JP3353834B2 - Easy-working high-strength copper alloy and its manufacturing method - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an easy-to-work high-strength copper alloy having high strength and high electrical conductivity suitable for materials for electronic and electrical equipment, and excellent in punching properties, machinability and heat resistance. The present invention relates to a high-strength copper-based sintered alloy and a method for producing the same.

[0002]

2. Description of the Related Art In recent years, there has been an increasing need for lighter, thinner and smaller electronic and electrical products, and the miniaturization and weight reduction of equipment used therefor has been promoted. Along with this, the demand for smaller, lighter, and higher performance parts has been further increased. For this reason, structural materials, connectors, lead frame materials, and the like constituting parts have been reduced in thickness, and materials having high strength and high electrical conductivity have been required. Further, these materials are required to have punching properties and machinability when working into a predetermined shape, and heat resistance to withstand a temperature rise during use.

[0003] Conductivity is a factor that determines the conductor resistance of electric wires, cables, connectors, and the like, and is expressed by the following equation. r _c = (K ₁ × K ₂ × K ₃ ) × 10 ⁵ / (58 × A × η) r _c : conductor resistance (Ω / km) A: conductor cross-sectional area (mm ² ) η: conductivity (%) K ₁ : Increasing rate due to twisting, etc. K ₂ : Increasing rate due to temperature coefficient of resistance K ₃ : Increasing rate due to skin effect and proximity effect Conductor cross-sectional area A by thinning connectors etc.
If decreases, the conductor resistance r _c is increased. But by improving the conductivity eta, it is possible to suppress an increase in the conductor resistance r _c. That higher conductivity η is large, conductor resistance r _c is small, the effective in thinning of such connectors and lead frames.

In order to reduce the thickness, it is necessary to increase the strength of the material. As a method to improve the strength of copper alloy,
Conventionally, a method utilizing aging precipitation has been known, and is applied to, for example, Cu-Be alloys, Cu-Ti alloys, Cu-Cr alloys, and the like. However, these alloys have a problem in that ductility is reduced by aging treatment, so that processing such as molding is difficult, and cracks and breaks occur. In addition, there is a problem that when the strength increases, the conductivity decreases.

Japanese Patent Application Laid-Open No. Hei 9-104935 discloses a high-strength conductive
A Cr-containing copper alloy and a method for producing the same are disclosed. This method melts a copper alloy containing Cr, and upon cooling and solidification from the melting zone, crystallizes Cr as a second phase and forms a two-phase composite material of Cu and Cr, thereby obtaining strength and conductivity. It is intended to produce a Cu-based alloy material having both of the above. However, this method has a problem that the management of operating conditions becomes complicated because the processing temperature and the processing rate when forming into a predetermined shape are limited to specific ranges. In addition, there is a problem that when the strength increases, the punchability and machinability decrease.

Japanese Patent Application Laid-Open No. 9-249925 discloses a method for producing a high-strength conductive high-Cr-containing copper alloy. This method aims to increase the strength without disturbing high conductivity by dispersing acicular Cr in copper. However, in this method, there is a problem that the punching property and the machinability decrease as the strength increases.

[0007]

DISCLOSURE OF THE INVENTION The present invention solves the above-mentioned problems, has high strength and high conductivity, and is excellent in punchability, machinability and heat resistance, and is an easily machined high-strength copper alloy. It is another object of the present invention to provide an easy-to-work high-strength copper-based sintered alloy and a method for manufacturing the same at low cost and easily.

[0008]

SUMMARY OF THE INVENTION The present invention, Ti Contact and total 0.1 to 30 wt% of one or two of Zr, 0.01 to the S
A composition containing 20% by mass or a total of 0.01 to 20% by mass of S and C, the balance being composed of Cu and unavoidable impurities, and a structure in which metal sulfides and / or metal complex carbosulfides are dispersed in a Cu matrix. It is an easy-working high-strength copper alloy having

In the invention of the above-mentioned easy-working high-strength copper alloy, as a first preferred embodiment, the metal sulfide is Ti ₃ S, T
It is preferable to use one or more of i ₂ S, TiS, Zr ₃ S ₂ and Zr S. As a second preferred embodiment, the metal complex carbonitride sulfide is preferably one or two of Ti ₂ CS and Zr ₂ C S.

