JP4737107B2 - Iron-based powder mixture, iron-based powder molded body, and method for producing iron-based powder sintered body - Google Patents

Description

The present invention relates to an iron-based powder mixture in which iron-based powders such as iron powder and alloy steel powder are mixed with predetermined additives, and further alloy powders such as graphite powder and copper powder. The present invention relates to an iron-based powder mixture for powder metallurgy, which is excellent in compressibility in pressure molding in a temperature range of less than 0 ° C. and is particularly suitable for the production of high-strength sintered parts for automobiles.
The present invention also relates to a method for producing an iron-based powder compact using the iron-based powder mixture as a raw material, and a method for producing an iron-based powder sintered body using the iron-based powder compact as a raw material.

  Iron-based powder mixture for powder metallurgy requires iron-based powder, alloy powder such as copper powder, graphite powder, and iron phosphide powder, lubricant such as zinc stearate, aluminum stearate, lead stearate, etc. In general, it is generally produced by mixing the machinability improving powder. The lubricant to be used has been selected in consideration of the miscibility with the iron-based powder and the dissipating property during sintering.

  In recent years, with increasing demand for higher strength for sintered parts, as disclosed in Patent Literature 1, Patent Literature 2, Patent Literature 3 and Patent Literature 4, by molding an iron-based powder mixture while heating, Warm forming technology that enables high density and high strength of the compact has been developed. This technique makes it possible to improve the density of the molded body at a lower load by utilizing the fact that the plastic deformation resistance of iron-based powder is reduced by heating.

However, such an iron-based powder mixture has left the following problems.
In other words, warm molding is a technique in which a mold and powder are preheated to a high temperature of 100 ° C. or higher, and then an iron-based powder mixture is pressure-molded, but an iron-based powder mixture having poor thermal conductivity is stably formed. Since it is extremely difficult to heat and keep above 100 ° C., the productivity of sintered parts tends to be reduced. In addition, heating the iron-based powder mixture for a long time has caused a problem of alteration due to oxidation of the iron-based powder mixture.

Patent Documents 5 and 6 disclose techniques using an inorganic compound having a layered crystal such as MoS ₂ , fluorocarbon, and graphite as a lubricant.
However, when MoS ₂ is used, there is a risk of decomposing at the time of sintering, generating harmful S and contaminating the firing furnace. In addition, when carbon fluoride is used and sintered in a hydrogen atmosphere, the generation of hydrogen fluoride is a concern.

Japanese Patent Laid-Open No. 2-156002 Japanese Patent Publication No. 7-103404 U.S. Pat.No. 5,256,185 U.S. Pat.No. 5,368,630 JP-A-9-104901 JP-A-10-317001

  By the way, in order to manufacture parts of various machines such as automobiles by powder metallurgy technology, an iron-based powder mixture is filled in a mold, compacted, and further sintered. The sintered parts thus obtained have good dimensional accuracy and can be manufactured in complex shapes. However, when manufacturing a sintered part that requires extremely strict dimensional accuracy, it is necessary to perform further machining (for example, cutting or drilling) after sintering.

However, since sintered parts are inferior in machinability, cutting tools used in machining are significantly worn. As a result, the machining cost increases and the manufacturing cost of the sintered part increases. Such deterioration of the machinability of the sintered part is caused by a decrease in the thermal conductivity of the sintered part due to pores present inside, and an increase in the temperature of the sintered part during cutting.
It has been conventionally known that the machinability of sintered parts is improved by adding a free-cutting component (for example, S, MnS, etc.) to an iron-based powder mixture for powder metallurgy. The free-cutting component has the effect of easily breaking chips, or the effect of increasing the lubricity of a cutting tool (particularly the rake face) by forming a thin component edge on the cutting tool.

