JP4401326B2 - Method for producing high-strength wear-resistant aluminum sintered alloy - Google Patents

Description

  The present invention relates to a method for producing a sintered aluminum part having high strength and wear resistance suitable as various sliding members such as a connecting rod and a piston, and in particular, a high strength with improved tensile strength and elongation as well as wear resistance. The present invention relates to a method for producing a strong and wear-resistant aluminum sintered alloy. In this specification, Al, Zn, Mg, and the like are element symbols.

  In recent years, the demand for aluminum sintered parts by powder metallurgy has been increasing because they are lightweight and have properties such as strength and wear resistance that cannot be obtained with melted materials. For example, in a cast alloy containing a large amount of Si, only an alloy having a metal structure with coarse primary crystal Si can be obtained, but in a sintered aluminum alloy, an Al—Si based alloy phase in which fine primary crystal Si is dispersed and primary crystal Si are obtained. An aluminum sintered alloy (Patent Documents 1 to 4), which has a metal structure in which an Al solid solution phase not containing aluminum is dispersed in a patch shape and is excellent in strength and wear resistance, has been put into practical use. Although these aluminum sintered alloys are excellent in wear resistance, their strength is limited to about 360 MPa even when forging or heat treatment is applied. Abradable aluminum sintered alloys are desired.

  For this reason, the present inventors have developed and filed a method for producing a 7000 series aluminum alloy known as ultra-super duralumin by a powder metallurgy method (Japanese Patent Application No. 2004-206957), and further, based on this alloy, hard particles By adding, a sintered aluminum alloy having high strength and wear resistance has been developed and applied (Japanese Patent Application No. 2004-207586, hereinafter referred to as a prior application). The high-strength wear-resistant aluminum sintered alloy of the prior application has a mass ratio of Zn: 3.0 to 10%, Mg: 0.5 to 5.0%, Cu: 0.5 to 5 0.0, hard particles: 0.1 to 10% by mass, and the balance is made of aluminum, and presents a metal structure in which hard particles are dispersed in an aluminum alloy matrix in which intermetallic compounds are precipitated and dispersed ( A high strength wear-resistant aluminum sintered alloy having high tensile strength of about 450 to 520 MPa (Example) and high wear resistance. In addition, in the prior application, as a manufacturing method for obtaining the above-mentioned high-strength wear-resistant aluminum sintered alloy, an aluminum powder, a hard particle powder, and a simple powder of zinc, magnesium, copper, or zinc, magnesium and copper It is described that a raw material powder to which at least two kinds of alloy powders or a mixed powder thereof is added is used.

Japanese Patent Laid-Open No. 4-365832 JP-A-7-197168 JP-A-7-197167 JP-A-7-224341

  The high-strength wear-resistant aluminum sintered alloy of the previous application mentioned above is particularly excellent in mechanical strength and wear resistance as described above, but the high-strength wear-resistant aluminum sintered alloy disclosed therein is disclosed. The manufacturing method of the bond gold uses Zn which is volatile at the time of sintering in the form of zinc powder, so the amount of Zn in the sintered aluminum alloy obtained after sintering is not stable, and the amount of Zn tends to vary. ing. Zn precipitates as an intermetallic compound in the aluminum alloy matrix and contributes to the improvement of mechanical strength. Therefore, if the amount of Zn varies, the mechanical strength of the sintered aluminum alloy obtained after sintering also varies. It becomes. For this reason, if the above-mentioned aluminum alloy is applied to a specific product, it must be designed with the lower limit of variation in mechanical strength in consideration of product safety, and the high-strength wear-resistant aluminum There was a drawback that it was difficult to fully exhibit the properties of the bond gold.

  Therefore, the object of the present invention is to improve the mechanical strength of the method for producing a high-strength wear-resistant aluminum sintered alloy disclosed in the last-mentioned prior application, in particular by devising a structure that can stably supply Zn. The purpose is to enable mass production of aluminum sintered alloys with small variations.

In order to solve the above problems, the method for producing a high-strength wear-resistant aluminum sintered alloy according to the present invention prevents the volatilization of Zn and stably supplies Zn by giving the total amount of Zn in the form of aluminum alloy powder. At the same time, the fact that the lowering of the compressibility of the raw material powder due to the alloying of Zn is suppressed by using 15% by mass or more of aluminum powder in the raw material powder is essential.
That is, in the method for producing a high-strength wear-resistant aluminum sintered alloy of the present invention, the component composition of the entire raw material powder is, by mass ratio, Zn: 3.0 to 10%, Mg: 0.5 to 5.0% Cu: 0.5 to 5.0%, hard particles: 0.1 to 10%, the balance is made of inevitable impurities and Al, and contains 15% by mass or more of aluminum powder as a raw material, and the total amount of Zn Using at least an aluminum alloy powder and 0.1 to 10% by mass of hard particle powder, mixing the raw material powder, and using the raw material powder obtained by the raw material powder blending step, the desired After filling the metal mold of the shape, a molding step of compacting at a molding pressure of 200 MPa or more, and a compact obtained in the molding step in a non-oxidizing atmosphere, sintering holding temperature: 580 to 610 ° C, sintering holding time: 1 After sintering for more than minutes, the sintering process is cooled to room temperature, and the sintered body obtained in the sintering process is heated to 460-490 ° C. and water-quenched to form a solution. A heat treatment step of aging precipitation by holding at 200 ° C. for 2 to 28 hours is performed in order.

  In the manufacturing method of the present invention described above, a cold forging process in which the sintered body that has undergone the sintering process is cold forged at an upsetting rate of 3 to 40% at room temperature, or 100 Upsetting rate at ˜450 ° C .: After performing the forging step by any one of hot forging steps in which hot forging is performed at an upsetting rate of 3 to 70%, the heat treatment step is performed (claim 2), The aluminum alloy powder is Zn: 10 to 30% by mass, the balance is made of Al and inevitable impurities (Claim 3), and the aluminum alloy powder further contains Cu: 10% by mass or less (Claim 4). The hard particle powder has a hardness of 1000 Hv or more and does not react with aluminum (Claim 5), and the hard particle powder is at least one of silicon carbide powder, chromium boride powder, and boron carbide powder. In (Claim 6) In the raw material powder, 0.01 to 0.5% by mass of Sn simple powder, Bi simple powder, In simple powder, and Sn, based on the total composition of the raw material powder, At least one powder of a eutectic compound powder and a monotectic compound powder containing either Bi or In as a main component and generating a eutectic liquid phase of the main component is further added and mixed (Claim 7), The size of the aluminum powder and the aluminum alloy powder is 100 mesh or less, the size of the hard particle powder is 125 mesh or less, and the size of the other powder is 200 mesh or less (claim 8), the sintering step The non-oxidizing atmosphere is preferably a nitrogen gas atmosphere having a dew point of −40 ° C. or lower.

