JP2002194469A - Cu-Al-Si BASED ALLOY POWDER - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide Cu-Al-Si based alloy powder which further has high strength, high thermal conductivity and high electric conductivity without deteriorating the characteristics of a binary alloy of Al-Si. SOLUTION: The powder is produced by rapidly solidifying the molten metal of an alloy containing Cu, Al, Si and M (wherein, M is one or more kinds of elements selected from the groups consisting of Fe, Ni, Cr, Co, Mn, Zr, V and Ti). The powder has a composition of SixCuyMzAl(100-x-y-z) (wherein, x, y and z denote atomic %, and, 15<=x<=40, 0<y<=22.5, 5<=z<=20 and 35<=100-x-y-z<=60 are satisfied), and an amorphous phase is contained at least in part.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

TECHNICAL FIELD The present invention relates to a Cu-Al-Si
It relates to a series alloy powder.

[0002]

2. Description of the Related Art Al-Si alloys are lightweight and have high strength.
Excellent heat resistance, abrasion resistance, thermal conductivity, and low thermal expansion coefficient. Powder metallurgy for various parts of automobile engines, cylinder liners for motorcycles, rotors for compressors, cylinders for VTRs, etc. Widely used as product material. For this reason, Al-Si alloys are often used in the form of powder, and atomized powder is widely used in terms of spherical shape and handling properties. As a typical production method of atomized powder,
There is a rotating water atomization method. As shown in FIG. 1, this rotary water flow atomizing method flows down a molten alloy into a swirling cooling liquid and rapidly solidifies the molten alloy.
This is for producing an alloy powder.

[0003]

In the above powder metallurgy product, a compact having a high true density can be obtained by hot working such as hot extrusion, hot pressing, and HIP (hot isostatic pressing). Since such a molded article is excellent in thermal conductivity and has a low coefficient of thermal expansion, it can be applied to, for example, a portable electronic device, a heat sink of an optical communication package, but is insufficient in hardness. Was. Also, utilizing the characteristics of the powder described above,
For example, even when Al-Si alloy powder is applied as a thermal spray material to a heat dissipation substrate such as a hybrid car,
It was insufficient in hardness. In addition, the conductivity of the Al-Si alloy is not sufficient, and is not often applied to applications requiring conductivity.

[0004] It is an object of the present invention to provide a high hardness, high heat conductivity,
An object of the present invention is to provide a Cu-Al-Si alloy powder having high conductivity.

[0005]

In order to solve the above-mentioned problems, a Cu-Al-Si-based alloy powder according to claim 1 of the present invention comprises Cu, Al, Si and M (where M is Fe, N
i, Cr, Co, Mn, Zr, V, and at least one element selected from the group consisting of V) is a powder produced by rapidly solidifying a molten alloy containing an alloy melt, the composition of the powder being: _{Si x Cu y M z Al (} 100-xyz) ( where,
x, y and z represent atomic%, 15 ≦ x ≦ 40, 0 <y
≤22.5, 5≤z≤20, and 35≤100-x-
yz ≦ 60), and at least partly has an amorphous phase. In the present specification, “rapid cooling” means that the cooling rate is 10 ³ K / s or more, preferably,
It means cooling of 10 ⁵ K / s or more. Cooling rate of 10 ³ K
Examples of the rapid solidification method of / s or more include water atomization, gas atomization, spraying, cavitation, spark erosion, and injection into a rotating liquid. In addition, examples of the rapid solidification method having a cooling rate of 10 ⁵ K / s or more include a rotary liquid atomizing method and a single roll method.

The Cu-A according to claim 2 of the present invention.
The l-Si alloy powder is Cu, Al, Si and M (however,
And M is Fe, Ni, Cr, Co, Mn, Zr, V and
One or more elements selected from the group consisting of Ti)
Powder produced by rapid solidification of molten alloy
Powder, the composition of the powder is Si_xCu_yM_zAl_(100-
xy-)(Where x, y and z represent atomic%, and 25 ≦ x ≦
35, 0 <y ≦ 15, 7.5 ≦ z ≦ 17.5, 10 ≦ y +
z ≦ 32.5 and 40 ≦ 100−x−y−z ≦ 55)
And the whole is substantially composed of an amorphous phase.
is there.

[0007]

[Function and effect] Rapid solidification in binary Al-Si alloy
However, because of the composition of the alloy, the entire structure is crystalline,
High hardness could not be obtained. However,
As described in claim 1, Cu, Al, Si and M (provided that
And M is Fe, Ni, Cr, Co, Mn, Zr, V and
One or more metals selected from the group consisting of Ti)
Rapid solidification of molten alloy_xCu_yM_zAl
_{(100 -xy}ー_z)(Where x, y and z represent atomic%, 15
≦ x ≦ 40, 0 <y ≦ 22.5, 5 ≦ z ≦ 20, and
35 ≦ 100−xyz ≦ 60)
Then, the obtained Cu-Al-Si-based alloy powder is less
In both cases, an amorphous phase is formed partially. amorphous
By forming a phase at least partially, Cu-A
The hardness of the l-Si alloy powder increases several times. further,
Because it contains Cu, compared to Al-Si binary alloy
Thus, the electrical conductivity and the thermal conductivity are also improved.

