Classifications

• • 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
  • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
• • 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
  • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
  • B22F1/09—Mixtures of metallic powders
• • 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
• • 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
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C1/00—Making non-ferrous alloys
  • C22C1/04—Making non-ferrous alloys by powder metallurgy
  • C22C1/05—Mixtures of metal powder with non-metallic powder
  • C22C1/059—Making alloys comprising less than 5% by weight of dispersed reinforcing phases
• • 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
  • C22C33/0207—Using a mixture of prealloyed powders or a master alloy
• • 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
• • 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
  • 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
  • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
• • 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
  • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
• • 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
  • B22F2301/10—Copper
• • 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
  • B22F2301/20—Refractory metals
• • 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

Definitions

• This disclosure relates to an alloyed steel powder for powder metallurgy, an iron-based mixed powder for powder metallurgy, and a sintered body.
• Powder metallurgical techniques enable producing parts with complicated shapes in shapes that are extremely close to product shapes (so-called near net shapes) with high dimensional accuracy, and consequently significantly reducing machining costs during the production of parts. Therefore, powder metallurgical products are widely used as all kinds of parts for machines. Further, to cope with demands for reductions in size and weight and increasing complexity of parts, requirements for powder metallurgical techniques are becoming more stringent.
• alloyed steel powders used in powder metallurgy are also becoming more stringent, and it is required that the alloyed steel powders have good compressibility and sintered bodies obtained by sintering the alloyed steel powders have excellent mechanical properties. Further, a reduction in production costs is strongly required. From such a viewpoint, it is desired that the alloyed steel powders can be produced by conventional metallurgical powder production processes without any additional step, and that the alloyed steel powders do not need to contain any expensive alloy component such as Ni.
• the following methods have been proposed to improve the strength of a sintered body: a method of mixing a steel powder with a specific metal powder to obtain a mixed powder, a method of diffusionally adhering a specific metal powder to the surface of a steel powder, a method of further combining with graphite powder, and a method of using an alloyed steel powder that has been alloyed with a specific metal element.
• JP2012520942A (PTL 1) proposes a steel powder alloyed with V and Mn, which may be mixed with Cu and Ni powders.
• WO2016092827A proposes an alloyed steel powder for powder metallurgy in which a Cu powder is diffusionally adhered to the surface of a steel powder alloyed with Cu.
• JP2003500538A proposes a mixed powder for powder metallurgy in which a steel powder alloyed with Mo is mixed with either or both of a Cu powder and a Ni powder.
• JP2010529302A (PTL 4) proposes an alloyed steel powder alloyed with Ni, Mo and Mn.
• JP2013508558A proposes a method of binding graphite powder to an iron-based powder by a binder, where the iron-based powder may be alloyed with alloying elements such as Ni, Cr, Mo and Mn.
• JP2013204112A (PTL 6) proposes a method of combining alloying elements such as Cr, Mo and Cu with a reduced amount of C.
• PTL 6 only improves the compressibility of a mixed powder by reducing the amount of C (graphite powder or the like) to be mixed with an alloyed steel powder, which cannot improve the compressibility of the alloyed steel powder itself. Further, it is necessary to set the cooling rate in quenching after sintering to 2 °C/s or higher to ensure the hardness and tensile strength of a sintered body. To control the cooling rate as above, it is necessary to modify production apparatus, which increases production costs.
• the compressibility refers to the density (compressed density) of a formed body obtained by performing pressing at a given pressure, and the value is preferably as high as possible.
• an alloyed steel powder using Cu, Mo, and at least one of V, Nb and Ti, each in a specific amount, as alloying elements has excellent compressibility and can be used to provide a sintered body that obtains improved strength simply by sintering, thereby completing the present disclosure.
• the alloyed steel powder of the present disclosure can uniformize the distribution of Cu and Mo, which in turn can uniformize the distribution of Cu and Mo in the sintered body.
