ALLOY STEEL POWDER FOR POWDER METALLURGY, AND SINTERED BODY

Abstract

An Fe—Mo—Cu—C-based alloy steel powder for powder metallurgy has a chemical composition containing Mo: 0.2 mass % to 1.5 mass %, Cu: 0.5 mass % to 4.0 mass %, and C: 0.1 mass % to 1.0 mass %, with a balance being Fe and incidental impurities, wherein an iron-based powder has a mean particle size of 30 μm to 120 μm, and a Cu powder has a mean particle size of 25 μm or less. Despite the alloy steel powder for powder metallurgy having a chemical composition not containing Ni, a part produced by sintering a press formed part of the powder and further carburizing-quenching-tempering the sintered part has mechanical properties of at least as high tensile strength, toughness, and sintered density as a Ni-added part.

Claims

1. An Fe—Mo—Cu—C-based alloy steel powder for powder metallurgy, comprising: a partial diffusion alloy steel powder obtained by diffusionally adhering Mo to an iron-based powder; a Cu powder; and a graphite powder, wherein the alloy steel powder for powder metallurgy has a chemical composition containing Mo: 0.2 mass % to 1.5 mass %, Cu: 0.5 mass % to 4.0 mass %, and C: 0.1 mass % to 1.0 mass %, with a balance being Fe and incidental impurities, and the iron-based powder has a mean particle size of 30 μm to 120 μm, and the Cu powder has a mean particle size of 25 μm or less.

2. An Fe—Mo—Cu—C-based alloy steel powder for powder metallurgy, comprising: a partial diffusion alloy steel powder obtained by diffusionally adhering Mo to an iron-based powder; a Cu powder; and a graphite powder, wherein the alloy steel powder for powder metallurgy has a chemical composition containing Mo: 0.2 mass % to 1.5 mass %, Cu: 0.5 mass % to 4.0 mass %, and C: 0.1 mass % to 1.0 mass %, with a balance being Fe and incidental impurities, and the iron-based powder has a mean particle size of 30 μm to 120 μm, and the Cu powder has a flat shape and satisfies a relation L≦−2d+50 where d is a thickness of the Cu powder in μm and L is a diameter in a major axis of the Cu powder in μm.

3. An Fe—Mo—Cu—C-based alloy steel powder for powder metallurgy, comprising: a partial diffusion alloy steel powder obtained by diffusionally adhering Mo to an iron-based powder; a Cu powder; and a graphite powder, wherein the alloy steel powder for powder metallurgy has a chemical composition containing Mo: 0.2 mass % to 1.5 mass %, Cu: 0.5 mass % to 4.0 mass %, and C: 0.1 mass % to 1.0 mass %, with a balance being Fe and incidental impurities, and the iron-based powder has a mean particle size of 30 μm to 120 μm, and the Cu powder is a mixed powder of a Cu powder having a mean particle size of 25 μm or less and a Cu powder having a flat shape and satisfying a relation L≦−2d+50 where d is a thickness of the Cu powder in μm and L is diameter in a major axis of the Cu powder in μm.

4. A sintered body produced using the alloy steel powder for powder metallurgy according to claim 1 as a material.

5. A sintered body produced using the alloy steel powder for powder metallurgy according to claim 2 as a material.

6. A sintered body produced using the alloy steel powder for powder metallurgy according to claim 3 as a material.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0049] In the accompanying drawings:

[0050] FIG. 1 is a diagram schematically illustrating a flat Cu powder according to one of the disclosed embodiments.

DETAILED DESCRIPTION

[0051] One of the disclosed embodiments is described in detail below.

[0052] A Fe—Mo—Cu—C-based alloy steel powder for powder metallurgy according to the embodiment is an alloy steel powder for powder metallurgy obtained by mixing a partial diffusion alloy steel powder (hereafter also referred to as “partial alloy steel powder”) formed by diffusionally adhering a Mo-containing powder to the surface of an iron-based powder having an appropriate mean particle size, with an appropriate amount of a Cu powder having a predetermined shape such as the below-mentioned mean particle size range and a graphite powder.

[0053] A sintered body according to the embodiment is produced by subjecting the alloy steel powder for powder metallurgy to conventional press forming to obtain a green compact and further subjecting the green compact to conventional sintering.

[0054] With the alloy steel powder for powder metallurgy according to the embodiment, a Mo-concentrated portion is formed in a sintered neck part between the particles of the iron-based powder of the green compact, thus facilitating sintering. Moreover, Cu expansion in the sintering is reduced, so that the sintered body density increases.