Sintered parts are used as parts for various devices, but automobile parts (for example, gears) are required to have high strength and high fatigue strength. Therefore, various techniques using an iron-based powder mixture to which alloy components are added have been studied in order to produce sintered parts having high strength and high fatigue strength.
For example, Patent Document 7 discloses a technique for adhering and diffusing powders such as Ni, Cu, and Mo to pure iron powder. The iron-based powder mixture obtained by this technique has excellent compressibility and is suitable for the production of sintered parts having high strength and high fatigue strength.
However, in the technique disclosed in Patent Document 7, since diffusion of Ni is slow, long-time sintering is required to sufficiently diffuse Ni into the pure iron powder. Moreover, since the hardness of the obtained sintered part is high, even if a free-cutting component is added to the iron-based powder mixture, a significant improvement in machinability cannot be expected.

Also, in Cited Document 8, an iron-based powder in which Cu powder and / or Ni powder is added to a low alloy steel powder containing C and Mo but substantially free of Mn and Cr, and further graphite powder is added. Mixtures are disclosed. Furthermore, cited document 9 discloses an iron-based powder mixture in which Cu powder is fused to alloy steel powder containing Mo, Mn, and C. These iron-based powder mixtures are suitable for the production of high strength sintered parts.
However, with the iron-based powder mixture disclosed in Patent Documents 8 and 9, it was difficult to produce a sintered part excellent in machinability.

Japanese Patent Publication No. 45-9649 JP-A-61-163239 JP 63-114903 A

The present invention advantageously solves the above-mentioned problems, and has excellent moldability in a low temperature range of less than 100 ° C. without adversely affecting the furnace environment of the firing furnace when the molded body is sintered. Another object of the present invention is to propose an iron-based powder mixture for powder metallurgy that is suitable for producing sintered parts excellent in machinability.
The present invention also proposes a method for producing an iron-based powder compact using the iron-based powder mixture as a raw material, and a method for producing an iron-based powder sintered body using the iron-based powder compact as a raw material. With the goal.

Now, as a measure for solving the above problems, the inventors do not adversely affect the furnace environment when forming the iron-based powder mixture, and lower the heating temperature of the iron-based powder mixture, preferably no heating. Even in the case of forming into a compact, the inventors have made extensive studies on the additive that enables the production of a high-density molded body.
As a result, when talc, steatite, and fatty acid amide are used as additives, and when metal soap is used, the iron-based powder particles are rearranged during pressure molding due to the lubricating function of these additives. The iron-based powder molded body having a high molding density can be obtained even at a molding temperature as low as room temperature, and the sintered body obtained by sintering such an iron-based powder molded body has mechanical strength and The knowledge of excellent machinability was obtained.
The present invention is based on the above findings.

That is, the gist configuration of the present invention is as follows.
(1) An iron-based powder mixture obtained by adding at least one selected from talc and steatite and a fatty acid amide as an additive to an iron-based powder , and further adding an alloy powder , the talc and The addition amount of at least one selected from steatite is in the range of 0.01 to 0.5 mass% with respect to the entire iron-based powder mixture, and the iron-based powder is added to the entire iron-based powder mixture. Mo: 0.3 to 0.5 mass% and Mn: 0.1 to 0.25 mass%, the balance is water atomized alloy steel powder composed of Fe and unavoidable impurities, and the addition amount of the above alloy powder is the above iron-based powder An iron-based powder mixture characterized in that Cu powder: 1 to 3 mass% and graphite powder: 0.5 to 1.0 mass% with respect to the entire mixture.

(2) The iron-based powder mixture as described in (1) above, wherein the additive further contains a metal soap.

( 3 ) A method for producing an iron-based powder molded body comprising filling the mold with the iron-based powder mixture according to claim (1) or (2) and molding at a temperature of less than 100 ° C.

( 4 ) Filling the mold with the iron-based powder mixture according to claim (1) or (2) and molding the mixture at a temperature of less than 100 ° C., and then sintering the obtained iron-based powder compact. A method for producing an iron-based powder sintered body characterized by the above.

