JPH06122933A - High ductility aluminum sintered plastic flow alloy, its manufacturing method and its use - Google Patents

Abstract

(57) [Summary] [Object] An object of the present invention is to provide a high-strength, high-ductility Al-Si based sintered alloy, a method for producing the same, and a use thereof. [Structure] The present invention is Si 1 to 45%, Group IIIa element 0.1
~ 20%, at least one element of group IVa and Va, 0.0
It is in a die-forged sintered alloy consisting of 1 to 5% and the balance substantially consisting of Al. Furthermore, Cu 0.01-5%, Mg 0.01
~ 5%, Fe 2.0% or less, Mn 1.5% or less and Co
One or more of 1.5% or less can be contained, and the amount of oxygen becomes 0.15% or less by sintering in vacuum. The present invention is used for automobile parts such as pistons and scroll compressors. [Effect] According to the present invention, an Al-Si based sintered alloy having a tensile strength of about 40 kg / mm ² or more and an elongation of 1.5 or more at 150 ° C can be obtained.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a new high-strength, wear-resistant Al plastic fluidized-sintered alloy, which is particularly excellent in loss wear resistance and plastic workability of a mating material or machinability. TECHNICAL FIELD The present invention relates to an aluminum-silicon based plastic fluidized-sinter alloy, a method for producing the same, and various applications using the alloy.

[0002]

2. Description of the Related Art Conventionally, as wear-resistant Al alloys, JIS standards AC8A and A390 have been manufactured by a melt casting method. However, in the melt casting method, Al with high Si content
-The manufacture of Si-based alloys is difficult. That is, when the amount of Si is more than the eutectic, coarse primary crystal Si is crystallized, the strength is lowered, and there is a problem in plastic workability, and there is a drawback that the hard and coarse primary crystal Si wears the counterpart material. Currently, there is a demand for smaller size, lighter weight and higher performance.
It was necessary to improve plastic workability, machinability and wear resistance.

Therefore, in recent years, Al-S has been produced by powder metallurgy.
i-Fe system, Al-Si-Mn system, and Al-Si-Ni system sintered alloys have been developed. In the method for producing these alloy powders, a predetermined alloy composition is melted, a rapidly solidified powder is produced by a gas atomizing method, etc., and the powder is shaped and then sintered or hot plastic worked to produce an alloy. In the rapidly solidified powder, the primary crystal Si is refined and uniformly dispersed, so that a high Si material having higher strength can be obtained as compared with the conventional melt casting method.

However, the sintered alloys of JP-A-64-56806 and JP-A-63-183148 produced by the rapid solidification powder sintering method can obtain high strength, but have extremely low toughness and a Charpy impact value. It is about 0.2 to 0.98 kg-m / cm ² . Further, in JP-A-60-131944, a rapidly solidified Al alloy powder and carbon powder are added in an amount of 0.5 to 10% by volume, and high strength cannot be obtained.

Next, JP-A-55-97447 discloses JP-A-60-1319.
As with No.44, high strength cannot be expected because graphite, sulfide, and fluoride, which are solid lubricating components, are added.

Further, JP-A-63-183148 and JP-A-1
-159345, JP2-61023, JP2-61
No. 024 and Japanese Patent Application Laid-Open No. 2-70036 disclose Si of 5 to 40%.
Cu, Mg, Mn, Fe, W, Ni, Cr, Co, C
Although it is disclosed that an alloy powder containing e, Ti, Zr, V, Mo and the like is molded and then an alloy is manufactured by hot plastic working, sufficient strength and toughness cannot be obtained.

[0007]

As described above, the conventional Al
-Si-Fe system, Al-Si-Mn system, Al-Si-N
Although the i-based sintered alloy has high strength, its toughness is low. Further, when a solid lubricant is added to the Al sintered alloy, the strength and toughness are extremely low. Therefore, there is a problem that the range of use is limited as a member to which a repeated impact force is applied and a high load sliding wear member.

An object of the present invention is to provide an Al plastic fluidized-sintered alloy having high strength and high toughness, a method for producing the same, and various applications using the alloy.

[0009]

The present invention is based on the weight of Si
1 to 45%, IIIa group element 0.1 to 20%, IVa group element and Va group element at least 0.01 to 5%, and the balance substantially consisting of Al, high ductility Al Sintered plastic flow alloy.

The present invention is based on the above alloy and contains Cu of 0.1 to 5%.
And Mg 0.1 to 5%, and further Fe2.0
% Or less, Mn 1.5% or less, and Co 1.5% or less.

Further, the present invention provides that, by weight, the Group IIIa element is 0.1.
1 to 20%, at least 1 of IVa group element and Va group element
A highly ductile Al sintered plastic flow alloy, characterized in that the seed is 0.01 to 5%, oxygen is 0.15% or less, and the balance substantially consists of Al. Based on this alloy, Si1 to 45%
May be included, and further, Mg 5% or less, Cu 10%
Below, Fe 20% or less, Mn 10% or less, Co 8% or less, W 5% or less, Mo 5% or less can be included. A lower oxygen content improves the ductility, but from the viewpoint of strength, it is better to contain 5 ppm or more. 50 to 500 ppm is preferable because both strength and ductility are high.