  The production method of the present invention has a high tensile strength and elongation in which hard particles are dispersed based on a 7000 series aluminum sintered alloy known as ultra-super duralumin, and has high wear resistance and excellent high strength resistance. This is a method for producing a wearable aluminum sintered alloy. By applying Zn, which is particularly volatile, in the form of alloy powder, the amount of Zn in the aluminum sintered alloy is stabilized and the variation in mechanical strength is small. A high-strength, wear-resistant aluminum sintered alloy can be reliably obtained.

(1) Raw material powder blending step (1) -1 Component composition of the entire raw material powder Zn:
Zn has the effect of increasing the strength by being precipitated together with Mg as MgZn ₂ (η phase) or Al ₂ Mg ₃ Zn ₃ (solid phase) in the Al matrix. Also, Zn is applied in the form of Al-Zn alloy powder, but the Al-Zn liquid phase generated from the Al-Zn alloy powder at the time of temperature rise during sintering wets the surface of the aluminum powder and the oxide film on the surface. And is diffused in the aluminum matrix and has an action of promoting bonding by diffusion of aluminum powders. If the Zn content is less than 3% by mass, the above-described effects cannot be obtained sufficiently and the effect of improving the strength becomes poor. On the other hand, if the amount exceeds 10% by mass, the amount of Zn or Zn-based eutectic liquid phase during sintering becomes excessive, making it impossible to maintain the shape, and the excessively Zn content in the aluminum base is a Zn-rich phase. Remains as. Moreover, when Zn becomes large quantity, it will become easy to volatilize, and the inside of a furnace will be contaminated and deposited. Therefore, Zn content shall be 3-10 mass%.

Mg:
Mg contributes to the improvement of strength by forming the above-mentioned precipitated compound together with the above-mentioned Zn. Mg also has a low melting point and has a function of generating a liquid phase during the temperature rising process during sintering, removing the oxide film, and promoting the progress of sintering. If the content of Mg is less than 0.5% by mass, the above effect is poor, and if it exceeds 5.0% by mass, the liquid phase becomes excessive and the shape cannot be maintained. Therefore, Mg content shall be 0.5-5.0 mass%.

Cu:
Cu is dissolved in the Al matrix and precipitates CuAl ₂ (θ phase) to contribute to improvement of strength, and also has a function of generating a liquid phase during sintering and promoting the progress of sintering. If the Cu content is less than 0.5% by mass, the above-described effect cannot be obtained sufficiently. If it exceeds 5.0% by mass, an unnecessary Cu—Zn alloy phase is formed with Zn, and along the grain boundary. Therefore, the Cu content is set to 0.5 to 5.0% by mass.

Hard particles:
In general, the addition of a hard phase to an alloy matrix causes a decrease in the strength and elongation of the alloy. However, since the base aluminum alloy matrix is alloyed with the above elements to form a high-strength aluminum sintered alloy, Even if the strength and elongation are slightly reduced by the addition, extremely high strength and elongation are exhibited as compared with a conventional aluminum-silicon wear-resistant aluminum sintered alloy or the like. Moreover, in this invention, it has the advantage that the kind and quantity of the hard particle to disperse | distribute can be easily changed with sliding conditions (especially sliding partner). For example, a conventional aluminum-silicon wear resistant aluminum sintered alloy disperses primary crystal Si as hard particles, but when the sliding partner is an iron-based material, the friction coefficient depends on the affinity between Fe and Si. Tends to be high. However, in the aluminum sintered alloy of the present invention, for example, by selecting hard particles having low affinity with Fe such as chromium boride, it is possible to reduce the friction coefficient and improve the wear resistance. is there.

  Since the addition amount of hard particles is 0.1% by mass or more, the effect of improving the wear resistance becomes remarkable. On the other hand, when the addition amount of hard particles exceeds 10% by mass, the decrease in strength and elongation becomes remarkable. It is necessary to add 1 to 10% by mass of the hard particles. Moreover, since hard particle | grains will raise | generate a plastic flow and a wear resistance will fall when hardness is low, a thing with a hardness of 1000 Hv or more is preferable.

Sn, Bi, In:
Sn, Bi, and In have a low melting point, generate a liquid phase during sintering, get wet on the surface of the aluminum powder, remove the oxide film on the surface of the aluminum powder, and promote the progress of sintering between the aluminum powders. At the same time, it has the effect of contributing to densification by shrinking the liquid phase due to the surface tension of the liquid phase, and therefore it is preferable to use it together with the above Zn, Mg, Cu as a sintering aid. This densification effect by the liquid phase is more advanced when the liquid phase is present for a long time, so the liquid phase is generated earlier in the sintering process, and most of the sintering process remains in the liquid phase. , The effect is greater. Therefore, Sn (melting point: 232 ° C.), Bi (melting point: 271 ° C.), and In (melting point: 155.4 ° C.), which have a low melting point and hardly dissolve with the main component Al, are very suitable in this respect.

  Further, it is more preferable to use an eutectic compound containing these elements as a main component and to generate a eutectic liquid phase of the main component because the melting point becomes lower than that of a simple substance. This eutectic liquid phase may be a eutectic liquid phase of a main component (Sn, Bi, In) and another element, or a eutectic liquid phase of a main component and an intermetallic compound of the main component and another element. But you can. In addition, some of the orthorhombic compounds have eutectic reaction lines, and orthorhombic compounds that generate such eutectic liquid phases of Sn, Bi, and In can also be used. Examples of elements that form such a eutectic liquid phase with Sn include Ag, Au, Ce, Cu, La, Li, Mg, Pb, Pt, Tl, and Zn, and Bi and such an eutectic liquid phase. Examples of the elements forming Ag include Ag, Au, Ca, Cd, Ce, Co, Cu, Ga, K, Li, Mg, Mn, Na, Pb, Rh, S, Se, Sn, Te, Tl, Zn, and the like. There are Ag, Au, Ca, Cd, Cu, Ga, Sb, Te, Zn, and the like as elements that form such a eutectic liquid phase with In. The above is an example of a simple binary system, but even in the case of a ternary system or a quaternary system or more, Sn, Bi, and In are similarly used as main components, and the eutectic liquid phase of this main component is used. The same effect can be obtained with a composition that generates odor. However, among these elements, Pb and Cd also generate eutectic liquid phases with Sn, Bi, and In, but it is preferable not to use them from the viewpoint of toxicity.

  Including the above viewpoints, it is preferable to use lead-free solder, which has been developed in recent years, as a eutectic alloy mainly composed of multi-element Sn, Bi, and In. Lead-free solder includes Sn-Zn, Sn-Bi, Sn-Zn-Bi, Sn-Ag-Bi, etc., and small amounts of In, Cu, Ni, Sb, Ga, Ge, etc. Some metal elements have been proposed, and some of them have been put to practical use. Such a commercially available lead-free solder is preferable because it is easily available.

