JP2889371B2 - Method for producing A1 alloy mixed powder and sintered A1 alloy - Google Patents

Description

The present invention relates to a raw material powder for a sintered Al alloy used for machine parts and the like, and a method for producing a sintered Al alloy component using the raw material powder.

[Related Art and Problems to be Solved] In recent years, in the field of office equipment and computer-related equipment, lightweight Al alloy parts have been required due to the need to reduce power consumption, prevent noise generation due to vibration, and improve portability. The use of is increasing.

One of the methods for producing such Al alloy parts is a normal green compacting and sintering method. This method has a great advantage, particularly in terms of cost, because a near net shape precision part can be manufactured by a simple process.

As a method of manufacturing Al alloy precision parts by green compaction sintering method, a mixed powder of pure Al powder mixed with a simple powder of alloy elements such as Cu, Si, Mg etc. that forms a eutectic with Al and a low melting point is used as a raw material A method using liquid phase sintering, a so-called elemental powder mixing method (Bl
The ended elemental method is well known. However, this method has a problem that it is difficult to generate a liquid phase due to the high melting point of the elemental element powder, and it is difficult for unreacted element powder to remain even after sintering and to obtain a sintered body having good mechanical properties. There was.

On the other hand, alloy elements are added to the powder in advance, and the alloy powder method (Pr
In the case of the ealloy method, since the powder is hard, the molding compressibility is poor, and a good molded product cannot be obtained by ordinary molding. Furthermore, since the melting point of the powder is low, the sintering temperature cannot be sufficiently increased, and there is a disadvantage that diffusion and sintering cannot be favorably advanced.

Furthermore, as an improved method of the element powder mixing method described above, a method of producing a mother alloy powder in which alloy elements are alloyed in advance with Al and using a mixed powder obtained by blending this mother alloy powder with pure Al powder, a so-called mother powder An alloy method (Master alloy method) has also been proposed (for example, JP-A-1-294833). In this method, pure Al powder that is easy to mold is used as the main raw material powder,
And since the alloying element is already alloyed with Al, and in many cases, the composition is adjusted to a composition that easily produces a multi-element low melting point eutectic, the liquid phase sintering proceeds easily, and A sintered body having mechanical properties can be obtained. However, the above-mentioned mother alloy method also has a problem that the mechanical properties, particularly the ductility, are insufficient depending on the use. In particular, depending on the part shape, it is difficult to uniformly supply the powder into the mold, and it is difficult to uniformly compress the powder, and it is not uncommon for the density to be locally low and the mechanical properties to be low. In order to maintain sufficient use performance, it was necessary to further improve the characteristics.

The present invention is intended to solve the problem of sinterability due to the oxide film of the raw material powder, and to manufacture an Al precision part having better mechanical properties than the conventional one by a normal compacting and sintering method. .

[Means for Solving the Problems] The present invention has devised a raw material powder in the master alloy method in order to solve such a problem of the prior art. First, a small amount of Al is used without using pure Al powder that has been used as the main raw material powder.
Al-Cu alloy powder to which Cu was added was used. Secondly, the composition and the amount of the mother alloy powder were optimized from the viewpoint of utilizing a technique of generating a liquid phase during sintering and promoting sintering (so-called liquid phase sintering). By these measures, it has become possible to sinter and diffuse the raw material powder satisfactorily, and it has been found that a sintered Al alloy having superior mechanical properties can be produced, which has led to the present invention. The details will be described below.

 First, the final alloy composition of the sintered Al alloy will be described.

Mg, Si, and Cu were used as alloying elements to be added to Al.

Mg and Si improve the strength of sintered Al alloy by age hardening in the coexistence. The effect is that the added amount of Mg and Si is 0.1w each.
It is scarcely recognized below t% (percentages are given by weight%). On the other hand, if the added amount exceeds 2%, the strength and the ductility are reduced by excessive addition. Therefore, as a range in which the effect of effective strength improvement can be obtained, the addition amounts of Mg and Si are each set to 0.1 to 2.0%.

Cu also improves the strength of the sintered body by age hardening. As described later, 0.1 to 3% of Cu is contained in the main raw material powder. Therefore C
The lower limit of the amount of u added is 0.1%, which is the same as that of the main raw material powder. On the other hand, if the addition amount exceeds 6%, undissolved coarse Cu
The compound remains, and on the contrary, strength and ductility decrease. Therefore, the addition amount of Cu is set to 0.1 to 6.0% as a range in which the effect of effective strength improvement can be obtained.