According to the present invention, the Si content is 45% or less from the hypereutectic amount, and the total number of Si particles having a particle size of 1 μm or less is 50 to 80%, and the particle size is more than 1 μm and 2.5 μm or less. High ductility Al calcination characterized by having 15 to 35% of particles, 5 to 20% of particles having a particle size of more than 2.5 μm and 5 μm or less, 5% of particles having a particle size of 5 μm or more, and the balance Al. It is in bond gold. Based on this alloy, group IIIa element 0.1
˜20%, 0.01 to 2% of at least one of IVa group element and Va group element, and 5% or less of Mg, C
u 10% or less, Fe 20% or less, Mn 10% or less, Co
At least one of 8% or less, W5% or less, and Mo5% or less can be included.

According to the present invention, by weight, Si 1 to 45%, IIIa
A molded body of an alloy powder having a group element of 0.1 to 20% and the balance of Al is degassed and sintered in a non-oxidizing atmosphere having an oxygen partial pressure of 2 × 10 ⁻³ mmHg or less to 90% of the theoretical density. % Or less, a method for producing a highly ductile Al sintered alloy. Based on this manufacturing method, it is particularly preferable to carry out sintering under a high vacuum of 10 ^-2 mmHg or less. The sintering method of the present invention can be applied to any of the above alloys, and a sintered body having an extremely small amount of oxygen can be obtained.

The present invention relates to the formation of an Al-based alloy containing 1 to 45% by weight of Si or an alloy powder containing 0.1 to 20% of a group IIIa element and / or 0.01 to 2% of a group IVa. The body is subjected to vacuum degassing and sintering at a high temperature of 350 ° C or higher and a melting point or lower under a vacuum of 10 ^-2 mmHg or less, then hot consolidation and upsetting, and then hot plastic working into a desired shape. The method for producing a high-ductility Al sintered alloy is characterized in that In particular, after sintering, primary processing with a die and further subjecting it to plastic working by a hot die in a die similar to the final product, this processing is performed directly using a hot extruded member. be able to.

After the final hot plastic working, a solution treatment and an aging treatment are carried out, and then the final product is formed by cutting.

The present invention may be used in each of the above-mentioned alloy compositions, which may be as-sintered, or may be hot-plasticized as it is, and then subjected to solution treatment and aging treatment after this processing. It is possible to form Si particles and intermetallic compound particles. Si grains are eutectic Si grains in hypoeutectic, and primary eutectic Si grains and eutectic Si grains are formed in hypereutectic.

According to the present invention, by weight, Si 1 to 45%, IIIa
A having 0.1 to 20% of group elements, 0.01 to 2% of at least one of IVa group elements and Va group elements, and the balance Al
l alloy powder, the above-mentioned IIIa, IVa,
The Al alloy powder is characterized by having a chrysanthemum pattern structure and a net structure in which the Va group element is concentrated. Based on this alloy powder, it is necessary to increase the content of the IIIa group element with respect to the IVa group and Va group elements. Based on this composition, the above-mentioned Cu, Mg, Fe, Mn, C
O, W, and Mo can be contained in similar contents.

The Al sintered alloy of the present invention is subjected to hot working by a die after sintering, and is subjected to solution heat treatment and aging treatment to be subjected to a cylinder block, a cylinder liner, a piston, a rocker arm, a connecting rod, a valve retainer. ，
It is applied to cylinder heads, buckets, shift forks, brake drums, valve spools, automobile parts such as brake master cylinders, vanes for compressors, rotors, Oldham rings, VTR tape guide cylinders, etc.

In particular, in the present invention, in a compressor provided with a fixed scroll and an orbiting scroll, at least one or both of the fixed scroll and the orbiting scroll have a Si content of 1 to 45% and a IIIa group element content of 0.1 to 20%. ， IVa
0.01-5% of at least one kind of group element and Va group element,
And a balance comprising a sintered plastic flow alloy having Al as the balance. Also, turn the orbiting scroll to A
l alloy, the fixed scroll can be cast iron,
Rapid start-up is possible by forming an Al alloy. The scroll has a pedestal with spiral teeth. In particular, this scroll has a tensile strength at 150 ° C. of 40 to 60 kg / mm ² , an elongation of 1.5 to 10%, and an average coefficient of thermal expansion at 20 to 300 ° C. of 14 to 22 × 10 ⁻⁶ / ° C. Preferably from 15 to 1
7 × 10 ⁻⁶ / ° C. is preferable.

[0020]

The present inventors have found that the conventional Al--Si--Fe system, A
It was found that the decrease in strength of the rapidly solidified powdered alloys of 1-Si-Mn type and Al-Si-Ni type is due to the weak bonding force between particles due to the residual oxide film on the particle surface.

Therefore, in the present invention, as a component for strengthening the bonding force between particles, Group IIIa elements, particularly Ce and IV of rare earth elements are used.
The present invention has been accomplished by finding that the combination of at least one of Group a and Group Va elements, especially Zr, is most effective in improving strength and toughness.

In the high-strength, wear-resistant Al-Si sintered plastic flow alloy of the present invention, Si improves wear resistance, but if the amount is less than 1% by weight, this effect is not sufficient and high strength can be obtained. Absent. On the other hand, when it is 45% by weight or more, the wear resistance is excellent, but the formability and plastic workability are remarkably lowered.

The alloy of the present invention can be divided into several stages according to the requirements of strength and wear resistance depending on the amount of Si contained. Each amount of Si is divided into the following stages, and is used according to the requirements of strength and wear resistance. (1) 1-6%, (2) 6%
Over 12% or less, (3) over 12% and 18% or less, (4)
18% to 30% or less, (5) 30% to 45% or less.

The sintered alloy of the present invention contains Cu, Mg, Fe, Mn, Co, W and M, which will be described later, based on these Si contents.
can contain o.