  The effect of these sintering aid powders becomes remarkable when 0.01% by mass or more is added. On the other hand, Sn, Bi, and In do not dissolve in Al, so when used in a large amount, they precipitate at the grain boundaries and cause a decrease in strength. When 0.5% by mass or more is added, the strength reduction due to precipitation of Sn, Bi, and In grain boundaries exceeds the effect of densification due to the liquid phase shrinkage, and the strength is reduced.

1- (2) Powder form Aluminum alloy powder and aluminum powder:
Since the above Zn is an element that easily volatilizes at a high temperature, when it is given as a simple powder, the amount of Zn remaining due to the volatilization of Zn is not constant, and variations due to products increase. For this reason, in this invention, volatilization of this Zn is prevented by alloying the whole quantity of Zn with aluminum, and providing with the form of aluminum alloy powder.

  However, Zn hardens the aluminum powder and lowers the compressibility, so when alloying with all of the aluminum content, the compressibility of the raw material powder decreases, so soft aluminum powder is added to the aluminum alloy powder containing the entire amount of Zn. It is necessary to mix and improve compressibility. In this case, the amount of aluminum powder added must be 15% by mass or more.

  If the aluminum alloy powder containing Zn has a composition such that an Al—Zn liquid phase is generated at a low temperature, Zn is more easily volatilized than the Al—Zn liquid phase, so that the temperature is as high as possible, that is, the final stage of the sintering process. It is desirable that the composition be such that an Al—Zn liquid phase is generated. In addition, when an aluminum alloy powder containing a large amount of Zn is used, the amount of aluminum powder is relatively increased. As a result, the dispersion of Zn is likely to be non-uniform in the aluminum alloy matrix, resulting in variations in mechanical properties. Become. For these reasons, the amount of Zn in the aluminum alloy powder is desirably 30% by mass or less. On the other hand, if the amount of Zn in the aluminum alloy powder is less than 10% by mass, the difference in Zn concentration from the aluminum powder is reduced, making it difficult to uniformly diffuse. Therefore, the amount of Zn in the aluminum alloy powder is desirably 10 to 30% by mass.

Application form of Mg and Cu:
Using an aluminum alloy powder having a composition that does not generate a liquid phase at a high temperature as described above is good in terms of preventing Zn volatilization, but is disadvantageous in terms of uniform diffusion of components. Therefore, by using Cu or Mg together, it is possible to achieve uniform diffusion of Zn into the base. Cu and Mg generate Zn and Cu-Zn liquid phase or Mg-Zn liquid phase in the aluminum alloy during the heating process of sintering, and these liquid phases are absorbed by the aluminum powder or aluminum alloy powder. As a result, the solidification is rapidly progressed by repeating the solidification immediately. Further, since the liquid phase at this time is immediately solidified, the problem of volatilization of Zn does not occur. Cu or Mg having such an action may be applied in the form of a simple powder, an alloy powder of both, or an alloy powder with aluminum, but Cu: 10 mass% or less is added to the aluminum alloy powder containing Zn. If it is given at the same time, the above effect is further enhanced. If the amount of Cu applied to the aluminum alloy powder exceeds 10% by mass, the liquid phase generation temperature with Zn moves to the high temperature side, which is disadvantageous in terms of uniform diffusion of components.

Form of Sn, In, Bi assignment:
When Sn, Bi, or In is used, it is added in the form of a simple powder or a eutectic alloy powder or a monotectic alloy powder in which a eutectic liquid phase of these components is generated as described above.

Hard particle powder:
As a method for dispersing the hard particles in the aluminum alloy matrix, a method of adding and giving hard particle powder is simple. In addition, the amount of hard particles added to the raw material powder is suitably 1 to 10% by mass as described above, but if the hard particles react with Al which is the main component of the matrix, after sintering, It becomes difficult to control the amount of hard particles dispersed in the aluminum alloy matrix and the particle size range. For this reason, it is preferable to add hard particles that do not react with aluminum as powder.

  As such hard particle powder, silicon carbide, chromium boride, boron carbide and the like are preferable because they are extremely hard substances and do not react with aluminum. These hard particle powders, which are extremely hard hard particles, are embedded in the aluminum alloy base during sliding because the aluminum alloy base serving as a base is somewhat soft, so that the wear of the sliding counterpart member is suppressed, and aluminum Suppresses plastic flow in the alloy base and contributes to improved wear resistance. Moreover, even if it falls off from the aluminum alloy base during sliding, it is immediately embedded in the soft aluminum alloy base, and the effect of preventing the base plastic flow is achieved.

1- (3) Size of powder In order for the above-described action of each component element to work uniformly in the base, it is necessary to uniformly diffuse each component element in the base. For this reason, these component element powders need to be applied in the form of fine powder of 200 mesh or less (size that passes through a 200-mesh (74 μm) sieve comb). The plain powder or alloy powder melts at the time of sintering temperature rise, becomes a liquid phase, gets wet on the surface of the aluminum powder, removes the oxide film on the surface, diffuses into the aluminum matrix, and diffuses between the aluminum powders However, if the size of the simple powder or alloy powder exceeds 200 mesh, local segregation occurs and the uniform diffusion of the constituent elements is hindered.

  On the other hand, if the powder is fine up to aluminum powder, the fluidity of the raw material powder decreases, so it is preferable to use a larger aluminum powder than the above component element powders. However, when it exceeds 100 mesh (powder having a size remaining on a 100-mesh (140 μm) sieve comb), each component element is difficult to diffuse to the center of the powder, and segregation of components occurs. It is necessary to use a powder having a mesh size (size passing through a sieve mesh of 100 mesh (140 μm)).

  Since the hard particle powder hardly reacts with the matrix, the added powder is dispersed as it is in the aluminum alloy matrix. For this reason, the hard particle powder may be determined by the particle size of the hard particles dispersed in the aluminum alloy matrix. The average particle size of the hard particles dispersed in the aluminum alloy matrix is preferably 1 to 100 μm. If the hard particles are finer than 1 μm, when the base is plastically flowed, it is easy to plastically flow with the base and it is difficult to stop the plastic flow of the base. On the other hand, when the average particle size of the hard particles exceeds 100 μm, although depending on the sliding conditions, it is not preferable because it tends to cause wear of the sliding counterpart member during sliding and a tendency to decrease strength. Therefore, in order to uniformly disperse the hard particles having the above average particle size range in the aluminum alloy base, the hard particle powder does not react with aluminum and passes through a sieve comb of 125 mesh or less (125 mesh (113 μm)). It is preferable to use (size) powder.

