JPH07188701A - Al3Ti dispersion strengthened aluminum alloy, powder thereof, and methods for producing the same - Google Patents

Abstract

(57) [Summary] [Object] To provide a heat-resistant strengthened aluminum alloy in which Al ₃ Ti is uniformly dispersed in an Al matrix, a powder for the alloy, and a method for producing the same. [Structure] The present invention provides pure Al powder or Al alloy powder,
A method for producing an Al ₃ Ti dispersion strengthened aluminum alloy powder, which comprises mixing Al ₃ Ti powder and subjecting the mixed powder to mechanical alloying, an alloy thereof, and a method for producing the alloy.

Description

Detailed Description of the Invention

[0001]

The present invention relates to aluminum (or Al
To a matrix, and an intermetallic compound, in particular Al ₃ Ti, dispersed uniformly therein, a heat-resistant strengthened aluminum alloy, a powder for producing the alloy, the alloy, and a method for producing the powder.

[0002]

2. Description of the Related Art Conventionally, there have been the following methods for strengthening aluminum alloys for mass production. (I) Fiber Reinforcement Method (FRM) (ii) Ceramic Particle Dispersion Reinforcement Method (iii) Rapidly Solidified Powder and Hot Extrusion Method (iv) Application of Ordinary T4, T5, T6 Heat Treatment (Precipitation Strengthening) This method , The solubility difference of solute atoms at high temperature and room temperature is used, and the aging precipitation after solution treatment is used.

[0003]

Among the above-mentioned conventional techniques, the present invention is directed to a particle dispersion strengthening method and is intended to solve the problems in this technical field. That is, for example, in a case where ceramic particles are dispersed and reinforced in a matrix of Al, the hardness of Al and the ceramic particles is too different, and therefore, the machinability of the reinforced material is significantly deteriorated. In addition, there is a problem in the wettability between the Al matrix and the reinforcing particles, so that the particles are often aggregated and the strength is greatly varied, so that the sufficient reinforcing effect may not be obtained. Other,
Although hardness, tensile strength, etc. are improved, elongation is drastically reduced, impact value and fracture toughness value are also lowered, and as a result, reliability as a material may be impaired. There is also a problem that hot working such as hot extrusion is difficult. Many of the matrices use pure Al, and many do not show sufficient strength in a high temperature range of 300 ° C. or higher.

On the other hand, the one using Mg ₂ Si powder (or intermetallic compound powder) as a reinforcing material has a drawback that the cost is heavy because it itself is expensive. In addition to Mg ₂ Si, when the intermetallic compound used for the reinforcing material is a material containing a high melting point element, atomization is difficult and not only the intended component composition cannot be obtained.
It was difficult to uniformly disperse the intermetallic compound.
The present invention has been made in view of the above circumstances, in which Al is used as a matrix, and the fine intermetallic compound Al ₃ Ti is uniformly dispersed in the matrix to improve the strength near room temperature and also in a high temperature range. An object of the present invention is to provide an Al ₃ Ti dispersion strengthened aluminum alloy showing excellent strength even at (300 to 500 ° C.), a powder for the alloy, and a method for producing them.

[0005]