Group IIIa elements are effective in improving strength,
Outside the range of 0.1 to 20% by weight, the effect of improving the strength is insufficient. Further, the total amount with Si is preferably 65% by weight or less, and when it exceeds 65% by weight, the plastic workability of the alloy is significantly deteriorated. Particularly, 0.5 to 10% is preferable, and 1 to 5 is more preferable.
% Is preferred.

IIIa group elements include Sc, Y, lanthanide group (La, Ce, Pr, Nd, Pm, Sm, Eu, Gd,
Tb, Dy, Ho, Er, Tm, Yb, Lu) and actinides (Ac, Th, Pa, U, Np, Pu, Am,
Cm, Bk, Cf, Es, Fm, Md, No), and at least one of these elements can be used. Among these elements, rare earth elements are particularly preferable, and most of the Si particles in the solidification from the molten metal have a grain size of 1 μm.
It has a function of forming in an extremely small state of m or less. Among rare earth elements, misch metal (about 5
It is especially preferred to use an alloy of 0% La and about 50% Ce).

It should be noted that P and alkali metals (Li, Na, K, Rb, Cs, and Fr) are considered to be effective as elements substituting for the group IIIa with similar contents.

The IVa group element (Ti, Zr, Hf) and the Va group element (V, Nb, Ta) are combined with the IIIa group element to solidify Si from the molten Al alloy containing Si.
It is contained in an amount of 0.01% or more in order to form fine grains. However, even if it exceeds 5%, no further effect is observed, and the ductility is lowered, so it is made 5% or less. In particular,
0.1 to 3% is preferable, and 0.5 to 2% is more preferable.
Group IVa elements are preferred, and Zr is particularly preferred.

The combination of the group IIIa element with the group IVa and group Va is S when solidifying from an Al alloy containing Si.
The i grain is formed finely, and the effect of suppressing the growth of the Si grain is observed even during the sintering process. The distribution of the Si grain is 50 to 80% when the grain size is 1 μm or less, and the grain size is 1 μm.
˜2.5 μm can be 15 to 30%, 2.5 to 5 μm can be 5 to 20%, and 5 μm to 10 μm can be 5% or less. Then, these elements are formed as an alloy powder in a chrysanthemum pattern structure that is thought to be formed by the concentration of these elements in the surroundings of Si particles, which suppresses the growth of Si particles during solidification and sintering. At the same time, it seems that the cleavage fracture of Si grains is eliminated and ductility is enhanced.

Particularly, Si particles having a particle size of 1 μm or less are 60 to 80%, and particles having a particle size of 1 to 2.5 μm are 22 to 30.
%, 2.5 to 5 μm is 7 to 15%, 5 to 10 μm
2% or less is preferable. By making the Si grains finer, a high ductility is obtained and the formability is also improved. Also, the fracture surface of Si is small in the fracture surface, and a temple fracture surface can be obtained.

The chrysanthemum pattern around the Si particles of the Al alloy powder is obtained by combining the above-mentioned elements and the amount of Si, and the amount of IIIa group element is larger than the amounts of IVa group and Va group element, IVa
It can be obtained by setting the amount of group and Va group to be not more than 0.20 of the amount of Si.

The sintered alloy of the present invention contains the above-mentioned Group IIIa element and IV
Combined with group a and Va group elements and ^{3 in} a non-oxidizing atmosphere under vacuum or oxygen partial pressure of 2 × 10 ⁻³ mmHg or less.
By degassing and sintering at 50 ° C. or higher, the oxygen content in the alloy is reduced to 0.15% or less. Thereby high ductility is obtained. The amount of oxygen can be set to 0.15% or less. Particularly, it is 0.10% or less, more preferably 0.1%.
It is preferable to set it to 05% or less.

The above aluminum powder alloy is produced by the air and nitrogen or argon gas atomizing method. In the case of an alloy component added to supersaturation, this is S in the casting method.
The i particles are coarsened, which adversely affects the strength and wear resistance. Therefore, the atomizing method is an appropriate manufacturing method for finely dispersing Si particles. A billet obtained by compression-molding such an aluminum powder alloy by cold isostatic pressing (CIP) is subjected to solid-phase sintering at a temperature of 460 to 500 ° C. in an inert gas such as vacuum, nitrogen or argon for densification. Particularly, in this sintering, it is not necessary to increase the density to 90% or more, and it may be about 70 to 90%. Since voids remain inside and have internal defects, it is more preferably 250 to 4
It is densified by recompressing by hot die compression at 50 ° C. at 4.5 ton / cm ² or more, particularly 5 to 9 ton / cm ² . Molding with a die is made into a shape similar to the final shape by a process of multiple steps. Further, for the plastic working with this die, a blank obtained by cutting a hot-extruded and densified billet can be used. The sintered alloy obtained by such a manufacturing process becomes a stable precipitate or an intermetallic compound from a metastable precipitate dissolved in supersaturation, and even if it receives a thermal history of a temperature lower than the recompression heating temperature. Strain deformation is less likely to occur because the precipitate does not re-dissolve or precipitate. However, in order to obtain higher strength, the sintered alloy is preferably 400
The solution treatment is performed by heating at ~ 520 ° C and then cooling with water to 100
˜200 ° C. In particular, age hardening treatment at 150 to 200 ° C. achieves high strength. Especially, the aging treatment is Cu and M
Preference is given to alloys containing g.

The alloy powder of the present invention is preferably solidified at a cooling rate of 50 ° C./second or more. The particle size of the powder is preferably 350 mesh or less, and particularly preferably 30 μm or less.

The forming process before sintering is preferably 2.5 ton / cm ² or more, and particularly preferably 3 to 5 ton / cm ² .