(2) Molding process:
In this step, the raw material powder obtained in the raw material powder blending step is filled into a mold having a desired shape and then compacted with a molding pressure of 200 MPa or more. Thereby, the molded object whose density ratio is 90% or more is obtained. When the molding pressure is less than 200 MPa, the density of the molded body becomes low, and even after the subsequent sintering process and forging process, 2% by volume or more of pores remain and high strength and elongation cannot be obtained. Moreover, it is not preferable because the dimensional change during sintering becomes large. A higher molding pressure is preferable because the density of the molded body is higher, and a pressure of 400 MPa or higher is more preferable because a molded body having a density ratio of 95% or higher can be obtained. However, if it exceeds 500 MPa, adhesion of aluminum powder to the mold tends to occur, such being undesirable.

(3) Sintering process:
In this process, Zn contained as a component is an element that has a low melting point and is likely to volatilize. However, when a large amount of liquid phase is generated during sintering, the shrinkage of the sintered body increases and the dimensional accuracy decreases. If volatilized, the amount of Zn dissolved in the base will decrease and the desired strength and elongation will not be obtained, and the sintering atmosphere will be contaminated and deposited in the sintering furnace, which will cause problems in the working environment. Will occur. In order to avoid such an adverse effect, it is necessary to rapidly raise the temperature to the sintering holding temperature.

  That is, in sintering the molded body obtained in the molding step, in the temperature rising process from room temperature to the sintering holding temperature, at least the temperature from 400 ° C. or more near the melting point of zinc to the sintering holding temperature. By rapidly heating the region at a heating rate of 10 ° C./min or more, the volatilization of the component elements is suppressed, and sintering holding temperature: 580 to 610 ° C., sintering holding time: sintering at 10 minutes or more Thus, uniform diffusion of the component elements can be achieved while suppressing an excessive decrease in dimensional accuracy due to the generation of the liquid phase. This sintering requirement is that if the rate of temperature rise to the sintering temperature is less than 10 ° C./min, the problem of volatilization of Zn described above becomes significant, and even if the sintering temperature exceeds 610 ° C., the volatilization of Zn This is because the problem of excessive shrinkage due to the liquid phase becomes prominent, and in this case, crystal grains grow and become coarse to reduce the strength. On the other hand, in order to uniformly dissolve each component element in the Al base, it is necessary to set the sintering temperature to 580 ° C. or more and the sintering holding time to 10 minutes or more. Below this condition, the diffusion of each component into the Al matrix becomes insufficient and the strength decreases.

  Since each component is in a solid solution state due to the sintering, the cooling rate is not particularly limited. However, when slow, particularly in a high temperature region (450 ° C. or higher), coarsening of crystal grains proceeds, During the cooling process, supersaturated components are precipitated along the grain boundaries, reducing the strength and elongation, and by the subsequent heat treatment (solution treatment), the generated supersaturated components are absorbed into the base and pores are generated. Accordingly, the high temperature region is preferably cooled as soon as possible, and the cooling rate in the temperature region of 450 ° C. or higher is preferably about −10 ° C./min.

  A non-oxidizing atmosphere is suitable for the sintering atmosphere, but a nitrogen gas atmosphere with a dew point of −40 ° C. or lower is most suitable. The dew point is an index indicating the amount of moisture in the atmospheric gas. When the moisture, that is, the amount of oxygen is large, Al easily binds to oxygen, so that the progress of sintering is inhibited and densification is inhibited. Nitrogen gas is preferable because it is cheaper and safer than other non-oxidizing gases.

  Thus, by performing liquid phase sintering, it is possible to obtain a sintered body in which the constituent elements are uniformly dissolved in the Al matrix and the remaining pores are closed pores at a density ratio of 95% or more.

(4) Heat treatment (T6 treatment) step:
In the production method of the present invention, the heat treatment (T6 treatment) step comprises heating the precipitated phase in the Al matrix to 460 to 490 ° C. to form a solid solution uniformly in the matrix, and then quenching by water quenching to supersaturated solid solution. And a aging precipitation treatment in which the precipitation phase (intermetallic compound) is precipitated and dispersed from the supersaturated solid solution while being kept at 110 to 200 ° C. for 2 to 28 hours. If the solution treatment temperature is less than 460 ° C., all precipitated components are not uniformly dissolved in the Al matrix. On the other hand, if the temperature exceeds 490 ° C., the effect does not change. Will occur. Also, in the aging treatment, when the temperature is less than 110 ° C. and when the time is less than 2 hours, sufficient precipitated compounds cannot be obtained, and when the temperature exceeds 200 ° C. and the time exceeds 28 hours. In this case, the precipitated compound grows and becomes coarse, resulting in a decrease in strength. The temperature and time are appropriately combined with the required characteristics within the above range. By performing the heat treatment in this way, a metal structure in which intermetallic compounds such as MgZn ₂ (η phase), Al ₂ Mg ₃ Zn ₃ (minor phase), CuAl ₂ (θ phase) are precipitated and dispersed in the aluminum alloy matrix is obtained. And mechanical properties are improved.

  The high-strength wear-resistant aluminum sintered alloy obtained as described above has a density ratio of 95% or more and a tensile strength as high as 450 MPa or more, as is clear from the following examples. Although the same elongation and wear resistance are exhibited, the following forging process can be added between the sintering process and the heat treatment process when further improvement in tensile strength and elongation is desired.

(5) Forging process:
In this process, cold forging a sintered body having a density ratio of 95% or more obtained up to the above-described sintering process at room temperature with an upsetting ratio of 3 to 40%. Sintered aluminum with high tensile strength and elongation by hot forging at a forging process or at an upsetting rate of 3 to 70% at 100 to 450 ° C. and a density ratio of 98% or more. Forged parts can be obtained.

  By the way, in general, it is known to increase the density by the forging process, but simply increasing the density closes the pores and does not bind metallicly, so that the material surface cracks during forging, Strength and elongation cannot be improved due to residual defects inside the product. Therefore, in order to obtain high strength and elongation, not only the pores but also the metal bonds must be formed there. In order to obtain such a metal bond, forging is generally performed in two steps: a forging process for densification and a deformation process for obtaining a metal bond by deforming a densified material. Has been done. In the present invention, in order to obtain a metal bond, the sintered body obtained as described above was pressed from above and below to compress the height to close the pores, and was provided transversely to the pressing direction. By using upset forging that deforms while forcibly bonding the original pores (blocked but not metal-bonded) by flowing the material into the space, this is done in two conventional processes. The forging process is integrated into one process. The deformation rate of the material in the pressing direction is the upsetting rate. In the forging process, if such upset deformation is the main, it may be locally extruded, and the forging of the present application includes the backward extrusion method. In addition, in the case of indentation forging and forward extrusion, the material is reduced in surface by the mold, but the pressing direction at this time is the circumferential direction, and the deformation direction of the material is the extrusion direction, that is, the direction orthogonal to the pressing direction. Therefore, it is included in the scope of the present invention. Moreover, by setting it as such forging, in addition to the said effect | action, while refine | miniaturizing the crystal grain which grew at the time of sintering, the effect | action which parting a precipitate is also acquired, and an intensity | strength and elongation are improved further.