• at least one of V, Nb and Ti is contained, precipitates in the sintered body are refined, and consequently, the microstructure can be refined. It is presumed that all these factors can lead to a sintered body with improved strength.
• the alloyed steel powder for powder metallurgy of the present disclosure has excellent compressibility and can be used to provide a sintered body that obtains improved strength simply by sintering.
• the alloyed steel powder for powder metallurgy of the present disclosure is advantageous in that it does not contain alloying elements that are easily oxidized, such as Cr and Mn, and thus does not cause a decrease in strength of a sintered body due to oxidation of alloying elements.
• the alloyed steel powder for powder metallurgy of the present disclosure does not contain elements such as Ni, which causes a high alloy cost, or Cr, which requires annealing in a special atmosphere, and it does not require additional production processes such as coating or plating. Therefore, it is advantageous in terms of cost and is also convenient in that it can be produced by conventional metallurgical powder production processes.
• the iron-based mixed powder for powder metallurgy of the present disclosure also has excellent compressibility and can be used to provide a sintered body that obtains improved strength simply by sintering.
• the alloyed steel powder for powder metallurgy or the iron-based mixed powder for powder metallurgy of the present disclosure it is possible to produce a sintered body with improved strength at a low cost.
• the alloyed steel powder for powder metallurgy of the present disclosure (hereinafter also referred to as “alloyed steel powder”) contains iron-based alloy in which Cu, Mo, and at least one of V, Nb and Ti are contained as essential components.
• the "iron-based” means containing 50 mass% or more of Fe.
• “%” denotes “mass%” unless otherwise noted.
• the content of the chemical composition of the alloyed steel powder for powder metallurgy is an amount with respect to 100 mass% of the alloyed steel powder for powder metallurgy.
• Cu is an element that improves hardenability, and Cu is superior to elements such as Si, Cr and Mn in that it is more resistant to oxidation. Cu is also advantageous in that it is cheaper than Ni.
• the Cu content is set to 1.0 % or more.
• sintering is generally performed at about 1130 °C during the production of sintered bodies. According to the Fe-Cu phase diagram, when the Cu content exceeds 8.0 %, Cu precipitates in the austenite phase. The Cu precipitates formed during sintering do not function effectively to improve hardenability, but rather remain as a soft phase in the microstructure, which may lead to deterioration of mechanical properties.
• the Cu content is set to 8.0 % or less.
• the Cu content is preferably 2.0 % or more.
• the Cu content is preferably 6.0 % or less.
• Mo is an element that improves hardenability, and Mo is superior to elements such as Si, Cr and Mn in that it is more resistant to oxidation. Further, Mo has a characteristic that a small amount of addition, which is less than that of Ni, is sufficient for obtaining an effect of improving hardenability.
• Mo content is 0.50 % or less, the strength-improving effect of Mo is insufficient. Therefore, the Mo content is set to more than 0.50 %.
• the Mo content exceeds 2.00 %, the compressibility of the alloyed steel powder decreases, and a die for pressing is easily worn out.
• the Mo content is set to 2.00 % or less.
• the Mo content is preferably 1.00 % or more.
• the Mo content is preferably 1.50 % or less.
• the alloyed steel powder of the present disclosure contains at least one of V, Nb and Ti.
• the alloyed steel powder may contain only one of V, Nb and Ti, two of them, or all three of them. When two of them are contained, it may be any combination of V and Nb, V and Ti, or Nb and Ti.
• the content of each of V, Nb and Ti is as follows.
• V 0.05 % or more and 0.50 % or less
• V is an element that acts extremely effectively to improve strength by precipitating as carbides in a solid portion of a sintered body.
• the V content is set to 0.05 % or more.
• the V content exceeds 0.50 %, the carbides are coarsened, which deteriorates the strength-improving effect, and each particle of the alloyed steel powder is hardened, which causes a decrease in compressibility. Further, it also is disadvantageous from an economic viewpoint. Therefore, the V content is set to 0.50 % or less. To effectively obtain a higher strength, the V content is preferably 0.10 % or more. The V content is preferably 0.40 % or less.