[0010] The present invention, one or two of Ti contact and Zr total 0.1 to 30% by weight in the sintered body, the S 0.01 to 20
Mass% or a total of 0.01 to 20 mass% of S and C,
An easy-to-work high-strength copper-based sintered alloy having a composition consisting of the balance of Cu and unavoidable impurities and a structure in which metal sulfides and / or metal complex carbosulfides are dispersed in a matrix structure.

In the above-mentioned invention of the easy-working high-strength copper-based sintered alloy, as a first preferred embodiment, the metal sulfide is Ti ₃
Preferably, one or more of S, Ti ₂ S, TiS, Zr ₃ S ₂ and Zr S are used. As a second preferred embodiment, the metal complex carbonitride sulfide, Ti ₂ CS and Zr ₂ C S
Is preferably one or two of.

[0012] The present invention, one or two of Ti us and Zr in dissolved Cu added total 0.1 to 30 mass%, further S is 0.01 to 20% by weight or S and C in the copper alloy S source or S source as bets are included if <br/> total 0.01 to 20% by weight equivalent
And a C source are added to produce an easily processed high-strength copper alloy. In the invention of the method for producing an easy-to-work high-strength copper alloy described above, as a first preferred embodiment, after performing a solution treatment on an ingot obtained by performing casting, hot rolling or cold rolling is further performed. It is preferable to perform aging treatment in the range of 250 to 600 ° C.

In a second preferred embodiment, the S source is S,
Preferably, one or more of CuS and Cu ₂ S are used. The present invention, one or two powders of the Ti contact and Zr were mixed 0.1 to 30 wt% of Cu powder, further
0.01-20 mass% of S or S and C in copper-based sintered alloy
S source or so that the total amount is equivalent to 0.01 to 20% by mass.
This is a method for producing an easy-to-work, high-strength copper-based sintered alloy in which an S source and a C source are mixed, and the obtained mixed powder is pressed into a predetermined shape and then sintered.

In the above-mentioned invention of the method for producing an easy-to-work high-strength copper-based sintered alloy, as a first preferred embodiment, a sintered body obtained by sintering is aged at a temperature of 250 to 600 ° C. Processing is preferred. In a second preferred embodiment, the S source is preferably one or more of S, CuS, and Cu ₂ S.

[0015]

DESCRIPTION OF THE PREFERRED EMBODIMENTS First, a copper alloy and a copper-based sintered alloy according to the present invention will be described. The composition of the copper alloy of the present invention is Ti
Contact and one or contain a total of 0.1 to 30 wt% of Zr, total and 0.01 to 20% by weight or S and C a S 0.01
-20% by mass. Further, the structure of the copper alloy of the present invention,
Metal sulfide and / or metal complex carbosulfide is dispersed in the Cu matrix.

[0016] Ti Contact and one or strength If the content is less than the total 0.1% by weight of the Zr, does not appear the effect of improving the characteristics of the conductive or the like, conductive when it exceeds the total of 30 wt% Properties are significantly reduced. Therefore, the content of these metals must satisfy the total range of 0.1 to 30% by mass.
The content of S or the total content of S and C is 0.01% by mass.
If it is less than 10%, sulfide formation is very small, so that the effect of improving characteristics such as strength and conductivity is not exhibited. If it is more than 20% by mass, the conductivity is reduced and the material becomes brittle. Therefore, the content of S or the total content of S and C is 0.01 to 20% by mass.
It is necessary to satisfy the range.