  In the case of cold forging, it is necessary to forge so that the upsetting rate is 3 to 40%. In forging with the same diameter or expanding diameter, if the upsetting rate is less than 3%, only local deformation occurs, the residual amount of pores increases, and the strength and elongation cannot be increased. Also, when pushing into a mold having a small diameter, such as indentation forging, upsetting of 3% or more is required for the above reason. In addition, it is more preferable that the upsetting rate is 10% or more because the density ratio of the forged body can be easily 98% or more. On the other hand, if the upsetting rate exceeds 40%, forging cracks accompanying crystal slip are likely to occur. In the case of cold forging, if the forging process is performed so that the end of the material expanded in the transverse direction is in full contact with the inner wall of the mold at the end of forging, the accuracy of the product dimensions and shape is stabilized. At the same time, it is preferable because defects are unlikely to remain on the outermost surface.

  In the case of hot forging, if the material (sintered body) is heated in the temperature range of 100 to 450 ° C., preferably 200 to 400 ° C., the upsetting rate can be in the range of 3 to 70%. Become. If the heating temperature of the material (sintered body) is less than 100 ° C., it is not much different from the case of cold forging, the deformability of the material is poor, and the upsetting rate cannot be increased. Moreover, it is preferable that the heating temperature of the material (sintered body) is 200 ° C. or higher because the material is softened and deformed to increase the forging pressure when performing hot forging at a desired upsetting rate. On the other hand, when the temperature exceeds 450 ° C., the adhesion between the mold and the material (sintered body) remarkably occurs, so the upper limit needs to be stopped at 450 ° C., preferably 400 ° C. However, forging cracks are likely to occur if the upsetting rate exceeds 70% even in the above temperature range. In the case of hot forging, it is preferable to perform upset forging so that the end of the material expanded in the transverse direction in the forging process is in contact with the inner wall of the mold at the end of forging because defects on the outermost surface are less likely to occur.

  The high-strength wear-resistant aluminum sintered alloy obtained as described above has a density ratio of 98% or more, a tensile strength of 500 MPa or more, and elongation is improved, as is apparent from the following examples. 2% or more, and it has excellent mechanical properties that are not present in the past as well as excellent wear resistance.

  Example 1 compares the case where Zn is given in the form of an aluminum alloy powder and the case where Zn is given in the form of a single powder. Specifically, in the raw material powder blending step, 100 mesh aluminum powder and aluminum alloy powder having a Zn content of 12% by mass, 125 mesh boron carbide powder as hard particle powder, and 250 mesh zinc powder, magnesium powder, Copper powder and tin powder were prepared, and these powders were mixed in the composition shown in Table 1. The component composition of the raw material powder was Zn: 5.5%, Mg: 2.5%, Cu: A raw material powder having 1.5%, Sn: 0.1%, hard particles (boron carbide): 5.0%, and the balance being Al and inevitable impurities was prepared.

  In the molding step, the raw material powder was used, and the molding pressure was set to 300 MPa, and compacted into a columnar shape of φ40 × 28. In the sintering process, these green compacts are heated in a nitrogen gas atmosphere in a temperature range from 400 ° C. to the sintering holding temperature at a heating rate of 10 ° C./min, and the sintering holding temperature: 600 ° C. for 20 minutes. After holding and sintering, the temperature range from the sintering holding temperature to 450 ° C. was cooled at a cooling rate of −20 ° C./min. In the forging process, the sintered body sample thus obtained was heated to 400 ° C. and placed in a mold heated to the same temperature, and hot forging with an upsetting rate of 40% was performed. After heating the obtained forged body to 470 degreeC and performing solution treatment, the heat treatment process which hold | maintains at 130 degreeC for 24 hours and performs an aging precipitation process was performed.

  In the evaluation, for the obtained samples 01 and 02, φ40 × 28 columnar shape samples were each processed into five tensile test pieces, a tensile test was performed, and tensile strength and elongation were measured. The results are shown in Table 2 as average values and 3σ. In addition, two friction test pieces cut out from a columnar shape sample and processed into a shape of φ7.98 × 20 were used, and an S45C heat treatment material was used as a sliding mating member in a pin-on-disk friction wear tester. A sliding test is performed at a sliding speed of 5 m / sec for 30 minutes while supplying engine oil in a state where a load is applied. If no sudden increase in the dynamic friction coefficient is observed during this test, replace the test piece and change the load. Table 2 also shows the load at which the dynamic friction coefficient is increased rapidly in increments of 5 MPa as the surface pressure load (limit surface pressure). Furthermore, in the above sample preparation, the density ratio (average value) was measured for each of the molded body after the molding process, the sintered body after the sintering process, and the forged body after the forging process. The results are also shown in Table 2.

  From Tables 1 and 2, the tensile strength is slightly more in the case where Zn is applied in the form of an alloy powder with Al (sample number 01) than in the case where Zn is applied in the form of a simple powder (sample number 02). It can be seen that the variation is high and the variation is small. It can also be seen that the elongation is slightly improved and the variation is kept small. This is considered to be due to the fact that the volatilization of Zn can be prevented by applying easily volatile Zn in the form of alloy powder, and the amount of Zn in the sample is stabilized. On the other hand, it can be seen that the surface load resistance is equivalent. From this example, it was confirmed that by applying Zn in the form of an alloy powder, the tensile strength and elongation can be improved and variation can be suppressed without causing a reduction in the surface pressure load.

  In Example 2, as the raw material powder blending step, aluminum powder of 100 mesh or less, and aluminum alloy powder having the composition shown in Table 3, magnesium powder, copper powder, and tin powder as low melting point metal powder of 250 mesh or less, respectively. And boron carbide powder of 125 mesh or less as hard particle powder, and mixed at a blending ratio shown in Table 3 to produce a raw material powder. Under the same conditions as in Example 1, the molding process, sintering process, forging Through the steps and the heat treatment step, samples having the overall composition shown in Table 4 were produced.

  In the above sample preparation, as in Example 1, the density ratio is measured and the tensile strength and the elongation are measured for the molded body after the molding process, the sintered body after the sintering process, and the forged body after the forging process. The surface pressure load (limit surface pressure) was measured, and the test results are shown in Table 5. In Tables 3 to 5, the ruled line is displayed thickly for each survey item, and the sample number 01 common to each survey item (Example 1) is reprinted and marked for each item. .