According to the present invention, in accordance with the above object, pure Al powder or Al alloy powder is mixed with Al ₃ Ti powder, and the mixed powder is mechanically alloyed.
The above-mentioned problems have been solved by the method for producing l ₃ Ti dispersion strengthened aluminum alloy powder. Further, in the present invention, pure Al powder and pure Ti powder are mixed, and the mixed powder is mechanically alloyed to produce an Al ₃ Ti-based precursor composite powder,
The above problems were solved by a method for producing an aluminum alloy powder in which a pure Al powder was further mixed with the precursor composite powder and the Al ₃ Ti based precursor composite was subjected to mechanical alloying again. The present invention uses Al ₃ Ti dispersion strengthened aluminum alloy powder produced by the method according to any one of claims 1 to 3, after the billet molding, the manufacturing method of hot working for Al ₃ Ti dispersion strengthened aluminum alloys The above problems have been resolved. The present invention also relates to Al ₃ T produced by the method according to any one of claims 4 to 7.
Using an aluminum alloy powder compounded with an i-based precursor composite, Al is mainly used in the steps from billet forming to hot working.
₃ Ti is produced by reaction to form Al ₃ T in the Al matrix.
The above problem was solved by a method for producing an Al ₃ Ti dispersion strengthened aluminum alloy in which i was dispersed. Further, the present invention has solved the above-mentioned problems by an Al ₃ Ti dispersion strengthened aluminum alloy produced by the method of claim 8. Further, the present invention has solved the above-mentioned problems by an Al ₃ Ti dispersion strengthened aluminum alloy produced by the method of claim 9. Further, the present invention uses the aluminum alloy powder compounded with the (Al, X) ₃ Ti-based precursor composite produced by the method according to any one of claims 15 to 17, in the steps from billet forming to hot working. (Al, X) ₃ Ti system (where X = N
p, V, Y, Mo, Zr, Si, Mn, Fe, Co, N
i, Hf, Cr, etc.) to produce an intermetallic compound,
The above problem was solved by a method for producing an intermetallic compound dispersion-strengthened aluminum alloy in which the intermetallic compound is dispersed in an l matrix. Further, the present invention has solved the above-mentioned problems by the (Al, X) ₃ Ti-based intermetallic compound dispersion strength aluminum alloy produced by the method of claim 19. Further, the present invention is manufactured by the method of claim 20 (A
The above-mentioned problems have been solved by using an (I, X) ₃ Ti-based intermetallic compound dispersion strengthened aluminum alloy.

The present invention will be described below with reference to the manufacturing process shown in FIG. 1 (referred to as process A). First, the particle size of the pure Al powder used is 250 to 20 μm.
It is preferably 44 μm or less, and the purity thereof is 99% or more, preferably 99.9% or more. 250
If the average particle size is 20 μm or less, the raw material cost is increased. The Al ₃ Ti powder used is 150 mesh to 250 mesh.
A fine powder having a mesh size or less, preferably an average particle size of 20 μm or less is used. If the powder is larger than this, the desired effect cannot be sufficiently obtained. The mixing ratio of Al ₃ Ti is 5 to 45% by weight of the whole. Al ₃ Ti has a low plastic deformability even during hot work, and when it is dispersed in Al of the matrix, it hinders hot plastic work. Therefore, when the mixing ratio of Al ₃ Ti exceeds 45% by weight, this tendency becomes remarkable,
The impact value and the elongation become small, the ductility peculiar to the Al alloy disappears, and conversely the tendency of embrittlement becomes stronger. Further, when the mixing ratio becomes large, the specific gravity becomes large, and since Al ₃ Ti is expensive, the cost increases. On the other hand, when the mixing ratio of Al ₃ Ti is less than 5% by weight, the effect as a reinforcing material is not recognized. Incidentally, instead of the pure Al powder, Cu, Ni, M
At least 2 elements out of g, Si, Zn, Fe, etc.
You may use the Al alloy powder which contains a total of 7 weight% or less of one or more elements.

In order to meet the above conditions, Al powder and A
l ₃ Ti powder is weighed and mixed, and then treated by a mechanical alloying method. That is, the mixed powder is put into a high energy type ball mill, that is, an attritor and processed. FIG. 3 shows the device structure. In the attritor 1, the rotation of the shaft 2 causes the agitator arm 3 to rotate, which causes the ball 4 to move. The raw materials are mixed by the movement of the balls 4. During the mixing operation, gas is introduced through the gas inlet to keep the mixed atmosphere constant. Further, cooling water is introduced from the water inlet 6 to keep the temperature constant. In FIG. 3, 7 is a gas outlet and 8 is a cooling water outlet.