• Nb 0.02 % or more and 0.40 % or less
• Nb is an element that not only greatly enhances hardenability but also acts effectively to improve strength by precipitating as carbides in a solid portion of a sintered body.
• the Nb content is set to 0.02 % or more.
• the Nb content exceeds 0.40 %, the carbides are coarsened, which deteriorates the strength-improving effect, and each particle of the alloyed steel powder is hardened, which causes a decrease in compressibility. Further, it also is disadvantageous from an economic viewpoint.
• the Nb content is set to 0.40 % or less.
• the Nb content is preferably 0.05 % or more to effectively obtain a higher strength.
• the Nb content is preferably 0.20 % or less to effectively obtain a higher strength.
• Ti is an element that acts effectively to improve strength by precipitating as carbides in a solid portion of a sintered body.
• the Ti content is set to 0.02 % or more.
• the Ti content exceeds 0.40 %, the carbides are coarsened, which deteriorates the strength-improving effect, and each particle of the alloyed steel powder is hardened, which causes a decrease in compressibility. Further, it also is disadvantageous from an economic viewpoint. Therefore, when Ti is contained, the Ti content is set to 0.40 % or less.
• the Ti content is preferably 0.05 % or more to effectively obtain a higher strength.
• the Ti content is preferably 0.20 % or less to effectively obtain a higher strength.
• the balance of the alloyed steel powder other than the aforementioned components consists of Fe and inevitable impurities.
• the amount of inevitable impurities is not particularly limited as long as it is an amount inevitably mixed in. However, it is preferable to control inevitable impurities so that they are substantially not contained. Because Ni causes an increase in alloy costs, it is preferable to control the Ni content to 0.1 % or less. Because Cr is easily oxidized and it requires control of annealing atmosphere, it is preferable to control the Cr content to 0.1 % or less. For the same reason as for Cr, it is preferable to control the Si content to 0.1 % or less.
• C 0.01 % or less, O to 0.20 % or less, Mn to 0.15 % or less, P to 0.025 % or less, S to 0.025 % or less, N to 0.05 % or less, and other elements to 0.01 % or less.
• the alloyed steel powder of the present disclosure includes the following embodiments.
• the method of producing the alloyed steel powder is not particularly limited, and the alloyed steel powder may be produced with any method.
• the alloyed steel powder may be an atomized powder produced with an atomizing method, and it is preferably a water atomized powder produced with a water atomizing method, which causes low production costs and is easy for mass production.
• the alloyed steel powder can be obtained by, for example, atomizing molten steel, which has been adjusted to have the predetermined chemical composition, to obtain a powder, and reducing and/or classifying the powder as necessary.
• the particle size of the alloyed steel powder is not particularly limited, and the alloyed steel powder may have any particle size. From the viewpoint of ease of production, it is preferable to have an average particle size of 30 ⁇ m or more and 150 ⁇ m or less. An alloyed steel powder having an average particle size within the above range can be produced industrially at low costs with a water atomizing method. As used here, the average particle size refers to the mass-based median size (D50). The average particle size can be determined by interpolation as a particle size for which a value of 50 % is reached when calculating the mass-based cumulative particle size distribution from particle size distribution measured with the dry sieving method described in JIS Z 2510.
• the alloyed steel powder can be used for powder metallurgy as it is, or it can be used as an iron-based mixed powder for powder metallurgy containing the alloyed steel powder and a metal powder (hereinafter also referred to as "mixed powder").
• the metal powder in the mixed powder of the present disclosure is either or both of a Cu powder: more than 0 % and 4 % or less, and a Mo powder: more than 0 % and 4 % or less.
• the content of the chemical composition of the iron-based mixed powder for powder metallurgy is an amount with respect to 100 mass% of the iron-based mixed powder for powder metallurgy.