[0055] If the sintered body density increases, both the strength and toughness of the sintered body increase. Unlike a conventional sintered body produced using Ni, the sintered body according to the embodiment has uniform metallic microstructure and so exhibits mechanical properties with little variation in strength or toughness.

[0056] The reasons for the limitations in the embodiment are described below. In the following description, “%” denotes mass %, and the amount of Mo, the amount of Cu, and the amount of graphite powder each denote the content ratio to the alloy steel powder for powder metallurgy.

[0057] The iron-based powder used in the embodiment is described first.

[0058] The iron-based powder used in the embodiment has a mean particle size of 30 μm to 120 μm. If the mean particle size is less than 30 μm the iron-based powder itself or the mixed powder obtained using the iron-based powder has poor fluidity, which is problematic in terms of production efficiency, etc. If the mean particle size is more than 120 μm the driving force of the shrinkage of the green compact during sintering is weak, and coarse holes form around coarse iron powder particles. These coarse holes cause a decrease in sintered density of the sintered body, and lead to lower strength and toughness of the sintered body after carburizing-quenching-tempering.

[0059] Accordingly, the mean particle size of the iron-based powder is limited to an appropriate range of 30 μm to 120 μm in the embodiment. The mean particle size of the iron-based powder is preferably in the range of 40 μm to 100 μm and further preferably in the range of 50 μm to 80 μm. The term “mean particle size” in the embodiment means median size (d.sub.50, volume-based).

[0060] Examples of the iron-based powder include an as-atomized powder, an atomized iron powder, and a reduced iron powder. The iron-based powder used in the embodiment is preferably an iron-based powder produced by an atomizing method, that is, an as-atomized powder and/or an atomized iron powder.

[0061] Thus, the iron-based powder used in the embodiment may be any of: an as-atomized powder obtained by atomizing molten steel and then drying and classifying the resulting powder without heat treatment for deoxidation (reduction), decarburization, or the like; and an atomized iron powder obtained by reducing an as-atomized powder in a reducing atmosphere.

[0062] The apparent density of the as-atomized powder or atomized iron powder may be about 2.0 Mg/m.sup.3 to 3.5 Mg/m.sup.3. The apparent density of the as-atomized powder or atomized iron powder is more preferably in the range of 2.5 Mg/m.sup.3 to 3.2 Mg/m.sup.3. The specific surface area of the as-atomized powder or atomized iron powder may be about 0.005 m.sup.2/g or more. The specific surface area of the as-atomized powder or atomized iron powder is more preferably 0.01 m.sup.2/g or more.

[0063] The apparent density mentioned here is measured by the test method of JIS Z 2504.

[0064] The following describes Mo used in the embodiment.

[0065] The amount of Mo diffusionally adhered is in the range of 0.2% to 1.5% with respect to the alloy steel powder for powder metallurgy in the embodiment. If the amount of Mo is less than 0.2%, the hardenability improving effect is low, and the strength increasing effect is low. If the amount of Mo is more than 1.5%, the hardenability improving effect is saturated, and the non-uniformity of the microstructure of the sintered body increases, making it impossible to obtain high strength and high toughness. The amount of Mo diffusionally adhered is therefore 0.2% to 1.5%. The amount of Mo diffusionally adhered is preferably in the range of 0.3% to 1.0%, and further preferably in the range of 0.4% to 0.8%.

[0066] As a Mo material powder, a Mo-containing powder itself may be used, or a Mo compound that can be reduced to a Mo-containing powder may be used. As the Mo-containing powder, a pure metal powder of Mo, an oxidized Mo powder, an Fe—Mo (ferromolybdenum) powder, or the like is advantageous. As the Mo compound, Mo carbide, Mo sulfide, Mo nitride, or the like is suitable.

[0067] The iron-based powder and the Mo material powder are mixed so that the amount of Mo is in the range of 0.2% to 1.5% with respect to the alloy steel powder for powder metallurgy. The mixing method is not particularly limited, and may be a conventional method using a Henschel mixer, a cone mixer or the like.

[0068] The mixed powder (the iron-based powder+the Mo material powder) is then held at a high temperature, and subjected to heat treatment of diffusionally bonding Mo to iron in the contact surface of the iron-based powder and the Mo material powder, to obtain a partial alloy steel powder of Mo.