The ball 4 has a maximum size of 1 inch, preferably 3
/ 8 inch steel balls are preferred. The ratio of the total weight of the balls to the total amount of powder added is such that the ratio of the total weight of the balls to the total weight of the powder is 150: 1 to 20: 1, preferably 140 :.
1 to 40: 1. The rotation speed of the shaft 2 is preferably 250 rpm. Ar or He or the like can be used as the mixed atmosphere. The peripheral speed of the tip of the agitator 3 is set to 3.0 m / sec or less and the processing is performed for 1 to 10 hours. If the treatment takes a long time, the manufacturing cost is increased, and Fe is mixed due to the abrasion of the balls and the container wall, which lowers the elongation of the finished product, which is not preferable. In the treatment, considering the dispersion of the powder and the lubricating effect,
This is mainly done by adding an organic solvent such as methanol or ethanol. The amount of this organic solvent added is regulated as follows. That is, the amount added is [dispersant amount (ml) / total powder weight (g)] × 100 = 1 to 5 (1). In addition, 1-5 with methanol and 1-with ethanol
3.5 is a suitable range. Pure A when the amount of dispersant is small
l adheres to the ball surface in the attritor and mechanical alloying cannot be performed sufficiently. On the other hand, if the amount is too large, the carbon that remains as a residue reacts with Al to form aluminum carbide and embrittle the material. It is preferable that the amount of carbon mixed from the residue of alcohol is 1% by weight or less. The carbon incorporated in Al exists in the form of Al ₄ C ₃ , which is
It has physical properties similar to ceramics. For this reason, an aluminum alloy containing a large amount of carbon has a low elongation and impact value and a poor toughness.

After the above treatment, the powder is discharged from the attritor container and classified. As the powder, a fine powder having a particle size of 300 μm or less, preferably 104 μm or less is used hereinafter. This can reduce void defects in the briquette and internal defects after extrusion. The powder having a particle size of more than 300 μm may be discarded or mechanically alloyed again and pulverized. Next, the mechanical alloying powder is housed in a mold, and this is compression molded to make a specific billet,
This billet is heated in a vacuum atmosphere for degassing. That is, the degree of vacuum is 10 ^-3 Torr or less, and the temperature is 400 to
Heating at 500 ° C. is performed for 3 to 5 hours. The degassed billet may be hot extruded under the conditions of an extrusion temperature of 400 to 500 ° C. and an extrusion ratio of 10 or more to form an extrusion rod. It is also possible to grind Al ₃ Ti in an attritor container first, and then mix a predetermined amount of pure Al or Al alloy for processing without discharging this from the container.
In this case, it is preferable that the amount of methanol added (see the formula (1)) is 2.5 to 5 in the treatment of Al ₃ Ti and the treatment is performed within 5 hours.

Next, as another method according to the present invention, pure A
The method of using 1 powder and pure Ti powder will be described with reference to the manufacturing process shown in FIG. 2 (this will be referred to as process B). As the pure Al powder, one having the same specifications as the process A is used. As the pure Ti powder, a powder having a fineness of 250 mesh or less, preferably finer than 400 mesh is used. The mixing ratio of Ti is 25 to 45% by weight, preferably 35 to 39%, and the balance is Al. This is because the stoichiometric composition of Al ₃ Ti is Al-37 wt% Ti,
The composition ratio of Ti is 35 to 39%. The stoichiometric composition means the chemical composition (atomic composition ratio) represented by the structural formula.

After mixing the pure Al powder and the pure Ti powder which are weighed so as to meet the above conditions, the pure Al powder and the pure Ti powder are put into the container of the attritor, and the mechanical alloying treatment (I) is carried out under the same conditions as in the process A. . Here, Al and Ti for reacting and producing Al ₃ Ti in a later step form a precursor composite powder. In this case, since Al and Ti both have strong adhesiveness and poor crushability, a dispersant is used. For example, methanol is used, and the addition amount is 2.5 to 5 in the formula (1), and the treatment is performed within 20 hours.