According to this invention, even if it shape | molds at the low temperature of about room temperature, the iron-based powder mixture with a high shaping | molding density and a small extraction output can be obtained.
Further, according to the present invention, by using the above iron-based powder mixture as a raw material, an iron-based powder molded body having a high molding density, an iron having a high sintering density, and excellent mechanical strength and machinability. A base powder sintered body can be obtained.

Hereinafter, the present invention will be specifically described.
First, the raw material of the iron-based powder mixture of the present invention will be described.
In the present invention, Tetsumotoko powder shall be the water-atomized alloyed steel powder.

Examples of the alloy powder include graphite powder, metal powder such as Cu, Mo, and Ni, boron powder, and cuprous oxide powder. The strength of the sintered body can be increased by mixing these alloy powders with the iron-based powder.
The blending amount of the alloy powder is preferably about 0.1 to 10 mass% in the iron-based powder mixture. This is because, by adding 0.1 mass% or more of the alloy powder, the strength of the obtained sintered body is advantageously improved, while when it exceeds 10 mass%, the dimensional accuracy of the sintered body decreases.

  In the present invention, it is important to add at least one selected from talc and steatite and a fatty acid amide as an additive. The talc preferably has a monoclinic or triclinic crystal structure, and the steatite preferably has a monoclinic crystal structure.

The reason why the addition of talc, steatite and fatty acid amide as an additive improves the compressibility of the molded body and at the same time reduces the output during molding and greatly improves the moldability is as follows. It is thought that
That is, talc and steatite, when subjected to shear stress between iron-based powder particles at the time of molding, the substance is easily cleaved along the crystal plane, so the frictional resistance between the particles inside the molded body is reduced, It is considered that the density of the molded body is improved by the lubrication effect of facilitating movement between particles. In addition, if talc or steatite is present between the molded body and the mold, it will be cleaved by the shearing stress from the mold surface when the molded body is extracted, which improves the ease of sliding of the molded body on the mold surface. It is considered that the unplugging power is reduced. These effects are remarkably improved by further adding a fatty acid amide.

  Since these effects are manifested regardless of the temperature of the iron-based powder mixture, it is not always necessary to heat the iron-based powder mixture, which effectively contributes to improving the density of the iron-based powder molded body in molding at room temperature. In addition, when the iron-based powder is heated, the plastic deformation resistance of the iron-based powder is reduced during pressure molding, so that a higher molded body density can be obtained. Therefore, although the heating temperature of the iron-based powder can be set as appropriate according to the required density of the compact, it is sufficient that the heating temperature is less than 100 ° C.

The addition amount of the talc and steatite shall be the order of 0.01 to 0.5 mass% relative to the total iron-based powder mixture. This is because by adding 0.01 mass% or more of these additives, it is possible to sufficiently improve the density of the molded body at the time of pressure molding and sufficiently reduce the output at the time of extracting the molded body. It is. On the other hand, when the added amount exceeds 0.5 mass%, there is a concern that the mechanical strength of the sintered material obtained by sintering the compact is reduced.

As the fatty acid amide, one or more selected from fatty acid monoamides and fatty acid bisamides are suitable. The addition amount of the fatty acid amide is preferably about 0.01 to 0.5 mass% with respect to the entire iron-based powder mixture. Since the added amount of poor Tanai and its addition effect fully to 0.01 mass%, whereas because lowering the strength of the shaped body and more than 0.5 mass%.

In the present invention, metal soap can be further contained in the additive. Here, as the metal soap, zinc stearate and lithium stearate are preferable. These not only improve the density of the compact but also improve the fluidity of the iron-based powder mixture by reducing the frictional resistance between the particles and making the particles easier to move due to the lubricating effect during the molding. Can be made.
The addition amount of the metal soap is preferably about 0.01 to 0.5 mass% with respect to the entire iron-based powder mixture. Because the addition amount poor Tanai and its addition effect fully to 0.01 mass%, whereas the strength of the shaped body and more than 0.5 mass% is lowered.
Furthermore, when a fatty acid amide and zinc stearate or lithium stearate are added in combination, the total amount of the fatty acid amide and zinc stearate or lithium stearate is added in an amount of 0.01 to 1.0 mass% with respect to the entire iron-based powder mixture. It is preferable that 0.05 to 0.5 mass% be added. This is because if the amount added is less than 0.01 mass%, the effect of adding metal soap does not appear. On the other hand, if it exceeds 1.0 mass%, the strength of the molded product decreases, and depending on the sintering conditions, sintering may be hindered. This is because the strength of the sintered body is lowered, which is not preferable.