• Cu powder more than 0 % and 4 % or less
• a Cu powder can be added to the alloyed steel powder to promote sintering and improve strength. However, when it exceeds 4 %, the amount of liquid phase formed during sintering increases, which decreases the density of a sintered body due to expansion and deteriorates the strength. Therefore, the amount of Cu powder added is set to 4 % or less. When a Cu powder is added, it is preferably 0.5 % or more to effectively improve the strength.
• Mo powder more than 0 % and 4 % or less
• a Mo powder can be added to the alloyed steel powder to promote sintering and improve strength. However, when it exceeds 4 %, the alloyed steel powder is hardened, which decreases the compressive density and deteriorates the strength. Therefore, the amount of Mo powder added is set to 4 % or less. When a Mo powder is added, it is preferably 0.5 % or more to effectively improve the strength.
• the method of producing the mixed powder is not particularly limited, and the mixed powder may be produced with any method.
• it can be produced by mixing either or both of the Cu and Mo powders of the contents described above with the alloyed steel powder.
• the mixing can be performed with any method. Examples thereof include methods of mixing using a V-shaped mixer, a double cone mixer, a Henschel Mixer, or a Nauta Mixer.
• a binder such as a machine oil may be added to prevent segregation of either or both of the Cu and Mo powders.
• the mixed powder may be obtained by filling the alloyed steel powder, and either or both of the Cu and Mo powders of the contents described above in a mold for pressing.
• the present disclosure also relates to a sintered body obtained by sintering a formed body containing the alloyed steel powder or the mixed powder.
• the sintered body may be produced using the alloyed steel powder or the mixed powder (hereinafter also referred to as "raw material") as a raw material.
• raw material the mixed powder
• the method of producing the sintered body is not particularly limited, and the sintered body may be produced with any production method.
• the sintered body can be produced by adding any optional component as required to the raw material, and subjecting them to pressing and then sintering.
• the raw material of the sintered body may be the raw material as it is, or may also include an auxiliary raw material such as a carbon powder.
• the carbon powder is not particularly limited and is preferably graphite powder (natural graphite powder, artificial graphite powder, etc.) or carbon black.
• the addition of carbon powder can further improve the strength of the sintered body.
• the carbon powder is preferably 0.2 parts by mass or more with respect to 100 parts by mass of the raw material in terms of the strength-improving effect.
• the carbon powder is preferably 1.2 parts by mass or less with respect to 100 parts by mass of the raw material.
• a lubricant may be added to the raw material. Containing a lubricant facilitates the extraction of a formed body from a press mold.
• the lubricant is not particularly limited, and examples thereof include metal soap (zinc stearate, lithium stearate, etc.) and amide-based wax (ethylene bis-stearate amide, etc.).
• the lubricant is preferably in powder form. When a lubricant is used, the lubricant is preferably 0.3 parts by mass or more with respect to 100 parts by mass of the raw material.
• the lubricant is preferably 1.0 part by mass or less with respect to 100 parts by mass of the raw material.
• a machinability-improving powder may be added to the raw material.
• the machinability-improving powder is not particularly limited, and examples thereof includes a MnS powder and an oxide powder.
• the machinability-improving powder is preferably 0.1 parts by mass or more with respect to 100 parts by mass of the raw material.
• the machinability-improving powder is preferably 0.7 parts by mass or less with respect to 100 parts by mass of the raw material.
• the raw material is blended with optional components such as an auxiliary raw material, a lubricant, and a machinability-improving powder as required and then subjected to pressing to obtain a formed body in a desired shape.
• the method of pressing is not particularly limited, and any method may be used. Examples thereof include a method of filling a press mold with the raw material and the like and performing pressing.
• a lubricant may be applied or adhered to the press mold.
• the amount of the lubricant is preferably 0.3 parts by mass or more with respect to 100 parts by mass of the raw material.
• the amount of the lubricant is preferably 1.0 part by mass or less with respect to 100 parts by mass of the raw material.
