to the Archimedes method. Specifically, the density is measured by measuring the mass of the sintered material in the air and the mass in pure water, and "(density of water x mass of the sintered material in the air) / (sintered material in the air). -Mass of sintered material in water) ".
  • the relative density (%) of the sintered material is determined as follows. Take multiple cross sections from the sintered material. Each cross section is observed with a microscope such as an SEM or an optical microscope. Image analysis is performed on this observation image, and the area ratio of the metal component is regarded as the relative density.
  • the region on each end face side of the sintered material and the vicinity of the center of the length along the axial direction of the sintered material Take a cross section from each of the regions.
  • the end face of the sintered material is a circular surface in this example.
  • the region on the end face side depends on the length of the sintered material and the thickness in this example, but for example, a region within 3 mm inward from the surface of the sintered material can be mentioned.
  • the region near the center depends on the length of the sintered material, and examples thereof include a region up to 1 mm from the center of the length toward each end face side, that is, a region having a total of 2 mm.
  • Examples of the cut surface include planes that intersect in the axial direction, and typically planes that are orthogonal to each other.
  • a plurality of observation fields for example, 10 or more are taken from each cross section.
  • Image processing such as binarization processing is performed on the observation image of each observation field of view, and a region made of metal is extracted from the processed image. Find the area of the region consisting of the extracted metal. Furthermore, the ratio of the area of the region made of metal to the area of the observation field of view is obtained. The ratio of this area is regarded as the relative density of each observation field. Average the relative densities of the obtained multiple observation fields. The obtained average value is defined as the relative density (%) of the sintered material.
  • 10 or more observation fields of view are taken from each of the two end face side regions.
  • 10 or more observation fields of view are taken from the region near the center. Then, the relative densities of each observation field of view are obtained, and the relative densities of 30 or more in total are averaged. This average value is taken as the relative density (%) of the sintered material and is shown in Table 1.
  • the relative density of the powder compact may be obtained in the same manner as the relative density of the sintered material.
  • the cross section of the powder compact is the region near the center of the length along the pressure axis direction in the powder compact, the pressure axis direction. It can be taken from the area on the end face side located at both ends of the. Examples of the cut surface include planes that intersect in the direction of the pressure axis, and typically planes that are orthogonal to each other.
  • the size of the pores is calculated as follows.
  • the sintered material of each sample has an arbitrary cross section.
  • the cross section is observed by SEM, and at least one field of view is taken from the cross section.
  • the size of the pores is measured by extracting a total of 50 or more pores.
  • the magnification is adjusted according to the size of the pores so that one or more pores are present in one visual field and the size of the pores can be measured accurately.
  • the cross section is observed with a magnification of 100 times, and if the maximum diameter of the pores is 70 ⁇ m or less, the magnification is changed to 300 times and the cross section is observed again. Increase the number of fields of view until a total of 50 or more pores are obtained.
  • the size of one field of view in 3 is about 355 ⁇ m ⁇ about 267 ⁇ m.
  • ⁇ Cross-sectional area> The cross-sectional area of each pore extracted from the above SEM image is obtained. Further, the average value of the cross-sectional areas of the pores is obtained. The average value of the cross-sectional areas is obtained by taking the total cross-sectional area of the extracted 50 or more pores and dividing the total by the number of pores. The average value of the cross-sectional areas is taken as the average cross-sectional area ( ⁇ m 2 ) and is shown in Table 1. Table 1 shows the number of pores (N number) used for measuring the cross-sectional area and the like.
  • ⁇ Maximum diameter> The maximum diameter of each pore extracted from the above SEM image is obtained. Furthermore, the average value of the maximum diameter is obtained. The average value of the maximum diameters is obtained by taking the sum of the maximum diameters of the extracted 50 or more pores and dividing the sum by the number of pores. Table 1 shows the average value ( ⁇ m) of the maximum diameter.