Cu and Mg are added as 0.1% or more each as an age hardening element for precipitating an intermetallic compound by aging treatment and improving the strength of the matrix. On the other hand, if it exceeds 5%, the toughness decreases, so it should be 5% or less. Therefore, Cu is 0.1-5 wt% and Mg
Is 0.1 to 5% by weight, the hardness of the matrix is the highest and the strength is improved. In particular, Cu2-5%, Mg0.
1 to 1% is preferable. When the oxygen content in the alloy is 0.15% or less, Cu can be contained up to 10%.

In order to improve the strength and heat resistance of the present invention, the content of Fe is 2.0% or less, Mn is 1.5% or less, and Co is 1.5% or less for alloys containing Cu and Mg. It may contain at least one selected or two or more selected. These elements form an intermetallic compound with Al to improve alloy strength and heat resistance. However, the content of each of these elements is preferably 0.01% or more. On the contrary, if the content of each of these elements exceeds the above range, the alloy strength decreases and the alloy becomes brittle.

In addition, the alloy of the present invention has an oxygen content of 0.15%.
When: Fe20% or less, Mn10% or less, Co8
% Or less, W5% or less, and Mo5% or less, and the total content of these elements is preferably 20% or less. Especially Fe5 ~ 13%, Mn2 ~ 5%, Co0.5
-3%, W1-3%, Mo1-3% are preferable.

According to the present invention, in a compressor scroll having a pedestal with spiral teeth, the teeth are formed substantially at right angles to the pedestal, and the curvature of the base of the pedestal and the end of the teeth. The corners have a curvature of 0.1 to 0.5 mm, and preferably have an elongation at room temperature of 1% or more. In particular, by using an Al sintered plastic flow alloy of hypereutectic Si having an elongation of 2% or more, the tooth thickness can be set to 1 to 5 mm, and the outer diameter of the scroll is 0.015 mm. ~
It can have a thickness of 0.05 mm. Particularly, it is preferable that the outer diameter of 1 mm is 0.02 to 0.04 mm.
The height of the teeth is preferably 0.1 to 0.3 mm per 1 mm of the scroll outer diameter, and more preferably 0.15 to 0.25 mm.

The plastic flow of the present invention is carried out by subjecting a compacted product of 95% or more to a mold and / or hot extrusion,
A convex portion having a length of 2 times or more (preferably 3 times or more) or 10 mm or more is formed from the flat member. Particularly in a scroll, since the tooth portion is subjected to plastic flow with a high processing rate, it is possible to obtain a high density and high strength ductility. In particular, in the specific composition of the present invention, the coefficient of friction of flake graphite cast iron with FC25 is initially 0.07 or less, the final is 0.025 or less, the seizure load is 200 to 500 kg / cm ² , and the HRB is 80 or more,
Tensile strength 40kg / mm ² or more, fatigue strength 5 at R0.1mm
kg / mm ² or more, permanent deformation (150 ° C, 300h) 2μ
m / 15.83 mm or less is obtained. By using such a material, the tooth thickness is 1.5 to 2.8 mm and the lap tip R0.
The width of the wrap can be set to 2 to 0.5 mm and the root of the lap R0.1 mm or less, and the fixed scroll can be set to the lap tip R0.1 mm or less and the lap root R0.01 mm or less with respect to the cast iron material.

[0041]

【Example】

Example 1 FIG. 1 is a perspective view of a partial cross-section compressor of a hermetic scroll compressor. This compressor is mainly composed of an orbiting scroll 1, a fixed scroll 2, a suction pipe 3, a discharge chamber 4, a case 5, an intermediate pressure chamber 6, a rotor 7, an auxiliary bearing 8, a lid 9, a stator 10, a chamber 11, a bottom 12, a frame. 13, the discharge pipe 14, and the crankshaft 15. This compressor is used for home or business use, and a scroll of 80 to 130 mmφ for home use and 200 to 300 mmφ for business use is used.

The orbiting scroll 1 shown in FIGS. 2 and 3 and the fixed scroll 2 shown in FIG. 4 were manufactured from the alloys shown in Table 1. Reference numerals 16 and 19 are pedestals, and 17 and 18 are tooth portions. The height of the teeth was 15 mm and the thickness was 2.7 mm. The diameter of the orbiting scroll was about 80 mm, and the teeth were almost straight without taper. The curvature of the root of the tooth was set to 0.5 mm. Then, similarly, solution heat treatment (490 ° C ×
After water cooling for 30 minutes and aging treatment (160 ° C. × 20 hours), the product was finished by machining. The fixed scroll is slightly larger than the orbiting scroll, and when they rotate, they come into contact with each other and slide with a slight gap. Even in the fixed scroll, the curvature of the root of the tooth part was set to 0.5 mm. 1 cap
It became 0 to 20 μm. The wall thickness of the teeth is 0 per 1 mm of outer diameter.
It has 034 mm and the height of the tooth portion is 0.18 mm per 1 mm. The height of the teeth is 0.19 mm per 1 mm outer diameter of the scroll.

[0043]

[Table 1]

As shown in the side view of FIG. 2 and the front view of the lower side thereof, 20 is provided with a groove on the entire side surface of the pedestal 19 necessary for performing the cutting work, and 21 stirs the oil in the chamber. Grooves are provided obliquely, and 22 is a recess for balancing the weight of the tooth portion 18 provided along the involute curve.