In addition, talc and steatite exhibit lubrication performance, and do not decompose when forming and sintering an iron-based powder mixture, that is, no harmful decomposition gas is generated and sintering is not inhibited. It also contributes to improving the mechanical strength of the body.
Furthermore, these talc and steatite are MgO-SiO ₂ oxides known as free-cutting components and contribute effectively to improving the machinability of the sintered body, but the effect is combined with metal soap. It improves further by doing.
Hereinafter, the addition amount of talc and steatite suitable for expressing the above effects will be described.

When talc (3MgO · 4SiO ₂ ) or steatite (MgO · SiO ₂ ) is added for the above purpose, it is sufficiently satisfactory if the addition amount does not reach 0.05 mass% in either case of single addition or compound addition. However, when the amount exceeds 0.5 mass%, the compressibility of the iron-based powder mixture is lowered and the strength of the sintered part is reduced.
Therefore, in order to obtain particularly suitable mechanical strength and machinability, it is preferable to add talc and steatite in the range of 0.05 to 0.5 mass% in either case of single addition or combined addition.

Next, an alloy composition suitable for obtaining the above-described excellent mechanical strength and machinability will be described.
As the iron-based powder, water atomized alloy steel powder is used , and the alloy components are as follows. In addition, content (mass%) of an alloy component shows the ratio which occupies for the mass (mass%) of the iron-based powder mixture obtained by mixing water atomized alloy steel powder and the additive mentioned later by an internal number.
Mo: 0.3-0.5mass%
Mo is an element that enhances the strength of sintered parts by strengthening the solid solution of water atomized alloy steel powder and improving hardenability. However, if the content is less than 0.3 mass%, it is not possible to expect a sufficiently satisfactory improvement in the strength of the sintered part. On the other hand, if it exceeds 0.5 mass%, not only the strength improvement effect of the sintered part is saturated, but also the machinability is improved. Incurs a decline. Therefore, Mo is in the range of 0.3 to 0.5 mass%.

Mn: 0.1-0.25mass%
Mn is an element that enhances the strength of sintered parts by strengthening the solid solution of water atomized alloy steel powder and improving hardenability. However, if the content is less than 0.1 mass%, sufficient strength improvement of the sintered parts cannot be expected. On the other hand, if the content exceeds 0.25 mass%, the oxidation of Mn tends to proceed, and the strength and compressibility of the alloy steel powder are reduced. descend. Therefore, Mn is set within a range of 0.1 to 0.25 mass%.

Additives described below are mixed with the above water atomized alloy steel powder. In addition, the addition amount (mass%) of these additives shows the ratio which occupies for the mass (mass%) of the iron-based powder mixture obtained by mixing water atomized alloy steel powder and an additive by internal number.
Cu powder: 1-3mass%
Cu is an element that increases the strength of sintered parts by strengthening the solid solution of water atomized alloy steel powder and improving hardenability. Further, the Cu powder melts during sintering to form a liquid phase, and has an effect of fixing the particles of the water atomized alloy steel powder to each other. However, if the added amount is less than 1 mass%, the effect is poor. On the other hand, if it exceeds 3 mass%, the effect of improving the strength of the sintered part is saturated, and the machinability is reduced. Therefore, Cu powder shall be in the range of 1-3 mass%.