  • the maximum diameter of each pore is calculated as follows. In the above SEM image, the outer shape of each pore is sandwiched by two parallel lines, and the distance between these two parallel lines is measured. The interval is a distance in a direction orthogonal to the parallel lines. In each pore, a plurality of sets of parallel lines in arbitrary directions are taken, and the above intervals are measured respectively. In each pore, the maximum value among the plurality of measured intervals is defined as the maximum diameter of each pore.
  • the maximum and minimum values of the maximum diameter of the pores were also calculated.
  • the maximum value ( ⁇ m) is shown in Table 1.
  • Table 1 shows the minimum value ( ⁇ m) of the above-mentioned maximum diameters of 50 or more pores.
  • the roundness of the pores was determined as follows.
  • the peripheral length of each pore extracted from the above-mentioned SEM image and the peripheral length of a circle having an area equivalent to the cross-sectional area of each pore are obtained.
  • (Peripheral length of pores / Peripheral length of the above circle) is defined as the roundness of each pore.
  • Table 1 shows the average value of the roundness of the pores of 50 or more.
  • the tensile strength (MPa) of the sintered material of each sample was examined. The results are shown in Table 1.
  • the tensile strength was measured by conducting a tensile test using a general-purpose tensile tester.
  • the tensile test piece conforms to the standards of the Japan Powder Metallurgy Industry Association, JPMA M 04-1992, and the sintered metal material tensile test piece.
  • the test piece is a flat plate material cut out from a sintered material. This test piece is composed of a narrow portion and a wide portion provided at both ends of the narrow portion.
  • the narrow portion is composed of a central portion and a shoulder portion.
  • the shoulder portion has an arcuate side surface formed from the central portion to the wide portion.
  • the size of the test piece is shown below.
  • the scoring distance is 30 mm.
  • the width of the wide part is 8.7 mm
  • 3 to 7 show, in order, the average cross-sectional area of the pores ( ⁇ m 2 ), the average peripheral length of the pores ( ⁇ m), the average value of the maximum diameters of the pores ( ⁇ m), and the maximum diameter of the pores for the sintered material of each sample.
  • It is a graph which shows the maximum value ( ⁇ m) of, and the minimum value ( ⁇ m) of the maximum diameter of pores.
  • the horizontal axis of each graph indicates the sample number.
  • the vertical axis of each graph is the average cross-sectional area of the pores ( ⁇ m 2 ) in FIG. 3, the average peripheral length of the pores ( ⁇ m) in FIG. 4, the average value of the maximum diameters of the pores ( ⁇ m) in FIG. 6, and the pores in FIG.
  • the maximum value ( ⁇ m) of the maximum diameter of the pores is shown, and FIG. 7 shows the minimum value ( ⁇ m) of the maximum diameter of the pores.
  • sample No. 1 to No. In the sintered material of No. 3, the sample No. It can be seen that the average cross-sectional area of the pores is smaller than that of the sintered materials of 101 to 103.
  • sample No. 1 to No. The sintered material of No. 3 is called a high-density molded sample.
  • Sample No. The sintered materials 101 to 103 are called high temperature sintered samples.
  • the average cross-sectional area of the pores is not more 500 [mu] m 2 or less, where in particular 450 [mu] m 2 or less.
  • No. in the sintered material of 3 the average cross-sectional area of the pores is 400 ⁇ m 2 or less, particularly 300 ⁇ m 2 or less, which is smaller.
  • the average peripheral length of the pores of the high-density molded sample is shorter than that of the high-temperature sintered sample.
  • the average peripheral length of the pores is 100 ⁇ m or less, in particular 70 ⁇ m or less.
  • the relative density of the sintered material is 93% or more, and as shown in Tables 1 and 8A to 8C, each pore 11 has a large cross-sectional area and a long peripheral length.
  • the powder compact of the high-temperature sintered sample has a small relative density as compared with the high-density molded sample, and therefore contains many pores.
  • the pores are easily discharged to some extent, but due to the combination of a plurality of bubbles inside, large pores are formed as shown in FIGS. 8A to 8C. Easy to remain. That is, pores having a large cross-sectional area and a long peripheral length tend to remain.