  By comparing the samples Nos. 01 and 03 to 08 in Tables 3 to 5, the influence of the addition amount of the aluminum powder was examined. In the samples of sample numbers 03 and 04 where the amount of aluminum powder added is less than 15% by mass, the amount of Zn in the total composition of the raw material powder exceeds 10% by mass, resulting in a liquid generated from the aluminum alloy powder. The deformation of the sintered body was large due to the phase, and the subsequent processes had to be stopped. On the other hand, when the addition amount of aluminum powder is 15% by mass or more, sintering can be performed without causing deformation of the sintered body, and high tensile strength, elongation, and surface pressure load are exhibited. From this, it was confirmed that when applying the total amount of Zn in the form of aluminum alloy powder, it is necessary to simultaneously use 15% by mass or more of aluminum powder. Further, when aluminum powder is added in excess of 15% by mass, the tensile strength and elongation tend to improve as the amount of aluminum powder added increases. When the amount exceeds 5.5% by mass (Sample No. 01), the tensile strength tends to decrease on the contrary, and in the sample No. 08 whose Zn content in the entire composition of the raw material powder is less than 3% by mass, As a result of the poor amount, a decrease in tensile strength and surface load resistance was observed.

  By comparing the samples Nos. 01 and 09 to 14 in Tables 3 to 5, the influence of the Zn content in the aluminum alloy powder was examined. In these comparisons, the Zn content in the overall composition of the raw material powder was adjusted to be constant (5.5% by mass). From these samples, the sample No. 09 whose Zn content in the aluminum alloy powder is less than 10% by mass shows a high tensile strength but a low elongation value of 0.7%. . On the other hand, it can be seen that when the Zn content in the aluminum alloy powder is 10% by mass or more, the tensile strength is high and the elongation value is also improved. However, when the amount of Zn in the aluminum alloy powder exceeds 30% by mass (Sample No. 14), a decrease in tensile strength and a decrease in elongation are observed. Moreover, although the surface pressure load shows a favorable surface pressure load when the Zn content in the aluminum alloy powder is in the range of 10 to 30% by mass, a decrease in the surface pressure load is recognized when the amount exceeds 30% by mass. Therefore, it was confirmed that the amount of Zn in the aluminum alloy powder is in the range of 10 to 30% by mass, and the tensile strength, elongation, and surface load resistance are high.

  In the optimum range of the amount of Zn in the aluminum alloy powder confirmed as described above, the lower limit value of Zn in the entire composition of the raw material powder was confirmed by the sample number 15 and the upper limit value was confirmed by the sample of the sample number 16. In addition, it was confirmed that Zn in the entire composition of the raw material powder exhibited high tensile strength, elongation and surface pressure load in the range of 3 to 10% by mass.

  Example 3 investigated the addition amount and the addition form of Mg and Cu, and together with the aluminum powder, aluminum alloy powder, magnesium powder, copper powder, tin powder boron carbide powder of Example 1, 100 mesh each of Table 6 Using the aluminum alloy powder having the composition shown in the following, and the aluminum-magnesium alloy powder consisting of Al and inevitable impurities with the remaining amount of Mg in the 250 mesh being 50% by mass, these powders are mixed at the blending ratio shown in Table 6, Raw material powders having the overall composition shown in Table 7 were prepared. Using these raw material powders, the molding step, sintering step, forging step, heat treatment step, test piece processing step are performed under the same conditions as in Example 1, and the obtained sample has a density ratio and tensile strength in each step. The elongation and the surface pressure load were measured. The results are shown in Table 8 together with the result (average value) of the sample No. 01 of Example 1.

  By comparing the samples Nos. 01, 17-19 and 21, 22 in Tables 6 to 8, the influence of the amount of Mg when Mg was given as a single unpowder was examined. When Mg is not added (Sample No. 17), a liquid phase involving Mg does not occur, and the tensile strength, elongation, and surface load resistance decrease, but Mg is provided in the form of a simple powder. When the amount of Mg is 0.5% by mass or more, it can be seen that the tensile strength, the elongation, and the surface pressure load are improved. However, in the sample of Sample No. 22 in which the Mg amount exceeds 5% by mass, the liquid phase generation amount is excessive, and the sintered body is deformed. From these, it was confirmed that the amount of Mg in the composition of the raw material powder has an effect of improving tensile strength, elongation, and load resistance against surface pressure in the range of 0.5 to 5% by mass.

  Sample No. 20 is an example in which Mg is applied in the form of an aluminum-magnesium alloy powder. Compared with the sample No. 01, when the amount of Mg in the entire composition of the raw material powder is equal, Mg is aluminum- It can be seen that even when applied in the form of magnesium alloy powder, the same tensile strength, elongation, and surface pressure load can be obtained.

  By comparing the samples Nos. 01 and 23 to 27 in Tables 6 to 8, the influence of the amount of Cu when Cu was given as a single powder was examined. When Cu is not added (Sample No. 23), a liquid phase involving Cu does not occur, and both the tensile strength and the surface pressure load are low, but Cu is applied in the form of a simple powder. In this case, it is understood that the tensile strength and the surface pressure resistance are improved when the amount of Cu is 0.5% by mass or more. However, in the sample of Sample No. 27 in which the amount of Cu exceeds 5% by mass, the liquid phase generation amount is excessive and the sintered body is deformed. On the other hand, the elongation tends to decrease as the amount of Cu increases. However, when the amount of Cu is up to 5% by mass, sufficient elongation of 1.0% or more is exhibited. From these, it is confirmed that the amount of Cu in the composition of the raw material powder has an effect of improving the tensile strength and the surface pressure load in the range of 0.5 to 5% by mass, and the elongation shows a sufficient value in this range. It was done.

  By comparing the samples of Sample Nos. 28 to 32 in Tables 6 to 8, the influence of the amount of Cu when Cu was applied in the form of an aluminum alloy powder containing Zn was examined. In this case, as in the case where Cu is applied in the form of a single powder, improvement in tensile strength and surface load resistance is observed from the sample without addition of Cu (Sample No. 23). Even if the amount is 0.5 to 5% by mass as confirmed above, if the amount of Cu in the aluminum alloy powder exceeds 10% by mass (Sample No. 32), the tensile strength and elongation may decrease instead. Recognize. From this, when Cu was alloyed and given to the aluminum alloy powder containing Zn, it was confirmed that the upper limit needs to be 10 mass%.

  In Example 4, the amount and type of hard particle powder added were investigated. 125 mesh silicon carbide each together with the aluminum powder, aluminum alloy powder, magnesium powder, copper powder, tin powder, and boron carbide powder of Example 1 was investigated. Using powder and chromium boride powder, these powders were mixed at the blending ratio shown in Table 9 to prepare raw material powder having the overall composition shown in Table 10. Using these raw material powders, the molding step, sintering step, forging step, heat treatment step, test piece processing step are performed under the same conditions as in Example 1, and the obtained sample has a density ratio and tensile strength in each step. The elongation and the surface pressure load were measured. The results are shown in Table 11 together with the result (average value) of the sample No. 01 of Example 1.