After the treatment, the powder of the mechanically alloyed precursor composite of Al and Ti is discharged from the attritor container and classified. The precursor composite powder used after classification is 104μ
m (150 mesh) or less, preferably finer than 250 mesh is used. Further, here, if necessary, a step of pulverization treatment is further added to obtain a preferable particle size. It is also possible to proceed to the next step without discharging and classifying the powder of the precursor complex from the attritor container (see route a in FIG. 2). Next, pure Al powder is mixed with the precursor composite powder of Al ₃ Ti. The mixing ratio of the precursor composite powder in this case is 5 to 45% by weight (wt%).

Next, a powder mixture of the precursor composite powder and pure Ti powder is put into an attritor container, and the mechanical alloying treatment (II) is performed again. The treatment conditions are basically the same as in the case of the mechanical alloying treatment, but in this step, since the purpose is to uniformly disperse the precursor composite in Al, the treatment time may be short and within 5 hours. And The Al alloy powder described at the beginning of the process A may be used instead of the pure Al powder used here. After the treatment is completed, the powder may be discharged from the attritor container, the powder may be molded into a billet in the same manner as in the process A, and the extrusion rod may be formed through degassing and hot working. The total oxygen content after hot working depending on the oxidation amount of the alloy powder (Since it exists as oxide Al ₂ O ₃ , it is expressed as the abundance ratio (wt%) of Al ₂ O ₃ )
It should be 5% by weight or less. If the amount of oxidation exceeds this, the elongation decreases, the extrudability deteriorates, and it becomes difficult to perform hot working for imparting shape later.

[0014] The above, when manufacturing the precursor complex of Al ₃ Ti, Al ₃ Ti stoichiometry (Al-37wt% T
According to i), the precursor composite powder was manufactured. However, this precursor complex is not always Al
The composition value of ₃ Ti single phase does not have to be Al + Al ₃ T
It may be i or Al ₃ Ti + TiAl ₂ (or TiAl) composition region. The state diagram of the Al-Ti element is shown in FIG.
As shown in Figure ₃ , Al ₃ Ti is
Onide) type, which has almost no composition width. Therefore, the composition value of the precursor composite can be laterally expanded centering on the stoichiometric composition of Al ₃ Ti.

[0015]

EXAMPLES Examples 1 to 3 of the present invention will be described in detail below.

Example 1 Performed according to Process A. Ti = 33.6 in wt%
%, Al ₂ O ₃ = 0.48%, the balance Al and other impurities, and an intermetallic compound Al ₃ Ti having a grain size of 400 mesh or less was used. 68.8 g of this powder was put into the attritor container shown in FIG. 3 and pulverized. The agitator rotation speed was 250 rpm, the grinding time was 2 hours, and 2 cc of methanol was added as a dispersant. After crushing is completed,
So that the composition ratio of Al-30 vol% Al ₃ Ti is
Pure Al powder (purity 99.99%, particle size 44μm or less is 90
%) 131.2 g from the upper part of the attritor container, and the agitator rotation speed is 115 rpm for 10 minutes.
After adding 2 cc of methanol and rotating at a low speed to sufficiently mix Al ₃ Ti powder that has already been pulverized and pure Al powder, increase the number of revolutions to 250 rpm and continue for 2 hours.
Processing continued. After cooling, the powder was discharged out of the container.

The powder thus obtained becomes a mixed powder in which Al ₃ Ti particles are finely incorporated in the Al matrix. FIG. 4 shows an enlarged structure of this mixed powder. Next, this powder was molded into a billet having a diameter of 32 mm by a press having a compression load of 100 tons, and then degassed at 500 ° C. for 5 hours in a vacuum atmosphere of 6 × 10 ⁻³ Torr. This billet was hot extruded at an extrusion ratio of 10, 450 ° C. to obtain a raw material. FIG. 5 is a metal structure showing an enlarged cross section of this material. In addition, Al-
20 vol% Al ₃ Ti, Al-10 vol% Al ₃ T
The material of i was evaluated and evaluated as follows.