In addition, when adding Cu, if the addition amount is within the above range,
(a) Add Cu powder to water atomized alloy steel powder and simply mix.
(b) Adhering Cu powder to the surface of the water atomized alloy steel powder via a binder,
(c) Any of the methods of mixing water atomized alloy steel powder and Cu powder, further heat-treating, and adhering and diffusing Cu powder on the surface of the water atomized alloy steel powder may be adopted.

Graphite powder: 0.5-1.0mass%
C, which is the main component of the graphite powder, is an element that increases the strength of the sintered part by strengthening the solid solution of the water atomized alloy steel powder and improving the hardenability. However, if the content of graphite powder is less than 0.5 mass%, the effect of addition is poor. On the other hand, if the content exceeds 1.0 mass%, the strength of the sintered part is excessively increased and the machinability is reduced. Therefore, the graphite powder is in the range of 0.5 to 1.0 mass%.

Next, the manufacturing method of the iron-based powder mixture of this invention is demonstrated.
The iron-based powder, talc, steatite and fatty acid amides, further additives, such as metal soaps, in addition to alloy powder, mixed primary. Next, the mixture after the primary mixing is stirred while being heated above the melting point of at least one of the above-mentioned additives, gradually cooled while mixing, and added to the surface of the iron-based powder. The alloy powder and other additives are fixed by the agent.
The above-mentioned additives such as talc, steatite, fatty acid amide, and metal soap do not necessarily need to be added all at once, but after adding only a part and performing primary mixing, the remainder is added. And secondary mixing.
The mixing means is not particularly limited and any conventionally known mixer can be used. However, a high-speed bottom stirring mixer, an inclined rotary pan mixer, a rotary mulberry mixer, and a cone that can be easily heated can be used. A planetary screw type mixer or the like is particularly advantageously adapted.

Next, a method for producing an iron-based powder molded body and a method for producing an iron-based powder sintered body using the iron-based powder mixture of the present invention will be described.
The iron-based powder mixture of the present invention can be formed into a molded body by a normal molding method. That is, it can be molded at room temperature. Nevertheless, it is advantageous to heat the iron-based powder mixture or the mold or to apply a lubricant to the mold. When molding is performed in a heated atmosphere, the temperature of the iron-based powder mixture and the mold is preferably less than 100 ° C. This is because the iron-based powder mixture according to the present invention is highly compressible and exhibits excellent moldability even at temperatures below 100 ° C., and when it exceeds 100 ° C., there is a concern about deterioration due to oxidation.

  Next, the high-density iron-based powder molded body obtained as described above is subjected to a sintering treatment to obtain a high-density sintered body. The sintering treatment is not particularly limited, and any conventionally known sintering treatment method can be suitably used. It is also possible to apply a heat treatment such as a gas carburizing heat treatment or a carbonitriding treatment after the sintering treatment.

Hereinafter, the present invention will be specifically described based on experimental examples and examples.
Table 1 shows the types of various iron powders for powder metallurgy (all average particle diameter: about 80 μm) used as iron-based powders in Experimental Examples 1 to 4. Particularly in the case of alloy steel powder, it is distinguished whether it is a fully alloyed steel powder, a partially alloyed steel powder, or a hybrid steel powder in which the alloy components are partially diffused in the fully alloyed steel powder. Indicates.

Experimental example 1
Various additives (primary additive) are added to various iron-based powders, natural graphite powder (average particle size: 5 μm) and / or copper powder (average particle size: 25 μm) shown in Table 2, and high-speed bottom stirring is performed. After heating to 140 ° C. while mixing with a mixer, cool to 60 ° C. or below, add various additives (secondary additives), stir at 500 rpm for 1 minute, and then discharge the mixed powder from the mixer . Table 2 shows the types and amounts of primary and secondary additives. The additive amount (parts by mass) of the additive is the total mass of iron-based powder, natural graphite powder, and copper powder: the ratio to 100 mass% is indicated by an external number, but is almost the same as the numerical value expressed by the internal number It is. The average particle sizes of talc powder and steatite powder were 6 μm and 4 μm, respectively.
For comparison, 0.8 mass% of zinc stearate as a lubricant is added to the same iron-based powder, natural graphite powder and / or copper powder composition as above, and mixed in a V-type container rotary mixer. The prepared mixed powder was prepared (see Table 3). This comparative material has a composition usually used in room temperature molding.