[0069] As the atmosphere of the heat treatment, a reducing atmosphere or a hydrogen-containing atmosphere is suitable, and a hydrogen atmosphere is particularly suitable. The heat treatment may be performed at atmospheric pressure, under reduced pressure, or under vacuum. The temperature of the heat treatment is preferably in the range of 800° C. to 1000° C.

[0070] In the case where the diffusionally adhering treatment is performed as mentioned above, the iron-based powder and the Mo-containing powder are in a state of being sintered and agglomerated. Therefore, the iron-based powder and the Mo-containing powder are ground and classified into a desired particle size. In detail, the grinding condition is strengthened or a coarse powder is removed by classification using a sieve with predetermined openings according to need, to achieve the desired particle size. The maximum particle size of the partial alloy steel powder obtained in this way is preferably 180 μm or less.

[0071] Coarse particles exceeding 180 μm lead to non-uniform microstructure after carburizing-quenching-tempering, as it takes time for C to reach the particle center during carburizing-quenching.

[0072] In addition, annealing may be optionally performed in the embodiment.

[0073] The balance of the partial alloy steel powder is iron and incidental impurities in the embodiment. Examples of the impurities contained in the partial alloy steel powder include C, O, N, and S. As long as the contents of these components are limited to C: 0.02% or less, O: 0.3% or less, N: 0.004% or less, and S: 0.03% or less with respect to the partial alloy steel powder, there is no particular problem. The O content is more preferably 0.25% or less. If the contents of the incidental impurities exceed these ranges, the partial alloy steel powder decreases in compressibility, and is difficult to be compression molded into a preformed body having sufficient density.

[0074] In the embodiment, a Cu powder and a graphite powder (a carbon powder such as graphite) are added to the partial alloy steel powder obtained as described above, in order to achieve a tensile strength of 1000 MPa or more after carburizing-quenching-tempering the sintered body.

[0075] The following describes the Cu powder used in the embodiment. [0076] The mean particle size of the Cu powder: 25 μm or less

[0077] Cu is a useful element that promotes the solid-solution-strengthening and hardenability improvement of the iron-based powder and enhances the strength of the sintered part. If a Cu powder of about 28 μm to 50 μm in mean particle size typically employed in iron-based powder metallurgy is used, molten Cu infiltrates between the particles of the iron powder and expands the volume of the sintered part, causing a decrease in sintered body density (Cu expansion). To suppress such a decrease in sintered body density, a Cu powder of 25 μm or less in mean particle size needs to be used. The mean particle size of the Cu powder is preferably 10 μm or less, and further preferably 5 μm or less. The lower limit of the mean particle size of the Cu powder is not particularly limited, but is preferably about 0.5 μm to avoid an unnecessary increase of the Cu powder production cost.

[0078] The mean particle size of the Cu powder in the embodiment means the median size of the primary particles of the Cu powder.

[0079] The median size can be determined by the following method.

[0080] Since the mean particle size of the Cu powder having such a particle size as in the embodiment is difficult to be measured by sieving, the particle size is measured by a laser diffraction-scattering type particle size distribution measurement device. An example of the measurement device is LA-950V2 made by HORIBA, Ltd. Although other laser diffraction-scattering type particle size distribution measurement devices may be used, a measurement device whose measurable particle size range lower limit is 0.1 μm or less and upper limit is 45 μm or more is preferable for accurate measurement.

[0081] The laser diffraction-scattering type particle size distribution measurement device applies laser light to a solvent in which the Cu powder is dispersed, and measures the particle size distribution and mean particle size of the Cu powder from the diffraction and scattering strength of the laser light. The solvent in which the Cu powder is dispersed is preferably ethanol which has good particle dispersibility and is easy to handle. The use of a solvent with a high van der Waals force and low dispersibility, such as water, is not preferable because particles coagulate during the measurement and the measurement result is coarser than the actual mean particle size.

[0082] The ethanol solution into which the Cu powder is charged is preferably subjected to ultrasonic dispersion treatment before the measurement. Since the appropriate dispersion treatment time differs depending on the powder to be measured, the measurement is performed several times while varying the dispersion treatment time in the range of 0 minutes to 60 minutes.