The present inventors have considered two types of alloy compositions as distinctive alloys within the above range of the final alloy composition. One of them is based on Al-Mg-Si system with the aim of a general-purpose alloy with excellent balance of strength and ductility, and excellent corrosion resistance.
It is an alloy having a composition to which a relatively small amount of Cu of 1 to 1.5% is added (hereinafter referred to as A alloy). A alloy is similar to wrought alloy 6000 series alloy, but as a result of our experiments, Mg
By adding Si in a slightly excessive amount, good mechanical properties are stably obtained. Its composition is Mg: 0.1-1.0
%, Si: 0.5-1.5%, Cu: 0.1-1.5%, more preferably
Mg: 0.3-0.7%, Si: 0.8-1.2%, Cu: 0.3-0.7%. Main applications are holder parts, plate parts, and other precision parts such as light electrical equipment and office automation equipment.

The other is an Al-Cu-based alloy which is characterized by particularly high strength, and in which the added amount of Cu is increased to 2 to 6%, and which is an alloy corresponding to the 2,000 wrought material (hereinafter referred to as B-alloy). ).
Its composition is Mg: 0.1-1.5%, Si: 0.1-1.5%, Cu: 2-6.
%, More preferably Mg: 0.1-0.8%, Si: 0.1-0.8%,
Cu: 3.5-4.5%. The main applications are precision parts for general industrial machines that require higher strength, such as connecting rods and arm parts.

The raw material powder of the present invention is produced by mixing two or more powders. Among these raw material powders, the powder with the largest amount is hereinafter referred to as main raw material powder. At least one of these raw material powders is a mother alloy powder. Hereinafter, the details of the main raw material powder and the mother alloy powder will be described.

 First, the main raw material powder will be described.

Three conditions are required for the main raw material powder of the compacting and sintering method: good compression moldability, good sinterability, and sintering at a sufficiently high temperature. .

Conventionally, pure Al powder has been used as a main raw material powder for a compacted sintered body of an Al alloy. On the other hand, the present inventors have studied to improve the sinterability by adding a small amount of alloy element to pure Al which is a main raw material powder, and thereby to improve the mechanical properties of the sintered Al alloy. As a result, Al-Cu with a small amount of Cu added instead of pure Al powder as the main raw material powder
The sinterability is improved by using the alloy powder, and the sintered Al
The inventors have found that the mechanical properties of the alloy are greatly improved, and have reached the present invention.

Specifically, an Al-Cu alloy powder obtained by adding 0.1 to 3% of Cu to Al is used as a main raw material powder. The reason for limiting the range of the Cu addition amount is as follows. When the addition amount of Cu is less than 0.1%, a clear effect of improving the sinterability is not recognized. On the other hand, Cu
If the addition amount exceeds 3%, not only the effect of improving the sinterability is saturated, but also the powder becomes hard, so that the compactibility of the powder is deteriorated, so that a sufficiently dense compact cannot be obtained.
Furthermore, since the melting point of the powder decreases, the sintering temperature cannot be increased sufficiently, which makes sintering and diffusion difficult. As a result, a sintered Al alloy having good mechanical properties cannot be obtained. That is, by setting the Cu addition amount to 0.1 to 3%, the effect of improving sinterability by adding Cu, good compression moldability, and sintering at a sufficiently high temperature are satisfied.

Another advantage of using Ai-Cu powder as the main raw material powder is that when manufacturing an alloy having a high Cu content, such as an alloy B, the amount of Cu required for the final alloy composition is reduced by the main raw material powder side and the master alloy powder side. In addition, the degree of freedom in designing the mother alloy composition and the compounding amount is increased.

Another group of the main raw material powder is Cu: 0.1 ~
Mn, Ni, Fe, Cr, Zr, Ti, V,
0.1 to 2 wt% of at least one alloy element selected from Pb, Bi, and Sn, with the balance containing unavoidable impurities
It has a composition of Al. This main raw material powder is intended to improve strength, machinability, etc., and as a trace element other than Cu, Mg, Si, Mn, Ni, Fe, Cr, Zr, Ti, V, Pb, Bi,
An object of the present invention is to obtain a sintered alloy containing at least one alloy element selected from Sn in a total amount of 4 wt% or less, with the balance being Al.