[0017] The composition of the copper-based sintered alloy of the present invention, Ti you and
One or two of Zr are contained in a total of 0.1 to 30% by mass,
S is contained in an amount of 0.01 to 20% by mass or S and C in a total amount of 0.01 to 20% by mass. In the structure of the copper-based sintered alloy of the present invention, a metal sulfide and / or a metal composite carbon sulfide are dispersed in a matrix structure.

[0018] Ti Contact and one or strength If the content is less than the total 0.1% by weight of the Zr, does not appear the effect of improving the characteristics of the conductive or the like, conductive when it exceeds the total of 30 wt% Properties are significantly reduced. Therefore, the content of these metals must satisfy the total range of 0.1 to 30% by mass.
The content of S or the total content of S and C is 0.01% by mass.
If it is less than 10%, sulfide formation is very small, so that the effect of improving characteristics such as strength and conductivity is not exhibited. If it is more than 20% by mass, the conductivity is reduced and the material becomes brittle. Therefore, the content of S or the total content of S and C is 0.01 to 20% by mass.
It is necessary to satisfy the range.

In the present invention, the metal sulfide dispersed in the Cu matrix is Ti ₃ S, Ti ₂ S, TiS, Zr ₃ S ₂ and
It is preferably one or more of Zr S.
To generate these metal sulfides, adding one or two metals of Ti us and Zr to Cu. Ti you and Zr
Is a metal that readily forms sulfides. Therefore, sulfide can be generated in a short time and productivity is improved, which is economically advantageous.

In the present invention, the metal sulfide dispersed in the matrix structure of the Cu-based sintered alloy is Ti ₃ S, Ti ₂ S,
Preferably, one or more of TiS, Zr ₃ S ₂ and Zr S are used. To generate these metal sulfides, adding one or two metals of Ti us and Zr to Cu. Ti contact and Zr is a metal which forms a readily sulfide. Therefore, sulfide can be generated in a short time and productivity is improved, which is economically advantageous.

[0021] In the present invention, the metal complex carbonitride sulfide dispersed in the Cu base is preferably one or two <br/> in the Ti ₂ CS and Zr ₂ C S. To generate these metal complex carbonitride sulfide, the addition of one or two metals of Ti contact and Zr. Ti contact and Zr is a metal which easily forms a complex carbonitride sulfide. As a result, complex carbon sulfide can be produced in a short time, and productivity is improved, which is economically advantageous.

In the present invention, the metal composite carbosulfide dispersed in the matrix structure of the Cu-based sintered alloy is Ti ₂ CS
It is preferable and one or two of Zr ₂ C S. In order to generate these metal complex carbosulfides,
One or two metals of Ti contact and Zr is added to Cu. Ti contact and Zr is a metal which easily forms a complex carbonitride sulfide. As a result, complex carbon sulfide can be produced in a short time, and productivity is improved, which is economically advantageous.

The copper alloy or copper-based sintered alloy of the present invention comprises:
A metal sulfide and / or a metal complex sulfide is dispersed in a Cu matrix or a matrix structure of a Cu-based sintered alloy. By dispersing metal sulfides and / or metal complex sulfides, copper alloys or copper-based joints that achieve both improvement in strength and conductivity at the same time, and have excellent punching, machinability and heat resistance You get money.

Generally, harmful Pb is added in order to improve the punchability and machinability. However, the copper alloy of the present invention is Pb
Since it does not contain, it is also effective in preventing environmental pollution. Next, a method for producing the copper alloy and the copper-based sintered alloy of the present invention will be described. The dissolved Cu, if one or two of Ti contact and Zr added total 0.1 to 30 mass%, further dispersing the metal sulfide in Cu base is in the copper alloy S is 0.01 to 20
If the S source is added so as to be equivalent to the mass% or the metal complex carbosulfide is dispersed in the Cu matrix,
S as S and C are contained equivalent total 0.01 to 20% by weight
A source and a C source are added and casting is performed to obtain an ingot.