[0083] The measurement is performed while stirring the solvent, to prevent particle recoagulation. The lowest value of the measurement results obtained while varying the dispersion treatment time is used as the mean particle size of the Cu powder. [0084] The Cu powder having a flat shape and satisfying the relation L≦−2d+50 where d (μm) is the thickness of the Cu powder and L (μm) is the diameter in the major axis of the Cu powder

[0085] The Cu powder can suppress the aforementioned decrease in sintered body density even when its mean particle size is more than 25 μm as long as the Cu powder has a predetermined flat shape. In this case, the Cu powder satisfies the relation L≦−2d+50 where d (μm) is the thickness of the powder and L (μm) is the diameter in the major axis of the powder. The lower limit of d is not particularly limited, but is preferably about 0.05 μm to avoid an unnecessary increase of the Cu powder production cost. The upper limit of d is not particularly limited, but is preferably about 12.5 μm.

[0086] The flat powder in the embodiment is a powder that satisfies the relation L≦−2d+50, and is made up of flat particles whose diameter (length) in the thickness direction (the direction perpendicular to the plane with the smallest flattening (highest roundness), the direction of reference sign 2 in FIG. 1) is smaller than the diameter in the spreading direction (the direction of the plane with the smallest flattening, the direction of reference sign 1 in FIG. 1) as illustrated in FIG. 1. In the embodiment, the diameter (length) in the thickness direction of a primary particle is defined as the thickness d, and the length of the longest part of the diameter in the spreading direction as the diameter in the major axis L, as illustrated in FIG. 1. Here, L is more than 0.

[0087] Regarding the thickness and major axis of the flat powder in the embodiment, their representative values can be evaluated by observing the Cu particles by a scanning electron microscope (SEM) and measuring the thickness d and diameter in major axis L of each of randomly selected 100 or more particles. Since d and L each have a distribution, their mean values are calculated and set as the thickness d and the diameter in the major axis L in the embodiment.

[0088] By limiting the Cu powder to the aforementioned shape, Cu expansion is suppressed, and the decrease in sintered body density is reduced, or rather the sintered body density increases.

[0089] A mixed Cu powder obtained by mixing the aforementioned Cu powder having a mean particle size of 25 μm or less and the aforementioned Cu powder having the predetermined flat shape, i.e. satisfying the relation L≦−2d+50, may be used in the embodiment. The mixture ratio of the Cu powders of the respective shapes in the mixed Cu powder is not particularly limited. [0090] The additive amount of the Cu powder: 0.5% to 4.0%

[0091] If the additive amount of the Cu powder is less than 0.5%, the aforementioned advantageous effect of the Cu addition cannot be achieved. If the additive amount of the Cu powder is more than 4.0%, not only the effect of increasing the strength of the sintered part is saturated, but also the effect of the Cu powder shape decreases, leading to a decrease in sintered body density. The additive amount of the Cu powder is therefore limited to the range of 0.5% to 4.0%. The additive amount of the Cu powder is preferably in the range of 1.0% to 3.0%.

[0092] The following describes the graphite powder used in the embodiment.

[0093] The graphite powder is effective in obtaining higher strength and higher fatigue strength. Apart from the aforementioned C as an impurity contained in the partial alloy steel powder, 0.1% to 1.0% the graphite powder is added as C to the alloy steel powder. If the additive amount is less than 0.1%, the effect of obtaining high strength and the like cannot be achieved. If the additive amount is more than 1.0%, the sintered body becomes hypereutectoid, and cementite precipitates and causes a decrease in strength of the sintered body. The additive amount of the graphite powder is therefore limited to the range of 0.1% to 1.0%. The mean particle size of the graphite powder added is preferably in the range of about 1 μm to 50 μm.

[0094] Thus, the partial diffusion alloy steel powder to which Mo is diffusionally adhered is mixed with the Cu powder and the graphite powder to obtain the Fe—Mo—Cu—C-based alloy steel powder for powder metallurgy in the embodiment. The mixing method used for each mixture may be a conventional powder mixing method.

[0095] In the case where the part needs to be further shaped by machining work or the like at the sintered body stage, powders for improving machinability such as MnS may be added as appropriate according to a conventional method.

[0096] The following describes suitable pressing conditions and sintering conditions for producing the sintered body using the alloy steel powder for powder metallurgy according to the embodiment.

[0097] When pressing the alloy steel powder for powder metallurgy according to the embodiment, a lubricant powder may also be mixed. The pressing may be performed by applying or adhering a lubricant to a die. In either case, as the lubricant, metal soap such as zinc stearate or lithium stearate, amide-based wax such as ethylenebisstearamide, and other well known lubricants may all be used suitably. In the case of mixing the lubricant, the amount of the lubricant is preferably about 0.1 parts by mass to 1.2 parts by mass with respect to 100 parts by mass the alloy steel powder for powder metallurgy.