 Next, the reasons for limiting the composition of the mother alloy powder will be described.

Mother alloy powder contributes to improving the strength of sintered Al alloy
i, supplying Cu and adjusting the final alloy composition of the sintered Al alloy, and eutectic reaction between the master alloy powder itself and the Al-Cu alloy powder, which is the main raw material powder, melting below the sintering temperature Has the role of generating a liquid phase and promoting sintering. Al-Mg-Si or Al-Cu-Mg
-Si alloys are conceivable.

In addition, since the master alloy powder is hard, a large amount impairs the compression moldability. Therefore, it is desirable that a predetermined alloy element amount can be supplied as a high alloy with a small amount of the mother alloy powder. Furthermore, it is also important as a factor for determining the composition that the aluminum alloy powder can be easily manufactured by the atmospheric atomizing method, which is an economical method for manufacturing an Al alloy powder.

From the above viewpoints, as the lower limit of the composition range of the mother alloy powder for the A alloy, Mg: 4% and Si: 12%, which are compositions close to the eutectic composition of the Al-Mg-Si ternary alloy having a low melting point. Was selected as the lower limit. On the other hand, if Mg exceeds 20%, the activity of the molten metal of the master alloy increases, the risk of oxidation explosion increases, and it becomes difficult to produce by the atmospheric atomizing method, so the upper limit is set to 20% or less. On the other hand, when the amount of Si exceeds 30%, the melting end temperature (liquidus temperature) of the master alloy increases, and it becomes difficult to melt and atomize the master alloy during powder production. Further, at the time of sintering, it becomes difficult to generate a liquid phase due to the eutectic reaction. Therefore, the content of Si is limited to 30% or less. Therefore, the composition of the mother alloy powder, Mg: 4 ~
20%, Si: 12 to 30%, balance Al, more preferably Mg: 5 to 15%, Si: 15 to 25%, balance Al.

Further, Cu was added to this mother alloy composition, and Al-Cu-Mg-Si
It can also be a mother alloy. The addition of Cu further lowers the melting onset temperature (solidus temperature) of the mother alloy powder, making it possible to adjust the temperature. This facilitates sintering, and further improves the mechanical properties of the sintered Al alloy in combination with the role of Cu as an age hardening element. However, since Cu is also supplied from the main raw material powder, it is not always necessary to include Cu in the mother alloy powder depending on the target final alloy composition.

When Cu is contained, the composition of the mother alloy powder is divided into two. This is because, as described above, the final alloy composition is mainly divided into an A alloy having a small amount of Cu and a B alloy having a large amount of Cu, and a suitable mother alloy powder composition is selected for each of them.

In the case of alloy A, the amount of Cu contained in the mother alloy powder may be relatively small because the target amount of Cu in the final alloy composition is relatively small. Therefore, based on the above-mentioned Al-Mg-Si-based mother alloy, a composition was used in which an appropriate amount of Cu was added thereto. In the case of alloy A, the addition of a large amount of Cu leads to an increase in the amount of Cu in the final alloy, and although Cu is useful for increasing the strength, it should be avoided to increase the amount of Cu unnecessarily because it deteriorates the corrosion resistance. From this point of view, it is considered that 30% or less is appropriate as the addition amount of Cu. Accordingly, the composition of the mother alloy powder for the A alloy having a small amount of Cu is as follows: Mg: 4 to 20%, Si: 12 to 30%, Cu: 1 to 30%.
%, Balance Al, more preferably Mg: 5 to 15%, Si: 15 to 25
%, Cu: 5 to 15%, with the balance being Al.

On the other hand, in the case of B alloy aiming for high strength,
It is necessary to increase the amount of Cu, and for that purpose, Cu in the mother alloy powder needs to be 30% or more. On the other hand, if it is 50% or more, the melting point increases, and the melting and atomizing work becomes difficult.
Both Mg and Si must be added to the master alloy powder in an amount of 1% or more as alloying elements for lowering the melting point of the master alloy powder and facilitating liquid phase sintering, and as age hardening of the sintered body. . On the other hand, if both Mg and Si are 20% or more, it is necessary to set each to 20% or less in order to make the dissolving atomizing work difficult for the reasons described above. That is, the composition of the mother alloy powder for the B alloy is Cu: 30 to 50%, and Si: 1 to 2%.
0%, Mg: 1 to 20%, more preferably Cu: 30 to 40%,
Si: 1 to 10%, Mg: 1 to 10%.