  • the high-density molded sample has higher tensile strength and superior strength as compared with the high-temperature sintered sample.
  • the sample No. with the highest tensile strength.
  • the high-density molded sample has an improved tensile strength of 15% or more. It is considered that the reason for this is that in the high-density molded sample, the pores were so small that the pores were unlikely to be the starting point of cracking.
  • the average value of the maximum pore diameters of the high-density molded sample is smaller than that of the high-temperature sintered sample. Quantitatively, the average value of the maximum diameter in the high-density molded sample is 30 ⁇ m or less, and here, in particular, 20 ⁇ m or less. The average value of the maximum diameter of the high-density molded sample is 5 ⁇ m or more, and here, particularly 10 ⁇ m or more. Although such pores are small, it can be said that they are not too small.
  • the maximum value and the minimum value of the maximum diameter of the pores of the high-density molded sample are smaller than those of the high-temperature sintered sample.
  • the maximum value of the maximum diameter in the high-density molded sample is 30 ⁇ m or less, and here, in particular, 25 ⁇ m or less.
  • the difference between the average value and the maximum value is smaller in the above-mentioned maximum diameter in the high-density molded sample than in the high-temperature sintered sample. Therefore, it can be said that the maximum diameter of the high-density molded sample has a uniform size.
  • the minimum value of the maximum diameter in a high-density molded sample is 20 ⁇ m or less, and here, particularly 5 ⁇ m or more and 15 ⁇ m or less. From this, it can be said that the pores of the high-density molded sample are small, but not too small.
  • the high-density molded sample has a smaller roundness than the high-temperature sintered sample. Quantitatively, the roundness of the high-density molded sample is 3.4 or less, and here it is 3.3 or less.
  • the sintered material having a relative density of 93% or more and 99.5% or less and having small pores is a powder compact having a relative density of 93% or more and 99.5% or less and lower than the liquidus temperature. It was shown that it can be manufactured by sintering at a relatively low temperature. Further, it was shown that the above-mentioned dense powder compact can be obtained by using a powder made of an iron-based alloy having a Vickers hardness Hv of 80 or more and 200 or less.
  • the sintered material having a relative density of 93% or more and 99.5% or less and having small pores is less likely to cause cracks in the pores and is excellent in strength. Therefore, it is expected that the sintered material can be suitably used for various parts and the like that require high strength. Further, if at least one pore is an open pore, good durability and good quietness can be expected by holding the lubricant. Therefore, it is expected that the sintered material can be suitably used for sliding members such as gears for which lubricity is desired and parts for which quietness is desired.
  • the composition of the sintered material and the production conditions may be changed.
  • the composition of the sintered material may be other than, for example, an iron-based material.
  • Regarding the production conditions for example, changing the relative density of the powder compact, the sintering temperature, and the like can be mentioned.

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JP2015004098A (ja) * 2013-06-20 2015-01-08 株式会社豊田中央研究所 鉄基焼結材およびその製造方法
WO2017175772A1 (ja) * 2016-04-07 2017-10-12 住友電気工業株式会社 焼結体の製造方法、および焼結体
WO2019021935A1 (ja) * 2017-07-26 2019-01-31 住友電気工業株式会社 焼結部材
JP2019019362A (ja) * 2017-07-13 2019-02-07 住友電気工業株式会社 焼結部材、及び焼結部材の製造方法

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JP2007533857A (ja) * 2004-04-21 2007-11-22 ホガナス アクチボラゲット 焼結金属部品及びその製造方法
JP2015004098A (ja) * 2013-06-20 2015-01-08 株式会社豊田中央研究所 鉄基焼結材およびその製造方法
WO2017175772A1 (ja) * 2016-04-07 2017-10-12 住友電気工業株式会社 焼結体の製造方法、および焼結体
JP2019019362A (ja) * 2017-07-13 2019-02-07 住友電気工業株式会社 焼結部材、及び焼結部材の製造方法
WO2019021935A1 (ja) * 2017-07-26 2019-01-31 住友電気工業株式会社 焼結部材

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