[0098] The pressing of the alloy steel powder for powder metallurgy according to the embodiment to produce the green compact is preferably performed with a pressure of 400 MPa to 1000 MPa. If the pressure is less than 400 MPa, the density of the obtained green compact is low, causing a decrease in various properties of the sintered body such as strength. If the pressure is more than 1000 MPa, the life of the die shortens extremely, which is economically disadvantageous. The pressing temperature is preferably in the range of room temperature (about 20° C.) to about 160° C.

[0099] The green compact is sintered preferably in the temperature range of 1100° C. to 1300° C. If the sintering temperature is less than 1100° C., the sintering does not progress, and a desired tensile strength (1000 MPa or more) is not obtained. If the sintering temperature is more than 1300° C., the life of the sintering furnace shortens, which is economically disadvantageous. The sintering time is preferably in the range of 10 minutes to 180 minutes.

[0100] The sintered body produced by the aforementioned procedure using the alloy steel powder according to the embodiment has higher sintered body density than a sintered body produced from a green compact of the same green density by a conventional production method.

[0101] The obtained sintered body may be optionally subjected to strengthening treatment such as carburizing-quenching, bright quenching, induction hardening, and carburizing nitriding treatment. Even in the case where such strengthening treatment is not performed, the sintered body produced using the alloy steel powder for powder metallurgy according to the embodiment has improved strength and toughness as compared with conventional sintered bodies not subjected to strengthening treatment. Each strengthening treatment may be performed according to a conventional method.

Examples

[0102] The disclosed techniques are described in more detail below by way of examples, although the disclosure is not limited to the following examples.

[0103] As iron-based powders, an as-atomized powder and a reduced iron powder with an apparent density of 2.50 Mg/m.sup.3 to 3.05 Mg/m.sup.3 were used.

[0104] An oxidized Mo powder (mean particle size: 10 μm) was added to each of these iron-based powders at a predetermined ratio, and the resultant powder was mixed for 15 minutes in a V-shaped mixer to obtain a mixed powder. The mixed powder was then subjected to heat treatment (holding temperature: 880° C., holding time: 1 h) in a hydrogen atmosphere with a drew point of 30° C. to diffusionally adhere the predetermined amount of Mo shown in Table 1 to the surface of the iron-based powder, thus obtaining a partial alloy steel powder.

[0105] Following this, a Cu powder of the mean particle size and amount shown in Table 1 and a graphite powder (mean particle size: 5 μm) of the amount shown in Table 1 were added to and mixed with the partial alloy steel powder, to produce an alloy steel powder for powder metallurgy.

[0106] 0.6 parts by mass ethylenebisstearamide was added with respect to 100 parts by mass the obtained alloy steel powder for powder metallurgy, and the resulting powder was mixed for 15 minutes in a V-shaped mixer. After the mixture, the powder was pressed to a density of 7.0 g/cm.sup.3, and (ten) tablet shaped green compacts with a length of 55 mm, a width of 10 mm, and a thickness of 10 mm, (ten) tablet shaped green compacts with a length of 80 mm, a width of 15 mm, and a thickness of 15 mm, and ring shaped green compacts with an outer diameter of 38 mm, an inner diameter of 25 mm, and a thickness of 10 mm were produced.

[0107] The tablet shaped green compacts and the ring shaped green compacts were each sintered to obtain a sintered body. The sintering was performed in a propane converted gas atmosphere at a sintering temperature of 1130° C. for a sintering time of 20 minutes.

[0108] Regarding the ring shaped sintered bodies, the outer diameter, the inner diameter, the thickness, and the mass were measured, and the sintered body density (Mg/m.sup.3) was calculated.

[0109] Regarding the tablet shaped sintered bodies with a length of 55 mm, a width of 10 mm, and a thickness of 10 mm, five tablet shaped sintered bodies were each processed into a round bar tensile test piece with a parallel portion diameter of 5 mm, for a tensile test specified in JIS Z 2241.