Further, another group of the mother alloy powder for a sintered Al alloy of the present invention is the above Mg: 4 to 20%, Si: 12 to 30% or Mg: 4
~ 20%, Si: 12-30%, Cu: 1-30% or Cu: 30-50%,
Si: 1 to 20%, Mg: 1 to 20% containing composition, Mn, Ni,
Fe, Cr, Zr, Ti, V, Pb, Bi, Sn, containing at least one alloy element selected from the group consisting of 0.1 to 8 wt%, and the balance being Al having an unavoidable impurity. is there. This mother alloy powder is intended to improve strength, machinability, etc., and other than Cu, Mg, Si, as trace elements, Mn, Ni, Fe, Cr,
Contains at least one alloying element selected from among Zr, Ti, V, Pb, Bi, and Sn in a total amount of 4 wt% or less, with the balance being Al
The purpose is to obtain a sintered alloy having a composition consisting of

As described above, the mother alloy powder is Al-Mg-Si based, Al-Mg-Si
-Cu based composition. By changing the composition within the scope of the claims, it becomes possible to adjust the melting start temperature of the mother alloy and the temperature at which a liquid phase is generated by the reaction with the main Al-Cu alloy raw material powder. Further, by adjusting the composition of the master alloy powder, the amount of the mother alloy powder in the raw material mixed powder can be adjusted.

If the amount of the mother alloy powder is too small, a sufficient amount of liquid phase cannot be secured in a sintered Al alloy in which liquid phase sintering is indispensable, and it is not possible to obtain a sintered body having good characteristics. It becomes possible. On the other hand, if it is too large, compression moldability is impaired, and the amount of liquid phase generated during sintering becomes too large, so that a sintered body having good surface properties cannot be obtained due to a sweating phenomenon. From such a viewpoint, the compounding amount of the master alloy is preferably 2% or more and 15% or less, more preferably 3% or more and 12% or less. The Al-Cu main raw material powder and the mother alloy powder are blended so as to have the final target composition in this range.

The particle size of these raw material powders is desirably at least 90% at 50 mesh or less and 635 mesh or more. This is because if there are many powders of 50 mesh or more, the filling property to the mold is poor, while 635
If the amount of powder below the mesh is large, the fluidity is impaired, and the powder easily enters the gaps of the mold during molding, which is not suitable because it tends to cause galling.

Further, the raw material powder may be heated and annealed in advance to soften the powder, thereby further improving the molding compressibility of the powder.

Further, by mixing a lubricant with the alloy powder, it is possible to improve the lubrication between the powders, the lubricity between the powder and the mold wall surface, and enhance the formability. 0.2% lubrication
In the following, the effect is insufficient, and when it is 2% or more, the effect is not only saturated, but also impairs the fluidity and moldability of the powder, and the lubricant is volatilized and scattered during sintering, and is unnecessary in the sintering furnace. Alternatively, in vacuum sintering, 0.2 to
2%. More preferably, it is 0.7 to 1.8%. As the kind of the lubricant, it is preferable that all of the lubricant be volatilized and scattered below the sintering temperature and have no detrimental effect on the material properties. From such a point of view, metal salt-based lubricants (eg, zinc stearate,
An organic lubricant such as an amide lubricant, which does not contain a metal, is more preferable than lithium stearate, aluminum stearate, etc.).

In addition, in order to impart functions such as wear resistance, lubricity, and low coefficient of thermal expansion to sintered parts, these powders are made of sintered alloys such as ceramics, metal, Si, carbon or solid lubricants, and particles such as fibers. Two-phase substances can also be mixed.

Next, a method for producing a sintered Al alloy using the above raw material powder will be described.