First, a test piece was sampled from each of the above materials, a high temperature tensile test was carried out, and its tensile strength and elongation were investigated. The test pieces tested at each temperature (samples 1, 2, and 3) were previously held at the test temperature for 100 hours and subjected to a heat history. Each sample has the following mixing ratio. Sample No. mixing ratio (vol%) mixture ratio (wt%) Sample _{1: Al-10vol% Al 3} Ti Al-12.0wt% Al 3 Ti Sample _{2: Al-20vol% Al 3} Ti Al-23.4wt% Al 3 Ti sample 3: shows the _{Al-30vol% Al 3 Ti Al} -34.4wt% Al 3 Ti test results the following Table 1 and Table 2.

[0019]

[Table 1]

[0020]

[Table 2]

Samples 1 and 2 are low in strength as a whole, but the matrix is not pure Al, and the JIS standard, for example, A20.
When alloy powders such as 24, A2017, A6061 and A7075 (which can be extruded) are used, not only the strength near room temperature (RT) but also 300 ° C. or higher is effective. However, if the mixing ratio is 5 wt% or less, no effect can be expected. Further, when the content is 30 vol% Al ₃ Ti or more, pure A is contained in the matrix.
It is more effective to use l for ensuring extrudability and toughness. As described above, in the case of Sample 3, the room temperature strength is at the level of commercially available high-strength aluminum alloys, and at 500 ° C., a value of 100 MPa, which cannot be achieved by conventional aluminum alloys, is obtained.

Example 2 Process B is carried out. The pure Al powder used is 2
50 to 20 μm, purity 99% or more, pure Ti powder has a particle size of 4
Those having a thickness of 5 to 10 μm and a purity of 99.5% or more were used. A
In order to prepare a precursor composite of l ₃ Ti (having a stoichiometric composition), a total of 300 g of pure Al powder 189 g and pure Ti powder 111 g
g was weighed. This was put into an attritor container and subjected to mechanical alloying treatment. Amount of methanol added 8c
c, the processing time is 15 hours, and other conditions are the same as those in the first embodiment.
Same as. The Al ₃ Ti precursor composite powder thus obtained was discharged from the container and classified. 1 by classification
Those having a size of 06 μm or less were used thereafter. The structure of this Al ₃ Ti precursor composite powder is shown enlarged in FIG.

Next, the Al ₃ Ti precursor composite powder 70.2
g in an attritor container, add 4 cc of methanol,
Grinding was carried out at an agitator rotation speed of 250 rpm for 2 hours. Next, with the treated powder still in the attritor container, 229.8 g of pure Al powder was charged from the upper part of the container, and the mixture was mixed at a low speed of 115 rpm for agitator for about 10 minutes. The composition of this mixed powder is Al-20 vol% Al.
₃ Ti has a target composition. The mechanical alloying process was performed again in order to form the above Al ₃ Ti precursor composite in pure Al. Agitator rotation speed 250 rp
m, the treatment time was 4 hours, and 2 cc and 1 cc of methanol were added at the start of the treatment and 2 hours after the start, respectively, to add a total of 3 cc. FIG. 7 shows the structure of powder in which this Al ₃ Ti precursor is compounded. Next, after the treated powder was cooled in the container, it was discharged into the atmosphere and classified. 104μ in this classification
Powders of m or less were used in the subsequent steps. Thereafter, the same treatment as in Example 1 was performed to obtain a material. FIG. 8 shows a metal structure in which the cross section of this material is enlarged.

In the above treatment, it was confirmed from the X-ray diffraction chart of FIG. 9 that Al ₃ Ti was not formed in the obtained powder before the hot extrusion step. Further, after hot extrusion, the precursor composite is
It can be confirmed from the X-ray diffraction chart in FIG. 10 that it has changed to l ₃ Ti. From this, it is understood that the process B of the present invention is a method completely different from the conventional method in which the reinforcing particles (for example, ceramics or intermetallic compound) are compounded during mechanical alloying. That is, according to the metallographic structure of the material after hot extrusion in FIG. 8, it is found that Al ₃ Ti having a maximum size of 5 μm and other submicron size are uniformly and finely dispersed.