[0110] Moreover, five tablet shaped sintered bodies as sintered were each subjected to a Charpy impact test specified in JIS Z 2242. Regarding the tablet shaped sintered bodies with a length of 80 mm, a width of 15 mm, and a thickness of 15 mm, they were each processed into a smooth round bar test piece with a parallel portion of 8 mm and a length of 15.4 mm, for a rotating bending fatigue test. Each obtained test piece was subjected to gas carburizing of carbon potential of 0.8 mass % (holding temperature: 870° C., holding time: 60 minutes), and then quenching (60° C., oil quenching) and tempering (holding temperature: 180° C., holding time: 60 minutes).

[0111] The round bar tensile test pieces, smooth round bar test pieces, and tablet shaped test pieces for the Charpy impact test which had undergone the carburizing-quenching-tempering processes were submitted to the tensile test specified in JIS Z 2241, the Charpy impact test specified in JIS Z 2242, and the fatigue test by an Ono type rotating bending fatigue test machine, to measure the tensile strength (MPa), the impact value (J/cm.sup.2), and the bending fatigue strength (MPa). In each of the measurements, a mean value of the number of test pieces n=5 was set as the measurement result.

[0112] The measurement results are shown in Table 1.

[0113] The following criteria were used.

[0114] (1) Thickness d and Diameter in Major Axis L of Particles

[0115] For the thickness and diameter in major axis of the powder, the Cu particles were observed by a scanning electron microscope (SEM), and the thickness d and diameter in major axis L of each of randomly selected 100 or more particles were measured. Since d and L each have a distribution, their mean values were set as the thickness d and the diameter in the major axis L in the examples.

[0116] (2) Iron Powder Flowability (Fluidity)

[0117] 100 g of the test powder was passed through a nozzle of 5 mmφ, in diameter. The test powder was rated good if the powder flew through the nozzle completely without stopping, and rated poor if a part or whole of the powder stopped and did not flow through the nozzle.

[0118] (3) Sintered Body Density

[0119] The sintered body was rated good if the sintered body density was 6.89 Mg/m.sup.3 or more, and rated poor if the sintered body density was less than 6.89 Mg/m.sup.3.

[0120] (4) Tensile Strength

[0121] The round bar tensile test piece that had undergone the carburizing-quenching-tempering processes was rated good if the tensile strength was 1000 MPa or more, and rated poor if the tensile strength was less than 1000 MPa.

[0122] (5) Impact Value

[0123] The tablet shaped test piece for the Charpy impact test that had undergone the carburizing-quenching-tempering processes was rated good if the impact value was 14.5 J/cm.sup.2 or more, and rated poor if the impact value was less than 14.5 J/cm.sup.2.

[0124] (6) Fatigue Test

[0125] The fatigue test by the Ono type rotating bending fatigue test machine was performed at a rotational speed of 3000 rpm and a stress ratio of R=−1, and the maximum stress not resulting in a fracture in 10.sup.7 cycles was set as the fatigue strength. The test piece was rated good if the fatigue strength was 350 MPa or more, i.e. at least as high as that of a 4Ni material, and rated poor if the fatigue strength was less than 350 MPa.