First, a mixed powder raw material having a desired alloy composition is prepared, and is subjected to pressure molding. If the molding pressure is less than 2 ton / cm ² , the compacts are not sufficiently densified and the powders are in insufficient contact with each other, so that good sintered body strength and ductility cannot be obtained. Therefore, it is necessary to mold at 2 ton / cm ² or more. On the other hand, when the molding pressure is too high, problems such as generation of lamination, galling on the mold, and shortening of the life of the mold occur. Therefore, a molding pressure exceeding 8 tons / cm ² is not suitable for practical operation. Therefore, molding is performed at 2 to 8 ton / cm ² .

Further, by molding the raw material powder in a state of being heated to 70 ° C. to 250 ° C., it is possible to further densify the molded body.

Regarding the sintering atmosphere, it is necessary to perform sintering in a vacuum or in a non-oxidizing atmosphere such as a nitrogen gas or argon gas atmosphere in order to prevent oxidation of the active Al alloy powder particles and sufficiently promote sintering. When sintering in vacuum, the degree of vacuum is 0.1 torr
r or less, desirably 0.01 torr or less. Further, sintering under a reduced pressure and flowing a small amount of an inert gas such as nitrogen gas after vacuum replacement of the inside of the sintering furnace also enhances the effect of removing gas components generated from the sintered body. When sintering in an inert atmosphere such as a nitrogen gas atmosphere or an argon gas atmosphere, the purity of the gas is important. In particular, the moisture contained in the gas has a bad influence on the characteristics of the sintered parts. Need to be controlled, preferably with a dew point of -40
It must be kept below ℃.

If the sintering temperature is lower than 500 ° C., the diffusion of elements is insufficient, and the sintering of the powders becomes insufficient. On the other hand, if the temperature is higher than 650 ° C, a large amount of liquid phase is generated or the powder cannot be melted, and the shape of the part cannot be maintained as the temperature rises.
It is necessary to sinter below.

Further, the sintered body thus obtained can be recompressed. An appropriate molding pressure for recompression is 3 to 11 tons / cm ² .
Recompression has the purpose of so-called sizing for improving the dimensional accuracy and the purpose of improving the mechanical properties of the sintered body. For the latter purpose, the sintered body is further densified by recompression, the bore in the sintered body is crushed, and the metal contact surface is newly increased. At that time, the strength of the recompressed body is improved by work hardening, and the ductility is reduced. On the other hand, after the recompression, the effect of work hardening is removed by performing a heat treatment described below, and further sintering and diffusion partially proceed, and both strength and ductility are improved. According to the examples of the present inventors, by performing recompression and heat treatment on the sintered body, the strength is improved by about 20 to 30%, and the elongation is about 1.4 to
4 times improved. That is, the process of recompression and heat treatment is very effective for improving the mechanical properties of the sintered body, and is particularly suitable for manufacturing various arm parts and the like that require ductility.

Further, mechanical properties, especially ductility, can be improved by re-sintering the compact obtained by re-compression.
Diffusion and sintering can be further advanced by sintering the structure densified by recompression again. The conditions at that time are basically the same as for sintering, and the resintering temperature is 500 ° C
The above is desirable.

Also, Cu, Mg, and Si, which are alloy components of these sintered bodies, originally contribute to improvement of mechanical properties by heat treatment.
Therefore, similarly to a normal Al alloy, it is effective to perform a solution-aging treatment of T6 or T4 to adjust and improve its mechanical properties. T6 treatment is an effective heat treatment especially when high strength is required.By applying it to Al-Cu alloy,
It is possible to provide a tensile strength of 35 kgf / mm ² or more. T
The 4 treatment is an effective heat treatment when a property having both moderate strength and good ductility is required.

Normally, practically sufficient characteristics can be obtained by forming, sintering, recompressing, and then solution-aging treatment.

[Action] The present invention relates to an Al-Cu alloy powder containing a small amount of Cu and Al
The use of -Mg-Si master alloy powder or Al-Mg-Si-Cu mother alloy powder facilitates generation of a liquid phase, thereby improving sinterability and significantly improving the mechanical properties of the sintered Al alloy. It will improve.

Examples of the Invention Hereinafter, examples of the present invention will be described.