The manufacturing process of the orbiting scroll in this embodiment is shown in FIG. After being manufactured by the steps shown in the figure, a final product is obtained by cutting into the shapes shown in FIGS. 2 and 3. The forging is performed by upper and lower molds made of tool steel, and the molds are heated to the same temperature as that of the object to be molded in the atmosphere.

The characteristics of the Al sintered alloy in this example are shown in Table 2. The Si grains in the alloy have a diameter of 10
Approximately 25 pieces with a diameter of 15 μm per mm ² and a diameter of 5 to 1
0 μm is about 1400 per 1 mm ² , and other 5 μm
It was: The alloy powder was obtained by air atomization.

[0047]

[Table 2]

FIG. 5 is a front view of the fixed scroll used in this embodiment. This scroll is formed by die casting into a shape substantially shown in the figure, and the material is eutectic graphite cast iron of FCE20.

SCM314 case hardening steel is used for the shaft 15,
The tensile strength was 85 kg / mm ² or more, and the hardness after quenching was HB550 or more.

This compressor has two upper and lower parts for room air conditioners.
Split bearing, intermediate pressure lubrication, power consumption 950W, 1
00V; 6.6kW, low noise of 35db, low vibration gravity, fit finization, wide range of rotation speed 500 ~ 9000rpm, pressure ratio 1.2 ~ 9.2, maximum pressure Pd 32kg / c
m ² , used refrigerant R-22, refrigerator oil Sniso 4GSI is achieved. As an example of room air conditioner, power supply: single phase 2
00V, 50 / 60Hz, theoretical pushing amount: 12.5ml / r
ev, Nominal output: 1300W, Nominal cold power: 3220W / 2
900W, forced draft cooling.

Due to the compression principle of the scroll compressor, a compression chamber having an intermediate pressure between the suction pressure and the discharge pressure is formed. Gas can be injected into the compression chamber at this intermediate pressure with a simple structure. , It has a feature suitable for gas injection type capacity control (capacity increase).

FIG. 6 is an overall configuration diagram of the room air conditioner. The high-pressure and high-temperature gas discharged from the compressor is liquefied in the condenser and is supercooled to some extent. Next, it isenthalpically expanded through the first capillary tube and enters the gas-liquid separator to separate into saturated liquid and gas. The liquid is gasified through the second capillary tube and the evaporator and sucked into the compressor. On the other hand, the saturated gas is injected during the compression stroke of the scroll compressor by providing a gas injection circuit connecting the gas-liquid separator and the compressor.

The circulation amount of the refrigerant flowing through the condenser (indoor heat exchanger) increases during heating, and the enthalpy difference of the refrigerant in the evaporator increases during cooling. As a result, the heating capacity and the cooling capacity can be improved by about 15%. As a result, 2.2
2.5 kW, 3. 0 kW, 3.0 kW, 3.75 kW Compressor with a gas injection mechanism added to increase capacity 2.5 kW, 3.
3kW and 4.4kW can be generated.

By using the sintered alloy of the present invention, the formability at high temperature was extremely good, the swelling at the center of the tooth portion of the scroll was good, and the entire tooth portion could be formed. Further, it has been found that by using the alloy of the present invention, its ductility is high, so that there is no problem even if the curvature of the rising portion of the tooth portion is small, and as a result, highly efficient compression can be obtained. The intermetallic compounds could not be clearly distinguished by a microscope. Especially in room air conditioners, the inverter can be used for quick start-up and warm air
It is possible to let cold air come out.

Example 2 Using the alloy powder shown in Table 1, the orbiting scroll shown in FIGS. 2 and 3 was manufactured by the manufacturing process shown in FIG. The fixed scroll is the same as in the first embodiment. The scroll obtained in this example had substantially the same Si particles and mechanical properties as in Example 1. Further, the performance of the compressor was similar to that of the first embodiment.

Example 3 An orbiting scroll and a fixed scroll having the composition shown in Example 1 were manufactured by the same method to manufacture a compressor having substantially the same structure. Both surfaces were anodized. Similarly, a nickel salt and an acrylic resin are formed by electrolysis, electrolysis is performed using a silver salt aqueous solution on the surface, and the product obtained by impregnating with silver has very good initial familiarity and higher performance than Example 1. was gotten.

Example 4 Table 3 shows the chemical composition (% by weight) of the scrolls obtained by the production methods of Examples 1 and 2. The powder was obtained by rapidly cooling the molten metal by a gas atomizing method using air to produce each alloy powder. A powder having a particle size of 100 mesh or less was used. The material of the present invention is No. 1 to 8, and the comparative material is No. 9 to 13.

[0058]

[Table 3]

Table 4 shows the obtained scrolls for tensile test and bending test (thickness 5 mm, width 20 mm, length 40 mm).
And processed into a test piece for impact test, tensile test, 3
A point support bending test and a 5 kg Charpy impact test were carried out. As is clear from the results, the Al-Si-Ce of the present invention
Sintered alloys have a tensile strength equal to or higher than that of the comparative materials, and the impact value of 25% Si is 0.83 kg / m ² compared to 0.39 kg-m / cm ² . / Cm ² or more, and bending strength is 89 kg / mm ² for 72 kg / mm ^2.
That is all.

[0060]

[Table 4]

Further, a seizure resistance limit surface was obtained using the obtained sintered alloy. For the friction conditions, flake graphite cast iron (FC25) was used as the mating material, and the atmosphere was set in refrigerating machine oil (mixed oil of lubricating oil and refrigerant). As is known from the results, Nos. 1, 4, 5, 6 and 7 of the material of the present invention and No. 9 of the comparative material,
When compared with the amounts of 25% Si of 10, 11 and 12, the seizure limit surface pressure of the material of the present invention is 218 kg / cm ² or more, which is higher than those of the comparative materials.