Next, the same evaluation as in Example 1 was performed. The sample is Al-20 vol% Al ₃
For comparison with the above-mentioned treated material of Ti (sample 4), A
The 2018-T ₆ forged bars (and Comparative Example 1) was used.

[0026]

[Table 3]

[0027]

[Table 4]

From the above, sample 4 has a temperature of 250 ° C. or higher as compared with Comparative example 1 (A2018-T ₆ material) which is one of the strongest in heat-resistant aluminum alloys on the market even though the matrix is pure Al. It was found that the difference was overwhelmingly significant. On the other hand, in the sample 4, the elongation decreases as the temperature rises, reaches a minimum around 300 ° C., and then tends to rise again. This tendency is not found in conventional Al alloys, indicating that it has excellent creep resistance. That is,
Since the pistons of automobile engines are constantly exposed to temperatures around this, it can be said that they are the optimum materials for this. Also,
If the elongation at room temperature is about 20%, the shape of the part may be inexpensively formed by cold forging.

Example 3 According to the process B, the composition value of the precursor composite was carried out in a range in which the composition value of the precursor composite can be expanded centering on the stoichiometric composition of Al ₃ Ti. The composition of the precursor composite was set to four types (samples 5 to 8) shown in Table 5, and mechanical alloying treatment and hot extrusion were performed under the same conditions as in Example 2 to obtain a raw material. In Sample 8, since the Al content ratio was large and the adhesive property was strong, fusion of the precursor composite occurred in the container and it was difficult to discharge it from the container. Further, even in the discharged product, Ti was not crushed efficiently, so that uniform composite formation was not possible, resulting in an extremely non-uniform structure. For this reason, it was judged that it was difficult to secure the strength of Sample 8, and the subsequent extrusion process was stopped. Further, Sample 5 had poor extrudability, and was hot extruded at 500 ° C.
Therefore, the strength test was performed on three kinds of samples 5 to 7.
The results are shown in Table 6.

[0030]

[Table 5]

[0031]

[Table 6]

Each sample was given a thermal history of holding for 100 hours at each test temperature. Further, in each of Samples 5 to 7, 20% was compounded with respect to the total amount of (pure Al) + (precursor composite).

From the above results, the following has become clear. (1) up to about the composition range of the sample 7, although room temperature strength is low, A2018-T ₆ in 300 ° C. or higher (Comparative Example 1) or more strength can be expected. However, if the composition ratio of the precursor composite is shifted to the Al side, it is difficult to obtain a uniform precursor composite, strength cannot be expected, and it takes a long time to discharge from the container, which increases the number of steps. (2) When the precursor composite of Sample 5 is used, the extrudability deteriorates, but this is due to Al + Ti → TiA in the extrusion process.
These can lead to the formation of these, such as 1 → Al ₃ Ti, which means that Al and T
It is judged from the three-phase state of iAl and Al ₃ Ti. (3) Even if only 20 vol% of the precursor composite of Sample 5 is composited as a whole, 12.9 wt% of expensive Ti is used, so that the material cost is significantly increased. (4) Compared with Sample 6, the composition ratio of Sample 5 does not differ greatly in strength. Rather, the strength of sample 6 is higher at 500 ° C. Therefore, the composition ratio of the precursor composite shown in Example 3 is about 25 to about Ti, centering on the stoichiometric composition of Al ₃ Ti.
It is preferable that 45 wt% and the balance be Al. In addition, T
Nb, V, Y, Mo, Zr, S in addition to the elements of i and Al
Even when at least one element of i, Mn, Fe, Co, Ni, Hf, and Cr is added as the third element to obtain a precursor composite, the Ti content is set to 25 to 45 wt%, and the third element is added.
The element is 3 to 15 wt%, and the balance is Al including inevitable impurities. This is an essential element for ensuring the hardness of the reinforcing particles after the subsequent hot extrusion, and contributes to the improvement of the strength of the raw material itself. If the addition of the third element exceeds 15 wt%, the effect originally aimed by the present invention is impaired.