Next, each obtained iron-based powder mixture was filled into a cemented carbide tablet mold having an inner diameter of 11 mm at room temperature, and pressure-molded at 490 MPa and 686 MPa. At that time, the output when the molded body was extracted from the mold and the green density of the obtained molded body were measured.
Further, each iron-based powder mixture obtained was separately compacted with a test piece for cutting test (outer diameter: 60 mm, inner diameter: 20 mm, length: 30 mm). The pressing force for compacting was 590 MPa. Sintering was performed in an RX gas atmosphere, the heating temperature was 1130 ° C., and the heating time was 20 minutes. In evaluating the machinability, a cutting test was performed using a cermet cutting tool under the conditions of cutting speed: 200 m / min, feed: 0.1 mm / turn, cutting depth: 0.3 mm, cutting distance: 1000 m. The wear width of the flank was measured. It shows that the machinability of a sintered compact is excellent, so that the wear width of the flank of a cutting tool is small.
Table 4 shows the obtained results.

As is clear from the comparison between Reference Examples 1 to 9 and Comparative Examples 1 to 9 shown in Tables 2 to 4, by using the additive according to the present invention as a lubricant, it can be removed even at room temperature molding. A high-density green compact could be obtained without significantly increasing the output.

Experimental example 2
After adding various additives (primary additive) to various iron-based powders, natural graphite powders and / or copper powders shown in Table 5 and heating at 140 ° C. while mixing with a high-speed bottom stirring mixer, After cooling to 60 ° C. or lower, various additives (secondary additives) were added, and the mixture was stirred at 500 rpm for 1 minute, and then the mixed powder was discharged from the mixer. Table 5 shows the types and amounts of the primary and secondary additives. The raw materials used are those described in Table 1 as in Experimental Example 1.
For comparison, 0.6 mass% of ethylene bisstearamide was added to the same iron-based powder, natural graphite powder and / or steel powder composition as above, and mixed with a V-type container rotary mixer. Mixed powder was prepared (comparative material).

  Next, each obtained iron-based powder mixture at room temperature was filled in a cemented carbide tablet mold having an inner diameter of 11 mm, which was heated in advance so that the cavity wall surface temperature was 80 ° C., and pressure-molded at 490 MPa and 686 MPa. At that time, the output when the molded body was extracted from the mold and the green density of the obtained molded body were measured.

In addition, after heating the comparative material to general warm molding conditions, that is, 120 ° C, the mold was filled in a cemented carbide tablet mold with an inner diameter of 11mm heated to 130 ° C and pressurized at 490MPa and 686MPa. Molded. At that time, the output when the molded body was extracted from the mold and the green density of the obtained molded body were measured.
Further, similarly to Experimental Example 1, a test piece for a cutting test was compacted and then sintered, and then a cutting test was performed.
The results obtained are shown in Table 6.

As is apparent from the comparison between Reference Examples 10 to 15 and Comparative Examples 10 to 15 shown in Tables 5 to 6, by adding the primary and secondary additives of the present invention as a lubricant, the mold can be obtained. By simply heating to a relatively low temperature of less than 100 ° C, we were able to obtain a high-density green compact equivalent to a general warm molding material without increasing the extraction power without heating the mixed powder. .
In addition, the flank wear width (mm) of each invention example was reduced to about 20 to 40% of the comparative example of the same system (number), and a marked improvement was also seen in machinability.