The production method and characteristics of the material No. 6 of the present invention were examined. 1-5 to the molding process in the manufacturing process
When the pressure is changed to n / cm ² , the bending strength and the density are not increased in the subsequent manufacturing process at the molding pressure of ² ton / cm ² or less. Further, when the pressure is 3.5 ton / cm ² or more, the bending strength and the density become the highest, and it is preferable that the molding pressure is higher than that.

In the manufacturing process, the sintering temperature is set to 350.
When the temperature is changed from ℃ to 525 ℃, the strength and density are low and the reliability is poor at 400 ℃ or lower, so that the sintering temperature higher than that is preferable. Further, at 525 ° C or higher, the strength and the density are slightly reduced.

In the manufacturing process, the re-pressing pressure is set to 4 to 8 to
When the pressure is changed to n / cm ² , the bending strength and the density are low at a re-pressing pressure of 5 ton / cm ² or less, so it is preferable to set the pressure more than that. Further, if it is 7 ton / cm ² or more, there is no great improvement, but bending strength and density are almost constant and stable strength is obtained.

In the manufacturing process, the recompression molding temperature is set to 200 to
When the temperature is changed to 400 ° C, the re-pressing temperature is 200 ° C to 3
Bending strength and density increase linearly up to 00 ° C. In particular, the bending strength and the density become constant at 350 ° C. or higher, and stable characteristics are obtained. Therefore, it is preferable to set the re-pressing temperature at 350 ° C. or higher.

Example 5 The alloy powders shown in Table 5 were produced by the gas atomizing method in the same manner as in Example 3.

[0067]

[Table 5]

The Si particles of these alloy powders are almost the same as those in Example 3.
Was similar to. An alloy was manufactured using this alloy powder by the same manufacturing process as in Example 3. The particle size distribution of the Al alloy powder is such that the particle size of 45 μm or less is 50% or more, whereby the particle size of 150 μm is 45% or less, and the remaining 5% or less is 200 μm. Particle size 50, 60, 60,
5 to 1 for each particle size of 100 and 150 μm
2%.

Table 6 shows the room temperature, 150 ° C. tensile strength, elongation, bending strength and thermal expansion coefficient at room temperature to 200 ° C. of the obtained alloy. The tensile strength of the alloy of the present invention is 47 at room temperature.
kg / mm ² or more and 40 kg / mm ² or more at 0.99 ° C., respectively from 0.4 to 0.5 percent elongation rate, with 2.0 to 3.0%, even be higher both than the conventional It was

[0070]

[Table 6]

The atomized powder of the present invention has a chrysanthemum pattern in which Cu, Mg, Fe, Ce and Zr are concentrated around Si particles.
The tissue (hatched portion) is formed. Due to the inclusion of Ce and Zr, Si grains are formed extremely finely, and the Si grains are kept fine during sintering and recompression molding at high temperature. Out of all Si particles in the powder, 80% or more have a particle size of 2.5 μm or less, 95% or more have a particle size of 5 μm or less, and have a particle size of 10 μm or less. Although some Si particles are formed by gathering and appear as large particles, each Si particle is 10 μm or less as described above. Relatively large particles are primary crystal Si, and fine particles, elongated particles, and linear particles are eutectic Si. Cu, Mg, Fe, Ce and Z are partially contained in the surroundings of these eutectic Si.
The tissue in which r is concentrated is formed in the shape of elongated grains. Eutectic Si and this concentrated structure are formed in a net shape.
The slender particle-shaped alloy concentrated portion is indicated by diagonal lines.

According to the photomicrograph of No. 16, two kinds of Al, Si, Cu, Mg, Fe, Ce and Zr were obtained by the aging treatment.
An intermetallic compound with one or more species is formed, but not found in the optical texture. The distribution of Si particles is almost the same as No. 17 described above, but the Si particles are formed slightly larger.

Example 6 In place of Zr of No. 14 of Example 4, Ti of the same content,
One kind of Hf and Nb, and Y and S of the same content instead of Ce
An alloy powder in which one of m was contained in each of Ti, Hf, and Nb was manufactured in the same manner as above, and subjected to solution treatment and aging treatment after sintering and recompression molding under the same conditions as in Example 1.

Tensile tests at 150 ° C. were performed on these alloys. As a result, the tensile strength is 37-43kg / m
The m ² and the elongation rate were 1.5 to 3.0%.

Embodiment 7 FIG. 8 is a sectional view of a scroll compressor for a car air conditioner. This compressor mainly comprises an orbiting scroll 1, a fixed scroll 2, a discharge valve 23, a discharge port 24, a bearing ball 25,
Rotation preventing member 26, suction port 27, tip seal 2
8, ring 29, driven clutch 30, electromagnetic clutch 3
1, a balance weight 32.

The orbiting scroll 1 shown in FIGS. 9 and 10 was made of the alloy of Example 1 and the fixed scroll was constructed in the same manner as in Example 1. Manufacturing conditions are the same as in Example 1. The tooth height of the scroll is 15 mm, the thickness is 2.7 mm, and the curve at the root of the tooth is 0.5 mm, which is a straight tooth.

By using the alloy of the present invention, the moldability was high, and a product as the mold was obtained over the entire scroll. The particle size distribution of the Si particles and the intermetallic compound were the same as described above.

As a result of actual operation, it was found that highly efficient compression was obtained. Further, as in Example 3, the orbiting scroll subjected to alumite treatment had good initial familiarity. Further, the fixed scroll can also be made of an Al alloy in the same manner, and excellent characteristics can be obtained.