[0034]

According to the present invention, the following effects can be obtained. 1. Softer than ceramics (hardness Hv 600) A
Since the l ₃ Ti particles are used as the reinforcing particles, the machinability is remarkably good. 2. Since it has the property of having the lowest elongation at around 300 ° C, it has excellent creep resistance. 3. Even if kept at each temperature for 100 hours, there is almost no decrease in strength as compared with the case of holding for 1 hour. That is, a thermally stable material can be obtained, and the effect is particularly remarkable at 300 to 500 ° C. 4. It is not necessary to use an expensive Al ₃ Ti intermetallic compound as a starting material, and a material in which Al ₃ Ti is uniformly and finely dispersed can be obtained. 5. Depending on the composition ratio, the elongation can reach nearly 20%, and the shape of the component can be imparted at low cost by cold forging.

[Brief description of drawings]

FIG. 1 is an explanatory diagram of a manufacturing process (process A) according to the present invention.

FIG. 2 is an explanatory diagram of a manufacturing process (process B) of the present invention.

FIG. 3 is an explanatory diagram of an attritor used in an embodiment of the present invention.

FIG. 4 is a photograph, instead of a drawing, showing the structure of a mixed powder obtained in the Example of Process A of the present invention.

5 is a photograph as a substitute for a drawing showing a metallographic structure of a material cross section obtained in the example of the same process A. FIG.

FIG. 6 is a photograph instead of a drawing, showing the structure of a precursor composite powder obtained in Example of Process B of the present invention.

FIG. 7 is a photograph as a drawing showing a structure of a powder obtained by compounding a precursor composite powder and a pure Al powder obtained in the example of the same process B.

FIG. 8 is a photograph instead of a drawing, which shows a metallographic structure of a material cross section obtained in the example of the same process B.

FIG. 9 is an X-ray diffraction chart of a powder obtained by compounding the precursor composite powder and the pure Al powder obtained in the example of the same process B.

FIG. 10 is an X-ray diffraction chart of a hot extruded bar using the powder compounded by the same process B.

FIG. 11 is a phase diagram of an Al—Ti 2 element.

[Explanation of symbols]

 1 Attritor 2 Agitator 3 Ball

Claims (21)