[0008] When the rotary liquid atomizing method is used as the rapid solidification method, the obtained Cu-Al-Si alloy powder is different from the angular powder obtained by pulverizing an alloy lump. Sintering, HIP
It is suitable not only for powder metallurgy, but also as a thermal spray material. Since the sintered body has high hardness and excellent thermal conductivity,
It is particularly suitably used as a heat sink for portable electronic devices and optical communication packages.

According to a second aspect of the present invention, Cu, A
1, Si and M (where M is Fe, Ni, Cr, Co,
(Mn, Zr, V and one or more elements selected from the group consisting of Ti)).
_{i x Cu y M z Al (} 100-xy chromatography _z) (where, x, y and z represent atomic%, 25 ≦ x ≦ 35,0 < y ≦ 15,7.5 ≦
z ≦ 17.5, 10 ≦ y + z ≦ 32.5, and 40 ≦ 1
When a powder satisfying (00−x−y−z ≦ 55) is produced, the obtained Cu—Al—Si based alloy powder has a substantially amorphous phase as a whole. The hardness of the Cu-Al-Si-based alloy powder is further improved as compared with a powder having an amorphous phase only partially.

[0010]

DESCRIPTION OF THE PREFERRED EMBODIMENTS Embodiment 1 In Embodiment 1,
A method for producing a Cu-Al-Si-based alloy powder having an amorphous phase in part will be described. The Cu-Al-Si alloy powder is prepared by rapidly solidifying a molten alloy. As the rapid solidification method, an atomizing device (1
(0), a rotating liquid atomizing method will be described as an example, but it can also be produced by a water atomizing method, a gas atomizing method, a spray method, a cavitation method, a spark erosion method, a rotating liquid injection method, or the like. .
The atomizing device (10) includes an injection crucible (50) for supplying a molten metal (56) and a molten metal (5) injected from the injection crucible (50).
A cooling container (42) for rapidly solidifying 6) is provided. As shown in FIG. 1, the injection crucible (50) is a container having an injection hole (52) at the lower end, and a high-frequency heating coil (54) is provided on the outer periphery. The crucible (50) has a final composition ratio of Six _x
Cu _y M _z Al _(100-xy - _z) (where M is Fe, Ni, C
at least one element selected from the group consisting of r, Co, Mn, Zr, V and Ti, x, y and z represent atomic%, 15 ≦ x ≦ 40, 0 <y ≦ 22.5, 5 ≦ z ≦ 2
0 and 35 ≦ 100−x−y−z ≦ 60) are charged, and the metal material is heated by the heating coil (54) to obtain a molten metal (56).

When a pressurized pressure medium such as an inert gas is supplied into the crucible (50), the molten metal (56) is ejected from the injection hole (52) due to an increase in the internal pressure.

The diameter of the cooling container (42) is reduced downward, and the cooling liquid is swirled along the inner wall to form a cooling liquid layer (44). The molten metal (56) flowing down from the crucible (50) is rapidly solidified in the cooling liquid layer (44) to form powder. A Cu-Al-Si alloy powder having an amorphous phase in part is produced. When a high-pressure gas is injected into the flowing molten metal (56), the particle size of the obtained powder can be reduced due to the gas dividing pressure.

[0013] The Cu-Al-Si alloy powder is suspended in the cooling liquid and discharged from the lower end of the cooling container (42) as a slurry. Remove water from the discharged slurry,
By drying, a Cu-Al-Si-based alloy powder partially having an amorphous phase is obtained.

In the case of the single-roll method, since the alloy is obtained in the form of a ribbon instead of a powder, the obtained ribbon body may be appropriately pulverized into powder having a desired particle size. In addition, in the case of the rotary injection method, an alloy can be obtained in the state of a wire.

[0015] "Embodiment 2" whole Cu-Al-Si alloy powder is substantially amorphous phase, the final composition _{ratio, Si x Cu y M z Al} (100-xy chromatography _z) (where, M Is Fe,
At least one element selected from the group consisting of Ni, Cr, Co, Mn, Zr, V, and Ti, x, y, and z represent atomic%, 25 ≦ x ≦ 35, 0 <y ≦ 15, 7.5
≦ z ≦ 17.5, 10 ≦ y + z ≦ 32.5, and 40 ≦
(100-x-y-z ≦ 55) by rapid solidification of the metal raw material. The preparation method is the same as in the first embodiment. By setting the content in the above-described composition range, a rapidly solidified powder substantially entirely composed of an amorphous phase can be obtained.