• the pressure at which pressing is performed to obtain a formed body may be set to 400 MPa or more and 1000 MPa or less. Within this range, the density of the formed body is lowered, the density of the sintered body is reduced, an insufficient strength can be avoided, and burden on the press mold can also be suppressed.
• the raw material of the present disclosure can be pressed under a pressure of 588 MPa to obtain a formed body with a density (compressed density) of 6.75 Mg/m 3 or more, for example.
• the density (compressed density) of the formed body is preferably 6.80 Mg/m 3 or more.
• the resulting formed body is then sintered.
• the method of sintering is not particularly limited and can be any method.
• the sintering temperature may be 1100 °C or higher and is preferably 1120 °C or higher from the viewpoint of performing sintering sufficiently.
• the distribution of Cu and Mo becomes uniform in the sintered body as the sintering temperature increases, so that the upper limit of the sintering temperature is not particularly limited.
• the sintering temperature is preferably 1250 °C or lower and more preferably 1180 °C or lower from the viewpoint of controlling the production costs.
• the raw material is an alloyed steel powder obtained by alloying Cu, Mo and at least one of V, Nb and Ti
• the distribution of Cu and Mo can be made uniform even at a sintering temperature within the above range.
• the strength of the sintered body can be effectively improved.
• the sintering time may be 15 minutes or longer and 50 minutes or shorter. Within this range, insufficient sintering and insufficient strength can be avoided, and the production costs can be suppressed.
• the cooling rate during cooling after sintering may be 20 °C/min or higher and 40 °C/min or lower. At a cooling rate of lower than 20 °C/min, quenching cannot be performed sufficiently, and the tensile strength may be reduced.
• a cooling rate of 40 °C/min or higher requires ancillary equipment to accelerate the cooling rate, which increases the production costs.
• a degreasing process may be added in which the formed body is held in a temperature range of 400 °C or higher and 700 °C or lower for a certain period of time to decompose and remove the lubricant before sintering.
• the conditions and equipment for the production of the sintered body other than the above are not particularly limited and may be any commonly known ones, for example.
• the resulting sintered body may be subjected to treatment such as carburizing-quenching and tempering.
• Alloyed steel powders and sintered bodies using the alloyed steel powders were produced by the following procedures in the examples.
• Molten steels were adjusted to have the chemical compositions listed in Table 1 to Table 4, and alloyed steel powders were prepared with a water atomizing method.
• the amounts of Si, Mn, P, S and Cr contained in the alloyed steel powder as inevitable impurities were as follows: Si: less than 0.05 mass%, Mn: less than 0.15 mass%, P: less than 0.025 mass%, S: less than 0.025 mass%, and Cr: less than 0.03 mass%.
• Each of the resulting alloyed steel powder was held at 920 °C in a hydrogen atmosphere for 30 minutes for finish-reduction. After finish-reduction, a heat-treated body, in which particles were sintered together to form a lump, was ground using a hammer mill and classified using a sieve with a mesh size of 180 ⁇ m, and the powder under the sieve was collected and used as an alloyed steel powder.
• the amounts of C, O and N contained in the alloyed steel powder as inevitable impurities were as follows: C: less than 0.01 mass%, O: less than 0.20 mass%, and N: less than 0.05 mass%.
• the chemical composition of the alloyed steel powder was equivalent to the chemical composition of the molten steel above.
• a Cu powder (D50 of about 30 ⁇ m) or an oxidized Mo powder (D50 of about 3 ⁇ m) was added to the alloyed steel powder in such an amount that the content of Cu or Mo in a diffusionally adhered alloy steel powder was the value listed in Table 1 to Table 3, and the powders were mixed in a V-shaped mixer for 15 minutes and then held at 920 °C in a hydrogen atmosphere for 30 minutes for finish-reduction. After finish-reduction, a reduced body, in which particles were sintered together to form a lump, was ground using a hammer mill and classified using a sieve with a mesh size of 180 ⁇ m, and the powder under the sieve was collected and used as a diffusionally adhered alloy steel powder to which Cu or Mo was diffusionally adhered.