[0079]

According to the present invention, it is possible to provide an Al-Si based sintered alloy having high strength and excellent high temperature ductility with high productivity.
The present invention can be applied to a member to which a shock and a high load are applied, which has not been obtained with the conventional Al-Si-Fe based sintered alloy, in particular, to a scroll for a compressor. Products to which the present invention is applied include room air conditioners, car air conditioners, refrigerators, vacuum pumps, and the like.

[Brief description of drawings]

FIG. 1 is a partial cross-sectional perspective view of a hermetic scroll compressor.

FIG. 2 is a front view of an orbiting scroll for a hermetic scroll compressor.

FIG. 3 is a bottom plan view of FIG.

FIG. 4 is a manufacturing process drawing of an orbiting scroll.

FIG. 5 is a front view of a fixed scroll.

FIG. 6 is a system diagram of an air conditioner.

FIG. 7 is a manufacturing process drawing of an orbiting scroll.

FIG. 8 is a plan view of a scroll compressor for a car air conditioner.

FIG. 9 is a cross-sectional view of a scroll for a car air conditioner scroll compressor.

FIG. 10 is a sectional view of a scroll for a car air conditioner scroll compressor.

[Explanation of symbols]

1 ... Orbiting scroll, 2 ... Fixed scroll, 3 ... Absorption pipe, 4 ... Discharge chamber, 7 ... Rotor, 10 ... Stator, 11 ...
Cases, 16, 19 ... Pedestal, 17, 18 ... Teeth

 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Ryo Hiraga Ryo Hiraga 6-6 Kanda Surugadai, Chiyoda-ku, Tokyo Hitachi, Ltd. (72) Keiichi Nakamura 292 Yoshida-cho, Totsuka-ku, Yokohama, Kanagawa Hitachi, Ltd. Manufacturing Engineering Laboratory (72) Inventor Toru Iizuka 800 Tomita, Ohira-machi, Shimotsuga-gun, Tochigi Hitachi Living Equipment Division (72) Inventor Koichi Inaba 800 Tomita, Ohira-machi, Shimotsuga-gun, Tochigi Hitachi, Ltd. Living Equipment Division (72) Inventor Yusaku Nakagawa 3-10-2 Bentencho, Hitachi City, Ibaraki Prefecture Hitachi Kyowa Industry Co., Ltd.

Claims (23)