Experimental example 3
After adding various additives (primary additive) to various iron-based powders, natural graphite powders and / or copper powders shown in Table 7, and heating at 140 ° C. while mixing with a high-speed bottom stirring mixer, After cooling to 60 ° C. or lower, various additives (secondary additives) were added, and the mixture was stirred at 500 rpm for 1 minute, and then the mixed powder was discharged from the mixer. Table 7 shows the types and amounts of the primary and secondary additives. The raw materials used are those described in Table 1 as in Experimental Example 1.
For comparison, each weight of ethylenebisstearamide was added, and mixed powder was prepared by mixing with a V-type container rotary mixer.

  Next, after heating each obtained iron-based powder mixture to 60 ° C, the cavity wall surface temperature was heated beforehand to 80 ° C, and lithium stearate powder was applied to the wall surface. The tablet mold was filled and pressure molded at 490 and 686 MPa. At that time, the output when the molded body was extracted from the mold and the green density of the obtained molded body were measured.

In addition, after heating the comparative material to the general warm molding conditions, that is, 120 ° C, the mold was filled in an 11 mm inside carbide tablet mold heated to 130 ° C and pressurized at 490 and 686 MPa. Molded. At that time, the output when the molded body was extracted from the mold and the green density of the obtained molded body were measured.
Table 8 shows the obtained results.

By adding the primary and secondary additives of the present invention as a lubricant, as is apparent from the comparison between Reference Example 16, Comparative Example 16, and Reference Example 17 and Comparative Example 17 shown in Tables 7 to 8. By simply heating the mold and the powder to a relatively low temperature of less than 100 ° C., it was possible to form a compact having a high density equivalent to that of a general warm molding material with an extremely low output.
Further, the flank wear width (mm) of each invention example was reduced to about 25 to 35% of the comparative example of the same system (number), and a marked improvement was also seen in the machinability.

Experimental Example 4
After adding various additives (primary additives) to various iron-based powders, natural graphite powders and / or copper powders shown in Table 9, and heating at 140 ° C. while mixing with a high-speed bottom stirring mixer, After cooling to 60 ° C. or lower, various additives (secondary additives) were added, and the mixture was stirred at 500 rpm for 1 minute, and then the mixed powder was discharged from the mixer. Table 9 shows the types and addition amounts of the primary and secondary additives. The raw materials used are the same as in Experimental Example 1. In Comparative Example 20, a steatite powder was added instead of the primary and secondary additions, and the mixture was mixed under the same conditions using a high-speed bottom stirring mixer.
Next, each obtained iron-based powder mixture was filled into a cemented carbide tablet mold having an inner diameter of 11 mm at room temperature, and pressure-molded at 490 MPa and 686 MPa. At that time, the output when the molded body was extracted from the mold and the green density of the obtained molded body were measured.
Furthermore, for the obtained iron-based powder mixture, a tensile test piece and a test piece for cutting test according to JPMA M04-1992 (outer diameter: 60 mm, inner diameter: 20 mm, length: 30 mm) are separately provided. The green compacting was performed. The pressing force for compacting was 590 MPa.
The green compact was then sintered. Sintering was performed in an RX gas atmosphere, the heating temperature was 1130 ° C., and the heating time was 20 minutes. The machinability evaluation method is the same as in Experimental Example 1.
The results obtained are shown in Table 10.

As is clear from the comparison between Reference Examples 18 to 21 and Comparative Examples 18 and 19 shown in Tables 9 to 10, the iron-based mixed powder to which steatite or the like is added within the scope of the present invention increases the output power. A high-density green compact can be obtained without this. In Comparative Example 19 in which steatite or the like was added in excess of 0.5 mass%, the mechanical properties were greatly reduced. Furthermore, from the viewpoint of mechanical properties, it can be seen from Reference Examples 18 to 21 that the addition amount of steatite and the like is more preferably 0.2 mass% or less.
Further, as is clear from the comparison between Reference Examples 22 and 23 and Comparative Examples 20 and 21, the addition of fatty acid amide and the like together with steatite and the like does not increase the output power, and a high-density green compact is obtained. It is effective in obtaining. Moreover, it turns out that the machinability of a sintered compact can be improved significantly by adding a metal soap further.