[Claims] 1. Pure Al powder or Al alloy powder is mixed with Al
_A method for producing an Al ₃ Ti dispersion strengthened aluminum alloy powder, comprising mixing ₃ Ti powder and subjecting the mixed powder to mechanical alloying treatment. 2. The mixing ratio of the Al ₃ Ti powder is 5 in total.
The method for producing Al ₃ Ti dispersion-strengthened aluminum alloy powder according to claim 1, wherein the content is about 45 wt%. 3. Al ₃ Ti dispersion strengthening according to claim 1, wherein alcohol is used as a dispersant during the mechanical alloying treatment, and the amount of carbon mixed from the residue of the alcohol is 1% by weight or less. Method for producing aluminum alloy powder. 4. A pure Al powder and a pure Ti powder are mixed, and the mixed powder is mechanically alloyed to obtain Al ₃ Ti.
To prepare a precursor composite powder systems, the progenitor composite powder, and further mixed with pure Al powder, again, a composite of precursor complexes of Al ₃ Ti system which comprises treating mechanical alloying aluminum Method for producing alloy powder. 5. The mixing ratio of the pure Ti powder and the pure Al powder of the precursor composite is 25 to 45% by weight of Ti, preferably 35.
The method for producing an Al ₃ Ti-based precursor composite powder according to claim 4, wherein the balance is ˜39% by weight and the balance is Al. 6. The mixing ratio of the precursor composite powder in the case of mixing the precursor composite powder and the pure Al powder is 5 to 45% by weight based on the whole amount. 1. A method for producing an aluminum alloy powder, which is a composite of the Al ₃ Ti-based precursor composite according to claim 1. 7. The Al ₃ Ti-based precursor according to claim 4, wherein an alcohol is used as a dispersant during the mechanical alloying treatment, and the amount of carbon mixed from the residue of the alcohol is 1% by weight or less. The manufacturing method of the aluminum alloy powder which compounded the compound. With 8. Al ₃ Ti dispersion strengthened aluminum alloy powder produced by the method according to any one of claims 1 to 3, after the billet molding, reinforced Al ₃ Ti dispersion, characterized by hot working Aluminum alloy manufacturing method. 9. An aluminum alloy powder composited with the Al ₃ Ti-based precursor composite produced by the method according to claim 4 is used to form Al _{3 in a} process from forming a billet to hot working. and reaction products of Ti, Al _3, characterized in that to disperse the Al ₃ Ti in the Al matrix
A method for producing a Ti dispersion strengthened aluminum alloy. 10. The particle size of the Al ₃ Ti particles dispersed in Al is 20 μm or less.
The method for producing an Al ₃ Ti dispersion strengthened aluminum alloy according to 1. 11. Al produced by the method of claim 8.
₃ Ti dispersion strengthened aluminum alloy. 12. The Al ₃ Ti dispersion strengthened aluminum alloy according to claim 11, wherein the total oxygen amount after hot working depending on the oxidation amount of the alloy powder is 5% by weight or less. 13. An Al produced by the method of claim 9.
₃ Ti dispersion strengthened aluminum alloy. 14. The Al ₃ Ti according to claim 13, wherein the total amount of oxidation (as the amount of Al ₂ O ₃ ) after hot working depending on the amount of oxidation of the alloy powder is 5% by weight or less. Dispersion strengthened aluminum alloy. 15. The precursor composite according to claim 4, comprising 25 to 45 wt% of Ti, Nb, V, Y, Mo, Zr, Si,
The Al according to claim 4, wherein at least one element of Mn, Fe, Co, Ni, Hf, and Cr (these are X) is 3 to 15 wt% and the balance is Al containing inevitable impurities. _{3 A} method for producing an aluminum alloy powder compounding a Ti-based precursor composite. 16. The mixing ratio of the precursor composite powder, when mixing the precursor composite powder and the pure Al powder, is 5 to 45% by weight based on the whole. 1. A method for producing an aluminum alloy powder comprising a composite of (Al, X) ₃ Ti based precursor composite. 17. The (Al, X) according to claim 15, wherein alcohol is used as a dispersant during the mechanical alloying treatment, and the amount of carbon mixed from the residue of the alcohol is 1% by weight or less. _{3 A} method for producing an aluminum alloy powder compounding a Ti-based precursor composite. 18. From billet molding to hot working, using an aluminum alloy powder composited with an (Al, X) ₃ Ti-based precursor composite produced by the method according to claim 15. (Al, X) ₃ Ti-based intermetallic compound is generated by reaction in the step, and the intermetallic compound is dispersed in the Al matrix (Al, X) ₃
A method for producing a Ti-based intermetallic compound dispersion strengthened aluminum alloy. g 19. The (Al, X) ₃ Ti-based intermetallic compound dispersion strengthened aluminum alloy according to claim 18, wherein the intermetallic compound particles dispersed in Al have a particle size of 20 μm or less. Production method. 20. An (Al, X) ₃ Ti-based intermetallic compound dispersion strengthened aluminum alloy produced by the method of claim 18. 21. The (Al, X) ₃ Ti-based intermetallic compound according to claim 20, wherein the total oxygen content after hot working depending on the oxidation content of the alloy powder is 5% by weight or less. Dispersion strengthened aluminum alloy.