TABLE-US-00001 TABLE 1 Apparent Mean particle Mean particle density of iron- size of iron- size of Type of iron-based based powder based powder Mo Cu powder L d Cu powder No. powder Mg/m.sup.3 μm mass % μm (μm) (μm) −2d + 50 mass % 1 As-atomized powder 2.65 60 1.4 5 — — — 1.0 2 As-atomized powder 2.65 60 1.0 1.5 — — — 0.5 3 As-atomized powder 2.80 60 0.8 24 — — — 2.0 4 As-atomized powder 2.80 60 0.6 15 — — — 3.0 5 As-atomized powder 2.80 60 0.7 0.9 — — — 2.0 6 As-atomized powder 2.65 60 1.4 30 — — — 1.0 7 As-atomized powder 2.65 60 1.0 35 — — — 0.5 8 As-atomized powder 2.80 60 0.8 28 — — — 2.0 9 As-atomized powder 2.80 60 0.6 30 — — — 3.0 10 As-atomized powder 2.80 60 0.7 35 — — — 2.0 11 As-atomized powder 2.50 20 0.8 24 — — — 1.0 12 As-atomized powder 2.70 30 0.8 24 — — — 1.0 13 As-atomized powder 2.80 40 0.8 24 — — — 1.0 14 As-atomized powder 2.90 50 0.8 24 — — — 1.0 15 As-atomized powder 2.95 80 0.8 24 — — — 1.0 16 As-atomized powder 3.00 100 0.8 24 — — — 1.0 17 As-atomized powder 3.05 120 0.8 24 — — — 1.0 18 As-atomized powder 3.00 150 0.8 24 — — — 1.0 19 As-atomized powder 3.00 60 0.1 24 — — — 1.0 20 As-atomized powder 3.00 60 0.2 24 — — — 1.0 21 As-atomized powder 3.00 60 0.4 24 — — — 1.0 22 As-atomized powder 3.00 60 0.6 24 — — — 1.0 23 As-atomized powder 3.00 60 0.8 24 — — — 1.0 24 As-atomized powder 3.00 60 1.0 24 — — — 1.0 25 As-atomized powder 3.00 60 1.5 24 — — — 1.0 26 As-atomized powder 3.00 60 2.0 24 — — — 1.0 27 As-atomized powder 3.00 60 0.8 1.5 — — — 0.2 28 As-atomized powder 3.00 60 0.8 1.5 — — — 0.5 29 As-atomized powder 3.00 60 0.8 1.5 — — — 1.5 30 As-atomized powder 3.00 60 0.8 1.5 — — — 3.0 31 As-atomized powder 3.00 60 0.8 1.5 — — — 4.0 32 As-atomized powder 3.00 60 0.8 1.5 — — — 5.0 33 As-atomized powder 3.00 60 0.8 1.5 — — — 2.0 34 As-atomized powder 3.00 60 0.8 1.5 — — — 2.0 35 As-atomized powder 3.00 60 0.8 1.5 — — — 2.0 36 As-atomized powder 3.00 60 0.8 1.5 — — — 2.0 37 As-atomized powder 3.00 60 0.8 1.5 — — — 2.0 38 As-atomized powder 3.00 60 0.8 29 30 1 48 2.0 39 As-atomized powder 3.00 60 0.8 22 25 1.5 47 2.0 40 As-atomized powder 3.00 60 0.8 18 20 2.5 45 2.0 41 As-atomized powder 3.00 60 0.8 14 15 4.5 41 2.0 42 As-atomized powder 3.00 60 0.8 9 10 9 32 2.0 43 As-atomized powder 3.00 60 0.8 47 45 2 46 2.0 44 As-atomized powder 3.00 60 0.8 39 48 1 48 2.0 45 As-atomized powder 3.00 60 0.8 74 55 5 40 2.0 46 Reduced iron powder 2.80 60 0.8 24 — — — 2.0 47 As-atomized powder 2.80 65 *2 *2 — — — *2 Sintered Bending Graphite Alloy body Tensile Impact fatigue powder steel powder density strength value test No. mass % flowability*.sup.1 Mg/m.sup.3 Result MPa Result J/cm.sup.2 Result MPa Result Remarks  1 0.5 Good 6.96 Good 1247 Good 15.5 Good 450 Good Example 1  2 0.3 Good 6.93 Good 1150 Good 14.5 Good 410 Good Example 2  3 0.3 Good 6.89 Good 1167 Good 15.4 Good 430 Good Example 3  4 0.5 Good 6.90 Good 1130 Good 15.6 Good 403 Good Example 4  5 0.1 Good 6.96 Good 1051 Good 14.6 Good 400 Good Example 5  6 0.5 Good 6.88 Poor 1220 Good 15.0 Good 430 Good Comparative Example 1  7 0.3 Good 6.87 Poor 1124 Good 14.1 Poor 405 Good Comparative Example 2  8 0.3 Good 6.86 Poor 1150 Good 15.2 Good 415 Good Comparative Example 3  9 0.5 Good 6.86 Poor 1120 Good 15.5 Good 415 Good Comparative Example 4 10 0.1 Good 6.88 Poor 1006 Good 14.0 Poor 370 Good Comparative Example 5 11 0.3 Poor 6.99 Good — — — — — — Comparative Example 6 12 0.3 Good 6.97 Good 1146 Good 16.1 Good 430 Good Example 6 13 0.3 Good 6.96 Good 1106 Good 15.9 Good 400 Good Example 7 14 0.3 Good 6.95 Good 1080 Good 15.7 Good 401 Good Example 8 15 0.3 Good 6.93 Good 1069 Good 15.2 Good 