[Claims] 1. Si1-45% by weight, Group IIIa element 0.
1 to 20%, at least 1 of IVa group element and Va group element
High ductility Al sintered plastic flow alloy, characterized in that the seed is 0.01 to 5% and the balance substantially consists of Al. 2. Si1-45% by weight, Group IIIa element 0.
1 to 20%, at least 1 of IVa group element and Va group element
Species 0.01 to 5%, Cu 0.1 to 5%, Mg 0.1 to 5
%, And the balance consisting essentially of Al, a highly ductile Al sintered plastic flow alloy. 3. Si1-45% by weight, Group IIIa element 0.
1 to 20%, at least 1 of IVa group element and Va group element
High ductility Al sinter plasticity, characterized in that at least one of 0.01 to 5% of species, Fe of 2.0% or less, Mn of 1.5% or less, and Co of 1.5% or less, and the balance substantially consisting of Al. Fluid alloy. 4. Si1-45% by weight, Group IIIa element 0.
1 to 20%, at least 1 of IVa group element and Va group element
Species 0.01 to 5%, Cu 0.1 to 5%, Mg 0.1 to 5
%, Fe 2.0% or less, Mn 1.5% or less and Co 1.5
% Or less, and the balance substantially consisting of Al, a highly ductile Al sintered plastic flow alloy. 5. IIIa group element 0.1 to 20% by weight, IVa
0.01-5% of at least one kind of group element and Va group element,
Highly ductile Al sintered plastic flow alloy, characterized in that oxygen is 0.15% or less and the balance is substantially Al. 6. A Group IIIa element, by weight, of 0.1 to 20%, IVa
0.01-5% of at least one kind of group element and Va group element,
Si 1-45%, oxygen 0.15% or less, Mg 0-5%,
Cu0-10%, Fe0-20%, Mn0-10%, C
A high ductility Al sintered plastic flow alloy, characterized in that 0 to 8%, W 0 to 5%, Mo 0 to 5%, and the balance substantially consisting of Al. 7. IIIa group element 0.1 to 20% by weight, IVa
0.01-5% of at least one kind of group element and Va group element,
Si 1-45%, oxygen 0.15% or less, Mg 0-5%,
Cu0-10%, Fe0-20%, Mn0-10%, C
A high ductility Al sintered body for plastic flow processing, characterized in that o is 0 to 8%, W is 0 to 5%, Mo is 0 to 5%, and the balance is substantially Al, and is still sintered. 8. Si1-45% by weight, Group IIIa element 0.
1 to 20%, at least 1 of IVa group element and Va group element
Species 0.01 to 5%, Mg 0 to 5%, Cu 0 to 10%, F
e0-20%, Mn0-10%, Co0-8%, W0-
A highly ductile Al-processed member, characterized by comprising 5%, Mo 0 to 5%, and the balance substantially Al, and subjected to hot extrusion. 9. By weight, Si 1 to 45%, IIIa group element 0.1.
1 to 20%, at least 1 of IVa group element and Va group element
Species 0.01 to 5%, Mg 0 to 5%, Cu 0 to 10%, F
e0-10%, Mn0-10%, Co0-8%, W0-
5%, Mo 0 to 5%, and the balance consisting essentially of Al, which is subjected to hot extrusion after sintering, and has Si particles and intermetallic compound particles having a particle size of 10 μm or less, and high ductility. Al alloy member. 10. By weight, a Si content of 45 to 45
% Or less, the number of particles having a grain size of 1 μm or less out of all Si grains is 50
-80%, the number of particles whose particle size exceeds 1 μm and 2.5 μm or less is 1
5 to 35%, the number of particles having a particle size of more than 2.5 μm and 5 μm or less is 5 to 20%, the number of particles having a particle size of 5 μm or less is 5% or less, IIIa
Group elements 0.1 to 20%, IVa group elements and Va group elements 0.01 to
2%, Mg0-5%, Cu0-10%, Fe0-20
%, Mn 0 to 10%, Co 0 to 8%, W 0 to 5%, Mo
A highly ductile Al sintered plastic flow alloy characterized by 0 to 5% and the balance being substantially Al. 11. A non-oxidizing atmosphere having an oxygen partial pressure of 2 × 10 ⁻³ mmHg or less is obtained by molding an alloy powder compact containing Si 1 to 45%, IIIa group element 0.1 to 20% by weight, and the balance Al. A method for producing a highly ductile Al sintered alloy, characterized by being degassed and sintered in an atmosphere of 90% or less of a theoretical density. 12. Si-1 to 45%, IIIa group element 0.1 to 20%, IVa group element and Va group element 0.01 to 2 by weight.
%, And the balance of Al alloy powder compacts are sintered in a non-oxidizing atmosphere with an oxygen partial pressure of 2 × 10 ⁻³ mmHg or less, and are 90% or less of the theoretical density. Ductile Al
Manufacturing method of sintered alloy. In 13. wt, Si1～45% IIIa group elements from 0.1 to 20%, and hot molded body melting point below 10 ^-2 mmHg following vacuum at 350 ° C. or more alloy powders having Al balance A method for producing a highly ductile Al sintered alloy, characterized in that vacuum degassing sintering is carried out, followed by hot compaction and upsetting, and then hot plastic working into a desired shape. 14. Si-1 to 45%, IIIa group element 0.1 to 20%, IVa group element and Va group element 0.01 to 2 by weight.
%, And the alloy powder compact having the balance Al is 10 ^-2 mm
It is characterized in that vacuum degassing sintering is performed under a vacuum of Hg or less at a high temperature of 350 ° C. or more and a melting point or less, then hot compaction and upsetting are performed, and then hot plastic working is performed to a desired shape. A method for producing a high ductility Al sintered alloy. 15. Al containing from 1 to 45% by weight of Si
After degassing sintering of the base alloy powder compact under vacuum, hot plastic working is performed with a mold of the desired shape, and then hot plastic working with a mold similar to the final shape. A method for producing a highly ductile Al sintered alloy, which comprises: 16. A hot-extruded member of an Al-based sintered alloy containing 1 to 45% by weight of Si is subjected to hot plastic working in a die having a desired shape, and then a shape similar to the final shape is obtained. A method for producing a highly ductile Al sintered alloy, which comprises performing hot plastic working with a die. 17. A high-ductility Al, characterized in that a round bar billet is obtained by hot extrusion of a molded body of an Al-based alloy powder containing 1 to 45% by weight of Si and 0.1 to 20% of a group IIIa element. Manufacturing method of sintered alloy. 18. Al according to any one of claims 1 to 15.
Cylinder block, cylinder liner, piston, rocker arm, connecting rod, valve retainer, cylinder head, bucket, shift fork, brake drum, valve spool, brake master cylinder automotive parts, compressor vane, rotor, etc.
A member comprising at least one of an Oldham ring and a VTR tape guide cylinder. 19. A compressor provided with a fixed scroll and an orbiting scroll, wherein at least one of the fixed scroll and the orbiting scroll has a Si1 to 45% by weight,
A compressor comprising a plastic fluidized sintered alloy having a Group IIIa element of 0.1 to 20%, at least one group IVa element and a group Va element of 0.01 to 5%, and the balance Al. 20. A compressor and a scroll for a compressor provided with a spiral tooth portion on a pedestal, wherein the scroll is by weight,
It is characterized by comprising a plastic fluidized sintered alloy containing 1 to 45% of Si, 0.1 to 20% of IIIa group element, 0.01 to 5% of at least one of IVa group element and Va group element, and the balance of Al. Scroll for compressor. 21. A compressor scroll having a spiral tooth portion on a pedestal, wherein the scroll has a tensile strength at 150 ° C. of 40 to 60 kg / mm ² , and an elongation of 1.5 to 10%. Two
Average coefficient of thermal expansion at 0-300 ° C is 16-22 × 10 ^-6
A scroll for a compressor, which is made of a plastic fluidized Al sintered alloy having a temperature of / ° C. 22. In a scroll for a compressor having a pedestal with spiral teeth, the teeth are formed substantially at right angles to the pedestal, and the curvature of the base of the pedestal and the corners of the end of the teeth. Hypereutectic Si-containing Al having a curvature of 0.1 to 0.5 mm
A scroll for a compressor, which is made of a plastic fluidized sintered alloy. 23. In a compressor scroll having a pedestal with spiral teeth, the teeth are formed substantially at right angles to the pedestal, and the thickness of the teeth is 0 per 1 mm of the height of the teeth. .1
A scroll for a compressor, which is made of a hyper-eutectic Si-containing Al plastic fluidized-sintered alloy having a diameter of up to 0.25 mm.