Example An Al alloy main raw material powder shown in Table 1 and a master alloy powder shown in Table 2 were produced by an atmospheric atomization method, and sieved.
A powder under 0 mesh to 325 mesh was obtained. These powders were blended at the blending ratio shown in Table 3, and 1% of an amide-based lubricant was further added thereto to obtain a raw material powder. It was molded at a molding pressure of 4 tons / cm ² into a tensile test specimen shape specified in JIS Z2550. The molded body is put in a nitrogen atmosphere of 1 to 3 torr
Sintered at 70-590 ° C for 2 hours. T6 or T4 for the sintered body
After the heat treatment, it was subjected to a tensile test. Table 4 shows the results.
Shown in Next, some of the sintered bodies were recompressed at 5 ton / cm ² and then subjected to a T6 or T4 heat treatment and subjected to a tensile test. The results are shown in Table 4.

Comparative Example 1 An Al-4% Cu powder was produced by an air atomizing method, which was sieved to obtain a powder on a screen below 100 mesh to a screen on 325 mesh. In addition, the powder Al-20% Si-10% Mg powder of Table 2
And amide-based lubricant 1%
Was added to obtain a raw material powder. It was used as a tensile test specimen under the same manufacturing conditions as in the examples and was subjected to the test. Table 4 shows the results.

Comparative Example 2 An Al powder was produced by an air atomizing method, and the obtained powder was sieved to obtain a powder on a screen below 100 mesh to a screen on 325 mesh. In addition, the powder of Al-20% Si-10% Cu-10% Mg powder, Al-
6% Si-40% Cu-6% Mg powder was mixed as shown in Table 3, and 1% of an amide-based lubricant was further added thereto to obtain a raw material powder. It was used as a tensile test specimen under the same manufacturing conditions as in the examples and was subjected to the test. Table 4 shows the results.

Comparative Example 3 An Al powder was produced by an air atomizing method, and the powder was sieved to obtain a powder on a screen below 100 mesh to a screen on 325 mesh. Also mix Si powder, Cu powder and Mg powder with adjusted particle size under 100 mesh sieve to 325 mesh sieve
Al-1% Si-0.5% Cu-0.5% Mg. Further, 1% of an amide-based lubricant was added thereto to obtain a raw material powder. It was used as a tensile test specimen under the same manufacturing conditions as in the examples and was subjected to the test. Table 4 shows the results.

From Table 4, it can be seen that the alloy A of the present invention was obtained by sintering + T6 treatment, and had a tensile strength of 22 to 25 kgf / mm ² and an elongation of 3% or more. It was excellent.

Furthermore, when it is recompressed and heat-treated, T6
Tensile processing strength: 28~33kgf / mm ^2, elongation: 8% or more and strength,
The properties are improved in a well-balanced manner in both ductility, and a material with an unprecedented elongation of at least 23% is obtained by T4 treatment. On the other hand, the B alloy was sintered + T6 and had a tensile strength of 3
Properties of 3 to 35 kgf / mm ² , elongation: 1.5% or more are obtained.
Strong strength and proper elongation are obtained. Further B alloy recompression + T6 treated with tensile strength: 38~41kgf / mm ² and no excellent strength to the prior are example. In the recompression + T4 treatment, the elongation shows an excellent value of 8% or more while maintaining the tensile strength of 30 kgf / mm ² or more.

Comparative Example 1 is an example in which Al-4% Cu powder was used as the main raw material powder. Due to the large amount of Cu added, the powder compressibility is poor,
Lamination occurs and a molded product that can be used practically has not been obtained.

Comparative Example 2 is an example of a conventional mother alloy method using pure Al powder as a main raw material powder. Comparative Example No. 20 is the alloy A of the present invention, No.
21 is an example of a composition corresponding to the alloy B of the present invention.

Both the strength and the elongation are lower than those of the sintered alloy according to the present invention.

Comparative Example 3 is an example of an element powder mixing method in which a simple powder of an alloy element of Si, Cu, and Mg is blended. Only low values were obtained for both strength and elongation.

[Effects] According to the present invention, an Al alloy member having high strength and high ductility can be obtained by a sintering method, which greatly contributes to weight reduction of a component having a complicated shape.