[0016]

Example 1 Example 1 By a rotating liquid atomizing method,
A powder of Si ₃₀ Cu ₂₀ Fe ₃ Ni _2.5 Cr ₂ Al _42.5 (composition range according to claim 1 of the present invention: invention example 1);
₃₀ Cu ₁₀ Fe ₅ Ni ₄ Cr _3.5 Al _47.5 powder (composition range according to claim 2 of the present invention: invention example 2) and Si ₅₀ A
3 kinds of Al-Si alloy powder of l ₅₀ (comparative example)
The X-ray diffraction pattern was measured.

FIG. 2 shows the results. Referring to FIG. 2, the powder of Inventive Example 2 shows no halo pattern without peaks of Al and Si, indicating that the entire powder is substantially in an amorphous state. In addition, the powder of Inventive Example 1 is:
Although a halo pattern is shown, a peak of Si is also observed, which indicates that both crystalline and amorphous phases are mixed. On the other hand, in the comparative example, no halo pattern was observed, and peaks of Si and Al were observed, indicating that the whole was crystalline.

Example 2 The hardness of the powders of Inventive Example 2 and Comparative Example was measured using a Micro Vickers hardness tester.
(Hv) was measured. The measurement was performed ten times under the condition of a load of 50 g, and the average value of each was calculated. The results are shown in Table 1.

[0019]

[Table 1]

Referring to Table 1, it can be seen that Inventive Example 2 is about four times as hard as Comparative Example.
This is because the powder of Inventive Example 2 was entirely in an amorphous state, while the powder of Comparative Example was crystalline. Inventive Example 1 was also measured in the same manner. As a result, it was inferior to Inventive Example 2, but higher in hardness than the Comparative Example.

The Cu—Al—Si alloy powder of the present invention comprises:
Harder than crystalline Al-Si alloy powder, excellent in thermal conductivity and low in thermal expansion, suitable for hot press, HIP and other hot sintering materials, as well as thermal spraying materials ing. Further, the sintered body of the Cu-Al-Si-based alloy powder of the present invention has excellent thermal conductivity and a low thermal resistance value, and thus is suitable for a heat sink of a portable electronic device or an optical communication package. Further, the Cu-Al-S of the present invention
The i-based alloy has the property of reacting to lithium ions and has excellent conductivity, so it can be used as a negative electrode material for lithium ion batteries. There is.

The description of the above embodiments is for the purpose of illustrating the present invention, and should not be construed as limiting the invention described in the claims or reducing the scope thereof. Further, the configuration of each part of the present invention is not limited to the above embodiment, and various modifications can be made within the technical scope described in the claims.

[Brief description of the drawings]

FIG. 1 is an explanatory diagram of an atomizing device.

FIG. 2 is a graph showing X-ray diffraction patterns of Cu—Al—Si alloy powder and Al—Si alloy powder.

[Explanation of symbols]

 (10) Atomizing device (50) Injection crucible (56) Molten metal (42) Cooling vessel

 ────────────────────────────────────────────────── ─── Continuing from the front page (72) Inventor Yoshinobu Okumura 1-1-1 Hama, Amagasaki-shi, Hyogo F-term in Kubota Technology Development Laboratory Co., Ltd. 4K017 AA04 BA01 BB04 BB05 BB06 BB07 BB08 BB09 BB16 DA05 EB00 EC00 ED00 4K018 BA08 BB07

Claims (2)

[Claims] 1. Cu, Al, Si and M (where M is F
e, one or more elements selected from the group consisting of Ni, Cr, Co, Mn, Zr, V, and Ti), which is a powder produced by rapidly solidifying an alloy melt containing is, Si _x Cu _y M _z Al
_(100-xyz) (where x, y and z represent atomic%, 15
≦ x ≦ 40, 0 <y ≦ 22.5, 5 ≦ z ≦ 20, and
35 ≦ 100−x−y−z ≦ 60), and at least a part thereof has an amorphous phase.
Al-Si alloy powder. 2. Cu, Al, Si and M (where M is F
e, one of at least one element selected from the group consisting of Ni, Cr, Co, Mn, Zr, V and Ti), which is a powder produced by rapidly solidifying a molten alloy containing is, Si _x Cu _y M _z Al
_(100-xyz) (where x, y and z represent atomic%, 25
≦ x ≦ 35, 0 <y ≦ 15, 7.5 ≦ z ≦ 17.5, 10
≤y + z≤32.5 and 40≤100-xyz
≦ 55), wherein the Cu-Al-Si alloy powder is substantially composed of an amorphous phase.