• the amounts of C, O and N contained in the diffusionally adhered alloy steel powder as inevitable impurities were as follows: C: less than 0.01 mass%, O: less than 0.20 mass%, and N: less than 0.05 mass%.
• the alloyed steel powder or diffusionally adhered alloy steel powder was added with 0.8 parts by mass of graphite powder, 0.6 parts by mass of a lubricant (zinc stearate), and a Cu powder (D50 of about 45 ⁇ m) or a Mo powder (D50 of about 25 ⁇ m) in an amount listed in Tables 1 to 3 or 5 with respect to 100 parts by mass of the alloyed steel powder or diffusionally adhered alloy steel powder, and the powders were mixed using a double-cone mixer to obtain an iron-based mixed powder.
• the iron-based mixed powder was pressed into a rectangular shape of 10 mm ⁇ 10 mm ⁇ 55 mm at a pressing pressure of 588 MPa to obtain a formed body.
• the density of the formed body was calculated by dividing the weight of the formed body by the volume of the rectangular body.
• the formed body was held at 1130 °C for 20 minutes in a 10 % H 2 -90 % N 2 atmosphere to obtain a sintered body.
• a test piece having a length of 50 mm and a diameter of 3 mm was cut out from the sintered body, and the maximum stress before breaking (tensile strength) was measured.
• Iron-based powders prepared under the following four sets of conditions were also evaluated as comparative examples.
• Cu was diffusively adhered to the surface of an alloyed steel powder containing Mo and V as alloying elements, and the alloyed steel powder was mixed with graphite powder and a lubricant.
• an alloyed steel powder containing Mo and V as alloying elements was mixed with a Cu powder, graphite powder and a lubricant.
• Mo was diffusively adhered to the surface of an alloyed steel powder containing Cu and V as alloying elements, and the alloyed steel powder was mixed with graphite powder and a lubricant.
• No. 1-13 an alloyed steel powder containing Cu and V as alloying elements was mixed with a Mo powder, graphite powder and a lubricant. Table 1 lists the amount adhered, the amount added and the evaluation results.
• the tensile strength was significantly improved in No.1-2 containing Cu, Mo and V as compared to No.1-1 containing only Cu and V.
• the tensile strength of No. 1-3 in which no V was added and Cu was increased, was not as high as that of No. 1-2.
• the tensile strength was significantly improved in No. 1-6 containing Cu, Mo and V as compared to No. 1-4 containing only Cu and V and No. 1-5 containing only Mo and V.
• a high tensile strength was obtained in No. 1-7 with increased Cu, No.1-8 with increased Mo, and No. 1-9 with increased V.
• Nos. 1-2 and 1-6 to 1-9 which are disclosed examples, all have a sufficiently high density and excellent compressibility. It can be seen from the results of Nos. 1-5 to 1-7 that Cu can improve the tensile strength by increasing the amount added while maintaining a high density.
• the sintered body of No. 1-10 using a diffusionally adhered alloy steel powder, in which Cu was diffusively adhered to the surface of an alloyed steel powder containing Mo and V as alloying elements, and the sintered body of No. 1-11 using a mixed powder obtained by mixing the same alloyed steel powder with a Cu powder were inferior to the sintered body of No. 1-6 in terms of tensile strength, although they had the same contents of Cu, Mo and V.
• Iron-based powders prepared under the following four sets of conditions were also evaluated as comparative examples.
• Cu was diffusively adhered to the surface of an alloyed steel powder containing Mo and Nb as alloying elements, and the alloyed steel powder was mixed with graphite powder and a lubricant.
• an alloyed steel powder containing Mo and Nb as alloying elements was mixed with a Cu powder, graphite powder and a lubricant.
• Mo was diffusively adhered to the surface of an alloyed steel powder containing Cu and Nb as alloying elements, and the alloyed steel powder was mixed with graphite powder and a lubricant.