390 Good Example 9 16 0.3 Good 6.92 Good 1052 Good 14.8 Good 385 Good Example 10 17 0.3 Good 6.90 Good 1033 Good 14.5 Good 382 Good Example 11 18 0.3 Good 6.87 Poor 998 Poor 13.9 Poor 365 Good Comparative Example 7 19 0.3 Good 6.97 Good 1118 Good 14.3 Poor 395 Good Comparative Example 8 20 0.3 Good 7.00 Good 1137 Good 15.1 Good 417 Good Example 12 21 0.3 Good 7.02 Good 1166 Good 16.1 Good 420 Good Example 13 22 0.3 Good 7.01 Good 1168 Good 14.9 Good 424 Good Example 14 23 0.3 Good 6.99 Good 1110 Good 14.7 Good 406 Good Example 15 24 0.3 Good 6.99 Good 1092 Good 14.5 Good 400 Good Example 16 25 0.3 Good 7.00 Good 1087 Good 14.6 Good 390 Good Example 17 26 0.3 Good 7.00 Good 1085 Good 13.6 Poor 410 Good Comparative Example 9 27 0.30 Good 7.07 Good 989 Poor 13.5 Poor 365 Good Comparative Example 10 28 0.30 Good 7.05 Good 1020 Good 14.5 Good 380 Good Example 18 29 0.30 Good 7.03 Good 1138 Good 15.4 Good 403 Good Example 19 30 0.30 Good 7.01 Good 1189 Good 16.8 Good 440 Good Example 20 31 0.30 Good 6.97 Good 1231 Good 17.4 Good 430 Good Example 21 32 0.30 Good 6.86 Poor 1254 Good 17.9 Good 460 Good Comparative Example 11 33 0.05 Good 7.01 Good 984 Poor 15.8 Good 360 Good Comparative Example 12 34 0.2 Good 7.04 Good 1088 Good 15.0 Good 398 Good Example 22 35 0.5 Good 6.99 Good 1138 Good 14.6 Good 407 Good Example 23 36 1.0 Good 7.01 Good 1169 Good 14.5 Good 415 Good Example 24 37 1.5 Good 7.02 Good 1125 Good 12.6 Poor 418 Good Comparative Example 13 38 0.3 Good 6.95 Good 1152 Good 15.5 Good 425 Good Example 25 39 0.3 Good 6.99 Good 1180 Good 16.5 Good 426 Good Example 26 40 0.3 Good 6.96 Good 1155 Good 16.3 Good 420 Good Example 27 41 0.3 Good 6.92 Good 1160 Good 15.7 Good 431 Good Example 28 42 0.3 Good 6.90 Good 1100 Good 15.5 Good 410 Good Example 29 43 0.3 Good 6.94 Good 1132 Good 15.5 Good 417 Good Example 30 44 0.3 Good 6.92 Good 1130 Good 15.3 Good 419 Good Example 31 45 0.3 Good 6.85 Poor 1010 Good 14.1 Poor 380 Good Comparative Example 14 46 0.3 Good 6.90 Good 1200 Good 15.7 Good 355 Good Example 32 47 0.3 Good 7.01 Good 998 Poor 13.3 Poor 348 Poor Conventional Example*.sup.2 *.sup.1100 g of alloy steel powder was passed through a nozzle of 5 mmφ in diameter. The powder was rated good if the powder flew through the nozzle completely without stopping, and rated poor if a part or whole of the powder stopped and did not flow through the nozzle. *2 4Ni material (4% Ni—1.5% Cu—0.5% Mo partial alloy steel powder)

[0126] As shown in Table 1, in all Examples, despite the alloy steel powder for powder metallurgy having a chemical composition not containing Ni, a part produced using the powder as a precursor powder had mechanical properties of at least as high tensile strength and toughness as a Ni-added material.

[0127] Table 1 also shows the results of a 4Ni material (4% Ni-1.5% Cu-0.5% Mo partial alloy steel powder obtained by adding a Ni powder (mean particle size: 8 μm), an oxidized Mo powder (mean particle size: 10 μm), and a Cu powder (mean particle size: 28 μm) to an iron-based powder (as-atomized powder, apparent density: 2.80 Mg/m.sup.3, mean particle size: 65 μm), mixing them, and heat treating the mixed powder to diffusionally adhere Ni, Mo, and Cu to the surface of the iron-based powder), as Conventional Example.

[0128] In Examples, a sintered body (iron-based sintered body) having high density and also having both high strength and high toughness was obtained even by a typical sintering method.

[0129] Moreover, in Examples, the alloy steel powder had excellent fluidity.

REFERENCE SIGNS LIST

[0130] 1 diameter in major axis: L [0131] 2 thickness: d