  Also, as conventional examples, aluminum powder of 100 mesh or less, and aluminum: Si: 20% by mass and the balance of Al-silicon alloy powder, each of Ni: 250 mesh or less of Ni: 4% by mass and the balance of copper of Cu— Nickel alloy powder and Mg: Aluminum-magnesium alloy powder containing 50% by mass and the balance being Al are prepared and mixed at a blending ratio shown in Table 1. The molding pressure is 200 MPa in the molding process, and nitrogen gas is used in the sintering process. In atmosphere, temperature rising rate from 400 ° C. to sintering holding temperature: 10 ° C./min, sintering holding temperature: 550 ° C., sintering holding time: 60 minutes, cooling rate from sintering holding temperature to 450 ° C .: − 20 ° C./minute, heating temperature of sintered body sample and forging mold: 450 ° C., upsetting rate: 40% in forging process, solution treatment temperature: 470 ° C. in heat treatment process, Effective precipitation treatment: as 130 ° C. × 24 hours to prepare the disclosed alloys in Patent Document 4 (JP-A-7-224341). For this sample (sample number 42), the density ratio, tensile strength, and mechanical properties of elongation in each step were measured, and the results are also shown in Table 11.

  By comparing the samples Nos. 01 and 33 to 40 in Tables 9 to 11, the effect of the addition amount of the hard particles can be examined. From these, it can be seen that the sample No. 33 to which no hard particles are added shows a high tensile strength and elongation, but is a material having a low surface pressure load and a low wear resistance. Even with such a material, by setting the amount of hard particles to 0.1% by mass or more, the wear resistance is improved while the decrease in tensile strength is slight, particularly 1.0% by mass or more. It can be seen that high wear resistance can be obtained by addition. On the other hand, the elongation tends to decrease slightly as the amount of hard particles increases, but it can be seen that the elongation value is 1% or more up to 10% by mass of the hard particles, indicating sufficient elongation. However, when the amount of hard particles exceeded 10% by mass (sample number 40), it was observed that the elongation value was less than 1% and the wear amount of the sliding counterpart member was increased. As described above, the amount of hard particles is in the range of 0.1 to 10% by mass, exhibits high tensile strength and elongation, improves wear resistance, and is a conventional aluminum-silicon wear resistant aluminum sintered alloy. It was confirmed that a wear-resistant aluminum sintered alloy having a higher tensile strength than that of (Sample No. 43) can be obtained. In particular, it was also found that the effect of improving the wear resistance is large when the amount of hard particles is in the range of 1.0 to 10% by mass.

  By comparing the samples Nos. 01, 41, and 42 in Tables 9 to 11, the influence of the type of hard particles can be examined. From these, it was confirmed that sufficient wear resistance (surface pressure load) can be obtained even if the kind of hard particles is changed from boron carbide to silicon carbide or chromium boride. In particular, when chromium boride is used, not only the tensile strength is higher than that of the conventional aluminum-silicon wear-resistant aluminum sintered alloy (Sample No. 43), but also the surface pressure load is equivalent. It has been found that an excellent wear-resistant aluminum sintered alloy can be obtained.

  In Example 5, the amount and type of the sintering aid powder were investigated, and together with the aluminum powder, aluminum alloy powder, magnesium powder, copper powder, boron carbide powder, and tin powder of Example 1, 250 mesh each. Bismuth powder, indium powder and Zn: 8% by mass, Bi: 3% by mass, and the remainder using lead-free solder powder composed of Sn and inevitable impurities, these powders were mixed at the blending ratio shown in Table 12, The raw material powder of the whole composition shown in 13 was prepared. Using these raw material powders, the molding step, sintering step, forging step, heat treatment step, test piece processing step are performed under the same conditions as in Example 1, and the obtained sample has a density ratio and tensile strength in each step. The elongation and the surface pressure load were measured. The results are shown in Table 14 together with the result (average value) of the sample No. 01 of Example 1.

  Here, the influence of the addition amount of the low melting point metal powder was examined using the samples Nos. 01 and 44 to 48 in Tables 12 to 14. As a result, it can be seen that when the low melting point metal is added, the tensile strength, the elongation and the surface pressure load are improved as compared with the case where the low melting point metal is not added (Sample No. 44). Moreover, the effect is recognized by the addition amount of 0.01-0.5 mass%, and although the effect is the highest when the addition amount is 0.05-0.1 mass%, it exceeds 0.5 mass% ( It can be seen from Sample No. 48) that the elongation is remarkably reduced and the surface pressure load is also reduced. Therefore, it was confirmed that the addition of the low melting point metal powder has an effect of improving the mechanical characteristics in the range of 0.01 to 0.5% by mass.

  In addition, the types of the low melting point metal powders were changed using the samples Nos. 01 and 49 to 51 in Tables 12 to 14, and the influence of the type of the low melting point metal powder was examined. As a result, it was confirmed that the same effect can be obtained even if the tin powder is replaced with bismuth powder, indium powder or lead-free solder powder.

  Example 6 investigated the case where the molding pressure was changed as the molding condition and the sintering temperature and the sintering time were changed as the sintering condition. The aluminum powder, the aluminum alloy powder used in the sample number 01 of Example 1, Using the raw material powder prepared by adjusting the magnesium powder, copper powder, and tin powder to the same component composition as in Example 1, the molding process and the sintering process were performed at the molding pressure, sintering temperature, and sintering time shown in Table 15. Thereafter, under the same conditions as in Example 1, a forging process, a heat treatment process, and a test piece processing process were performed. The samples thus obtained were measured for density ratio, tensile strength, elongation, and surface pressure load in each step. The results are shown in Table 16 together with the result (average value) of the sample No. 01 of Example 1.

  From the samples of sample numbers 01 and 52 to 55 in Tables 15 and 16, a molded body sample having a molding pressure in the range of 200 to 400 MPa and a density ratio of the molded body of 90% or more was obtained. -It turns out that high tensile strength, elongation, and surface load resistance are exhibited through the heat treatment step. On the other hand, in the sample of Sample No. 52 whose molding pressure is less than 200 MPa, since the density of the molded body is low, the amount of shrinkage due to the liquid phase generation is large, and the die forging is discontinued. Canceled. Further, when the molding pressure exceeded 400 MPa (Sample No. 55), mold galling occurred and the subsequent sintering process was stopped and the test was stopped.