────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Yoshio Machida 1505 Shimokagemori, Chichibu City, Saitama Prefecture Showa Denko Chichibu Laboratories Co., Ltd. 247044 (JP, A) JP-A-1-230743 (JP, A) JP-A-52-153806 (JP, A) JP-A-1-294833 (JP, A) JP-B-45-24207 (JP, B1) (58) Field surveyed (Int. Cl. ⁶ , DB name) C22C 21/00-21/18 C22C 1/04 B22F 1/00, 3/10

Claims (7)

(57) [Claims] (1) A main raw material powder composed of Al: Cu: 0.1 to 3.0 wt% and the balance containing unavoidable impurities: Mg: 4 to 20 wt%, Si: 12 to 3 wt.
Master alloy powder or Mg consisting of Al containing 0 wt% and the balance containing unavoidable impurities, Mg: 4 to 20 wt%, Si: 12 to 30 wt%, Cu: 1
It is a powder obtained by mixing one or two of the mother alloy powders of Al containing up to 30 wt% and the balance containing unavoidable impurities, wherein the composition of the mixed powder is Mg: 0.1-1.0 wt%, Si: 0.5- 1.5
An Al alloy mixed powder for a sintered Al alloy, wherein wt%, Cu: 0.1 to 1.5 wt%, and the balance is substantially made of Al. 2. A main raw material powder composed of Al: Cu: 0.1 to 3.0 wt% and the balance containing unavoidable impurities: Mg: 1 to 20 wt%, Si: 1 to 20 wt.
wt%, Cu: 30 ~ 50wt%, the balance is mixed with a master alloy powder consisting of Al containing unavoidable impurities, the composition of the mixed powder is
Mg: 0.1-1.5wt%, Si: 0.1-1.5wt%, Cu: 2-6wt%, with the balance being substantially Al for sintered Al alloys
Al alloy mixed powder. 3. A mixed powder obtained by mixing a main raw material powder and a mother alloy powder, wherein the main raw material powder is 0.1% to 2% by weight of Mn, further added to the main raw material powder or the main raw material powder. Ni,
The mother alloy according to claim 1, wherein the mother alloy powder is a main raw material powder to which at least one element selected from the group consisting of Fe, Cr, Zr, Ti, V, Pb, Bi, and Sn is added. 0.1 to 8 wt% of Mn, Ni, Fe, C
r, Zr, Ti, V, Pb, Bi, Sn is a mother alloy powder to which at least one element selected from the group is added, and the composition of the mixed powder is Mg: 0.1 to 1.0 wt%, Si: 0.5 ~ 1.5wt%, C
u: 0.1 to 1.5 wt%, Mn, Ni, Fe, Cr, Zr, T
a sintered Al alloy containing one or more alloying elements selected from i, V, Pb, Bi, and Sn in an amount of 4% or less, with the balance being substantially Al Al alloy mixed powder for use. 4. A mixed powder obtained by mixing a main raw material powder and a mother alloy powder, wherein the main raw material powder further contains 0.1 to 2 wt% of Mn, Ni,
The mother alloy according to claim 2, wherein the mother alloy is a main raw material powder to which at least one element selected from the group consisting of Fe, Cr, Zr, Ti, V, Pb, Bi and Sn is added. 0.1 to 8 wt% of Mn, Ni, Fe, C
A master alloy powder to which at least one element selected from the group consisting of r, Zr, Ti, V, Pb, Bi, and Sn is added, wherein the composition of the mixed powder is Mg: 0.1 to 1.5 wt%, Si: 0.1 ~ 1.5wt%, C
u: contains 2 to 6 wt%, and further contains Mn, Ni, Fe, Cr, Zr, Ti,
V, Pb, Bi, Sn, including the amount of one or more alloying elements selected from among the total amount of 4% or less, the balance is substantially Al
An Al alloy mixed powder for a sintered Al alloy, comprising: 5. An Al alloy mixed powder for a sintered Al alloy, wherein 0.2 to 2% by weight of a lubricant is mixed with the mixed powder according to any one of claims 1 to 4. 6. A powder compact is molded from the mixed powder according to any one of claims 1 to 5 at a pressure of ² to 8 ton / cm ² , and then the powder compact is subjected to a non-oxidizing process. A method for producing a sintered Al alloy, comprising sintering in a temperature range of 500 to 650 ° C in an atmosphere. 7. A powder compact is molded from the mixed powder according to any one of claims 1 to 5 at a pressing force of ² to 8 ton / cm ² , and then the compact is non-oxidizing. Sintering in a temperature range of 500 to 650 ° C. in an atmosphere, further recompressing the sintered alloy again at a pressure of 3 to 11 tons / cm ² , and further performing a solution-aging treatment. Method of producing sintered Al alloy.