[0025] Ti Contact and one or strength If the addition amount is less than the total 0.1% by weight of the Zr, does not appear the effect of improving the characteristics of the conductive or the like, conductive when it exceeds the total of 30 wt% Properties are significantly reduced. Therefore, the added amount of these metals must satisfy the total range of 0.1 to 30% by mass.
The content of S or the total content of S and C is 0.01% by mass.
If it is less than 10%, sulfide formation is very small, so that the effect of improving characteristics such as strength and conductivity is not exhibited. If it is more than 20% by mass, the conductivity is reduced and the material becomes brittle. Therefore, S
The total content of the content or S and C must satisfy the range of 0.01 to 20 wt%.

By casting in this way, a copper alloy in which metal sulfides and / or metal complex carbosulfides are dispersed in a Cu matrix can be produced. In order to further improve the properties, it is preferable that the obtained ingot is subjected to a solution treatment, followed by hot rolling or cold rolling and further aging treatment. Rolling may be either hot rolling or cold rolling.

Further the Cu powder, if one or two powders of the Ti contact and Zr were mixed 0.1 to 30 mass%, further dispersing the metal sulfide to the base tissue of Cu-based sintered alloy is ,copper
S should be included in the base sintered alloy in an amount of 0.01 to 20% by mass.
When mixing the S source or dispersing the metal complex carbosulfide in the matrix structure of the Cu-based sintered alloy , add
S source so that S and C are contained in a total amount of 0.01 to 20% by mass.
And the C source .

[0028] Ti Contact and one or two of strength when the mixing amount is less than the total 0.1% by weight of the powder of the Zr, the effect of improving characteristics of the conductive or the like does not appear, if a total of more than 30 wt% Has a significantly reduced conductivity. Therefore, the mixing amount of these metal powders must satisfy the total range of 0.1 to 30% by mass.

When the content of S or the total content of S and C is less than 0.01% by mass, the formation of sulfide is very small, and the effect of improving properties such as strength and conductivity does not appear. %, The conductivity decreases and the material becomes brittle. Therefore, the content of S or the total content of S and C is
It is necessary to satisfy the range of 0.01 to 20% by mass.

The obtained mixed powder is press-formed into a predetermined shape and then sintered, whereby a copper-based sintered alloy in which metal sulfides and / or metal complex carbosulfides are dispersed can be produced. . In order to further improve the characteristics, it is preferable to subject the obtained sintered body to aging treatment.

In any case, the temperature of the aging treatment is from 250 to
It must be in the range of 600 ° C. Aging temperature is 250
If the temperature is lower than ℃, precipitation hardening does not occur. If the temperature exceeds 600 ° C., age hardening does not occur and softening occurs. When producing a copper alloy or a copper-based sintered alloy by the method of the present invention, the metal or metal powder to be added or mixed is Ti
Is preferably one or two of us and Zr.
Ti contact and Zr is a metal which easily forms a metal sulfides and / or metal complex carbonitride sulfide. Therefore, metal sulfide and / or metal complex carbosulfide can be produced in a short time, and productivity is improved, which is economically advantageous.

In the copper alloy or the copper-based sintered alloy of the present invention, not only pure copper but also an existing copper alloy such as aluminum bronze, phosphor bronze, brass or the like is used as a base composition, and metal sulfide and / or metal composite carbon is used. Similar effects can be obtained by dispersing sulfides. In the present invention, the S source is
Although not limited to a specific material, it is preferable to use one or more of S, CuS, and Cu ₂ S. These materials are economically advantageous because they are relatively inexpensive and readily available.

[0033]

[Example] Ti as a metal forming sulfide in dissolved Cu
Was added, and CuS and Cu ₂ S were further added to dissolve the copper alloys of the five components shown in Table 1, and then cast to produce an ingot having a thickness of 30 mm. The copper alloys A to D are examples of the present invention, and the copper alloy U is a comparative example containing no S.