• an alloyed steel powder containing Cu and Nb as alloying elements was mixed with a Mo powder, graphite powder and a lubricant. Table 2 lists the amount adhered, the amount added and the evaluation results.
• the tensile strength was significantly improved in No. 2-2 containing Cu, Mo and Nb as compared to No. 2-1 containing only Cu and Nb.
• the tensile strength of No. 2-3 in which no Nb was added and Cu was increased, was not as high as that of No. 2-2.
• the tensile strength was significantly improved in No. 2-6 containing Cu, Mo and Nb as compared to No. 2-4 containing only Cu and Nb and No. 2-5 containing only Mo and Nb.
• No. 2-6 a high tensile strength was obtained in No. 2-7 with increased Cu, No. 2-8 with increased Mo, and No. 2-9 with increased Nb.
• No. 2-10 in which the amounts of Cu, Mo and Nb were outside the range of the present disclosure, had a lowered density and a deteriorated tensile strength.
• Nos. 2-2 and 2-6 to 2-9 which are disclosed examples, all have a sufficiently high density and excellent compressibility. It can be seen from the results of Nos. 2-5 to 2-7 that Cu can improve the tensile strength by increasing the amount added while maintaining a high density.
• the sintered body of No. 2-11 using a diffusionally adhered alloy steel powder, in which Cu was diffusively adhered to the surface of an alloyed steel powder containing Mo and Nb as alloying elements, and the sintered body of No. 2-12 using a mixed powder obtained by mixing the same alloyed steel powder with a Cu powder were inferior to the sintered body of No. 2-6 in terms of tensile strength, although they had the same contents of Cu, Mo and Nb.
• Iron-based powders prepared under the following four sets of conditions were also evaluated as comparative examples.
• Cu was diffusively adhered to the surface of an alloyed steel powder containing Mo and Ti as alloying elements, and the alloyed steel powder was mixed with graphite powder and a lubricant.
• an alloyed steel powder containing Mo and Ti as alloying elements was mixed with a Cu powder, graphite powder and a lubricant.
• Mo was diffusively adhered to the surface of an alloyed steel powder containing Cu and Ti as alloying elements, and the alloyed steel powder was mixed with graphite powder and a lubricant.
• an alloyed steel powder containing Cu and Ti as alloying elements was mixed with a Mo powder, graphite powder and a lubricant. Table 1 lists the amount adhered, the amount added and the evaluation results.
• the tensile strength was significantly improved in No. 3-2 containing Cu, Mo and Ti as compared to No. 3-1 containing only Cu and Ti.
• the tensile strength of No. 3-3 in which no Ti was added and Cu was increased, was not as high as that of No. 3-2.
• the tensile strength was significantly improved in No. 3-6 containing Cu, Mo and Ti as compared to No. 3-4 containing only Cu and Ti and No. 3-5 containing only Mo and Ti.
• No. 3-6 a high tensile strength was obtained in No. 3-7 with increased Cu, No. 3-8 with increased Mo, and No. 3-9 with increased Ti.
• No. 3-10 in which the amounts of Cu, Mo and Ti were outside the range of the present disclosure, had a lowered density and a deteriorated tensile strength.
• Nos. 3-2 and 3-6 to 3-9 which are disclosed examples, all have a sufficiently high density and excellent compressibility. It can be seen from the results of Nos. 3-5 to 3-7 that Cu can improve the tensile strength by increasing the amount added while maintaining a high density.
• the sintered body of No. 3-11 using a diffusionally adhered alloy steel powder, in which Cu was diffusively adhered to the surface of an alloyed steel powder containing Mo and Ti as alloying elements, and the sintered body of No. 3-12 using a mixed powder obtained by mixing the same alloyed steel powder with a Cu powder were inferior to the sintered body of No. 3-6 in terms of tensile strength, although they had the same contents of Cu, Mo and Ti.
• Table 5 lists the amounts of the alloyed steel powder, Cu powder and Mo powder added, as well as the evaluation results.

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• 2020
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