Example 1
Water atomized steel powder having the components shown in Table 11 was produced by the water atomization method. The balance other than Mn and Mo is Fe and inevitable impurities. To this water atomized alloy steel powder, Cu powder, graphite powder, talc and steatite were added in the proportions shown in Table 11. The Mn content, Mo content (mass%) in the water atomized steel powder, and Cu powder, graphite powder, talc, and steatite added to the water atomized steel powder (mass%) are all iron-based. The ratio to the mass of the powder mixture is shown by the internal number.

Further, the additive was added at a ratio shown in Table 11. The additive amount (parts by mass) of the additive indicates the ratio to the mass (100 parts by mass) of the iron-based powder mixture obtained by mixing the water atomized steel powder and the additive (in this case, this ratio is It is almost the same as the number expressed in the number.)
Next, the mixture was mixed with a V-type blender, and the obtained iron-based powder mixture was filled in a mold, and a tensile test piece and a test piece for cutting test (outer diameter: 60 mm, in accordance with JPMA M04-1992) Compaction molding was performed with an inner diameter of 20 mm and a length of 30 mm. The pressing force for compacting was 590 MPa.
The green compact was then sintered. Sintering was performed in an RX gas atmosphere, the heating temperature was 1130 ° C., and the heating time was 20 minutes.

The results of investigation on the tensile strength and machinability of the sintered body thus obtained are also shown in Table 11.
The tensile strength was measured by a tensile test.
For cutting performance, a cutting test was performed using a cermet cutting tool under the conditions of cutting speed: 200 m / min, feed: 0.1 mm / turn, cutting depth: 0.5 mm, cutting distance: 1000 m. The wear width of the flank was measured. The smaller the wear width of the flank, the better the machinability of the sintered body.

In Table 11, inventive examples are examples using an iron-based powder mixture that satisfies the scope of the present invention, and comparative examples are examples using an iron-based powder mixture that is outside the scope of the present invention. The conventional example of No. 15 is an example in which a conventional lubricant is added to a powder mixture for powder metallurgy using Fe-4Ni-1.5Cu-0.5Mo water atomized alloy steel powder that has been put to practical use. . The numerical value attached to the alloy element of No. 15 indicates mass%.

As is apparent from Table 11, all the sintered bodies obtained from the iron-based powder mixtures of the inventive examples are excellent in mechanical properties and machinability. On the other hand, especially in the conventional example, the machinability of the sintered body is extremely poor.
In addition, when water atomized alloy steel powder contains Mo: 0.3 to 0.5 mass% and Mn: 0.1 to 0.25 mass%, and Cu powder: 1 to 3 mass% and graphite powder: 0.5 to 1.0 mass%, tensile A sintered body having a strength of 500 MPa or more and excellent machinability can be obtained.

Claims (4)

An iron-based powder mixture obtained by adding at least one selected from talc and steatite and a fatty acid amide as an additive to an iron-based powder , and further adding an alloy powder , the talc and steatite The addition amount of at least one selected from the above is in the range of 0.01 to 0.5 mass% with respect to the entire iron-based powder mixture, and the iron-based powder is Mo: 0.3 -0.5mass% and Mn: 0.1-0.25mass%, the balance is water atomized alloy steel powder composed of Fe and inevitable impurities, and the addition amount of the alloy powder is added to the entire iron-based powder mixture. On the other hand , an iron-based powder mixture characterized by Cu powder: 1 to 3 mass% and graphite powder: 0.5 to 1.0 mass% .   The iron-based powder mixture according to claim 1, wherein the additive further contains a metal soap. A method for producing an iron-based powder molded body, wherein the iron-based powder mixture according to claim 1 or 2 is filled in a mold and molded at a temperature of less than 100 ° C. An iron-based powder characterized in that the iron-based powder mixture according to claim 1 or 2 is filled in a mold and molded at a temperature of less than 100 ° C, and then the obtained iron-based powder compact is sintered. A method for producing a sintered body.