  The influence of the sintering holding temperature was examined using samples Nos. 01 and 56 to 59 in Table 15 and Table 16. As a result, it can be seen that the samples Nos. 01, 57 and 58 having a sintering holding temperature in the range of 580 to 610 ° C. exhibit high tensile strength and elongation. On the other hand, in the sample of sample number 56 whose sintering holding temperature is less than 580 ° C., the tensile strength and the elongation are both low. It is presumed that this is because the component elements cannot be completely dissolved in the Al matrix, but are segregated locally and remain, resulting in low mechanical properties. On the other hand, in the sample of sample No. 59 having a sintering holding temperature exceeding 610 ° C., the liquid phase amount was excessively generated. As a result, the sintered body melted and deformed, and the subsequent tests were stopped.

  Further, the influence of the sintering holding time was examined using the sample numbers 01 and 60 to 63 in Table 15 and Table 16. As a result, in the sample of sample number 60 whose sintering time is less than 10 minutes, both the tensile strength and the elongation are low. This is presumed that when the sintering time of the component is short, it cannot be sufficiently dissolved in the Al matrix and segregates and remains locally, resulting in low mechanical properties. On the other hand, the samples Nos. 01 and 61 to 63 having a sintering time of 10 minutes or more are high machines in which the components are uniformly dissolved in the Al matrix, the tensile strength is 500 MPa or more, and the elongation exceeds 3%. Characteristics. However, even if the sintering holding time exceeds 30 minutes, the mechanical properties do not change, so a sintering holding time of 30 minutes or less is sufficient.

  In Example 7, as in Example 6, the raw material powder adjusted to the same component composition as in Example 1 was used using the aluminum powder, aluminum alloy powder, magnesium powder, copper powder, and tin powder of sample number 01 of Example 1. A sample was prepared under the same sample preparation conditions as in Example 1 except that the forging conditions were changed to the conditions shown in Table 17. Table 18 shows the results of measuring the density ratio, tensile strength, elongation, and surface pressure resistance load of these samples, together with the measurement results of the sample No. 01 of Example 1. In Table 17, the “forging temperature” column is labeled “room temperature” in the case of cold forging, and the heating temperature of the sintered body sample as the material in the case of hot forging. Moreover, the sample of the sample number 64 is a conventional example similar to Patent Document 1 in which forging is not performed.

  Here, the influence of the upsetting rate in the case of cold forging at room temperature was examined using samples Nos. 64-69 in Tables 17 and 18. As a result, in the case of cold forging, when the upsetting rate is in the range of 3 to 40%, it can be seen that high tensile strength, elongation, and surface load resistance can be obtained. On the other hand, when the upsetting rate exceeded 40% (Sample No. 69), the sample was cracked by forging, and the test was stopped.

  Moreover, the influence of the heating temperature at the time of carrying out hot forging by changing the heating temperature of a sintered compact with the sample number 68 (cold forging) of Table 17 and 18 and the samples of 01 and 70-75 was investigated. As a result, it can be seen that the values of tensile strength, elongation, and surface load resistance are improved by hot forging. This is because, in the case of cold forging, there are very few hair cracks inside the sample and the elongation is lowered, but there is no hair cracking by hot forging with a material heating temperature of 100 ° C. or higher. Is attributed. On the other hand, when the forging temperature exceeded 400 ° C. (sample number 75), adhesion of the sintered body to the mold (mold galling) occurred, so the test was stopped.

Moreover, the influence of the upsetting rate in the case of performing hot forging was examined using samples Nos. 01 and 76 to 80 in Tables 17 and 18. As a result, in the case of hot forging, it can be seen that even if the upsetting rate is expanded to a range of 3 to 70%, high tensile strength, elongation, and surface pressure load can be obtained. On the other hand, when the upsetting rate exceeded 70% (sample number 80), the sample was cracked by forging, and the test was stopped.

Claims (9)

The component composition of the entire raw material powder is, by mass ratio, Zn: 3.0 to 10%, Mg: 0.5 to 5.0%, Cu: 0.5 to 5.0%, hard particles: 0.1 10% and the balance consisting of inevitable impurities and Al, and 15 wt% or more aluminum powder as a raw material, aluminum alloy powder containing the total amount of Zn, and 0.1 to 10 wt% hard particle powder at least Raw material powder blending step of using and mixing those raw material powders;
Using the raw material powder obtained by the raw material powder blending step, after filling a mold of a desired shape, a molding step of compacting at a molding pressure of 200 MPa or more,
A sintering step of sintering the molded body obtained in the molding step in a non-oxidizing atmosphere at a sintering holding temperature of 580 to 610 ° C. and a sintering holding time of 10 minutes or more, and then cooling to a normal temperature; ,
The sintered body obtained in the sintering step is heated to 460 to 490 ° C. and water-quenched to form a solution, and then held at 110 to 200 ° C. for 2 to 28 hours for aging precipitation,
A method for producing a high-strength, wear-resistant aluminum sintered alloy characterized in that   The sintered body that has undergone the sintering step is cold forged at a room temperature upsetting ratio of 3 to 40%, or cold forging at an upsetting ratio of 3 to 40%, or at 100 to 450 ° C. upsetting ratio of 3 to 70%. 2. The high-strength wear-resistant aluminum sintered alloy according to claim 1, wherein the heat treatment step is performed after the forging step according to any one of the hot forging steps in which hot forging is performed at an upsetting rate of 2%. Manufacturing method.   3. The method for producing a high-strength wear-resistant aluminum sintered alloy according to claim 1, wherein the aluminum alloy powder is Zn: 10 to 30% by mass, and the balance is made of Al and inevitable impurities.   The said aluminum alloy powder further contains Cu: 10 mass% or less, The manufacturing method of the high intensity | strength wear-resistant aluminum sintered alloy in any one of Claim 1 to 3 characterized by the above-mentioned.   The method for producing a high-strength wear-resistant aluminum sintered alloy according to any one of claims 1 to 4, wherein the hard particle powder has a hardness of 1000 Hv or more and does not react with aluminum.   The method for producing a high-strength wear-resistant aluminum sintered alloy according to claim 5, wherein the hard particle powder is at least one of silicon carbide powder, chromium boride powder, and boron carbide powder.   In the raw material powder, 0.01 to 0.5 mass% of Sn simple powder, Bi simple powder, In simple powder, and any of Sn, Bi, and In with respect to the total composition of the raw material powder 7. The powder according to claim 1, wherein at least one powder of a eutectic compound powder and a monotectic compound powder, which are main components and generate a eutectic liquid phase of the main component, is further added and mixed. Manufacturing method of high-strength wear-resistant aluminum sintered alloy.   The size of the aluminum powder and the aluminum alloy powder is 100 mesh or less, the size of the hard particle powder is 125 mesh or less, and the size of the other powders is 200 mesh or less. The manufacturing method of the high intensity | strength wear-resistant aluminum sintered alloy in any one. 9. The production of a high-strength wear-resistant aluminum sintered alloy according to claim 1, wherein the non-oxidizing atmosphere in the sintering step is a nitrogen gas atmosphere having a dew point of −40 ° C. or less. Method.