To the dissolved Cu, Zr was added as a metal forming a sulfide, and CuS and Cu ₂ S were further added to melt the copper alloys of the five components shown in Table 2 and then cast. Thus, an ingot having a thickness of 30 mm was produced. In addition, copper alloy E ~
H is an example of the present invention, and copper alloy V is a comparative example containing no S. Next, Ti or Zr as a metal forming a complex carbosulfide is added to the dissolved Cu, and CuS, Cu ₂ S
And C were added to melt the two types of copper alloys shown in Table 3 and then cast to produce a 30 mm thick ingot.

[0035]

[Table 1]

[0036]

[Table 2]

[0037]

[Table 3]

The obtained ingot was subjected to a solution treatment by heating and holding at 900 ° C. for 20 minutes, and then cooled to room temperature and cold rolled to obtain a 6 mm thick plate. Further, aging treatment was performed at various temperatures. The aging time was 1 hour. The Vickers hardness (Hv) and the electrical conductivity (% IACS) of the plate material thus obtained were measured. The results are shown in Tables 4, 6, and 7. The electrical conductivity (% IACS) is a ratio of the volume resistivity of international standard annealed copper 17.241 × 10 ⁻⁹ μΩ · m divided by the volume resistivity of the material.

The aging time of copper alloy C is 0.5 to
Aging time (hr) and hardness (H
The relationship of v) was investigated. Table 5 shows the results.

[0040]

[Table 4]

[0041]

[Table 5]

[0042]

[Table 6]

[0043]

[Table 7]

The relationship between the aging temperature (° C.) and the Vickers hardness (Hv), the relationship between the aging temperature (° C.) and the electrical conductivity (% IACS), and the aging time (hr) in the measurement results shown in Tables 4 to 7. ) And Vickers hardness (Hv) are shown in FIGS. As shown in FIGS. 1, 4 and 6, copper alloys A to
The Vickers hardness of J was increased by cold rolling compared with the hardness after solution treatment, and further increased by aging treatment. When the aging temperature was 250 ° C. or higher, the Vickers hardness was higher than the hardness after cold rolling. If the aging temperature is 600 ° C or lower, the Vickers hardness is higher than the hardness after solution treatment.

That is, the aging temperature must be in the range of 250 to 600 ° C. However, in order to increase the hardness by aging treatment from the value after cold rolling, it is preferable to perform aging treatment in the range of 300 to 550 ° C, and it is most effective to perform aging treatment in the range of 400 to 500 ° C. Is big. FIG. 2,
As shown in FIGS. 5 and 7, the conductivity of the copper alloys A to J was higher than the conductivity after the solution treatment by aging at an aging temperature of 250 to 600 ° C.

That is, the aging temperature must be in the range of 250 to 600 ° C. However, in order to increase the conductivity by aging treatment to a value higher than the value after cold rolling, it is preferable to perform aging treatment in the range of 300 to 550 ° C, and it is most effective to perform aging treatment in the range of 400 to 500 ° C. Is big. In the copper alloy of the present invention, it is necessary to contain <br/> total 0.1 to 30 wt% of one or two of Ti contact and Zr, in order to significantly improve the strength and conductivity, etc. Is preferably set to a content of 1.0 to 10% by mass as shown in Tables 1 to 3.

Further, in the copper alloy of the present invention, S is set to 0.1.
It is necessary to contain 0.01 to 20% by mass or a total of 0.01 to 20% by mass of S and C. However, in order to remarkably improve the strength and electric conductivity, the content is 0.05% as shown in Tables 1 to 3. ~ 2.0
It is preferable to set it as mass%. As shown in FIG. 3, the Vickers hardness increased as the aging time became longer in the range of 0.5 to 1 hr. When the aging time was 1 hour or longer, the Vickers hardness was almost constant regardless of the aging time. However, when the aging temperature was 350 ° C, the Vickers hardness increased even when the aging time was 100 hours. However, long-term aging treatment is economically disadvantageous, and depending on the aging temperature, if the aging time exceeds 10 hours, the Vickers hardness decreases. Therefore, the aging time is preferably in the range of 0.5 to 10 hours. More preferably, it is within a range of 10 hours.

Next, the heat resistance, punching property,
The machinability and bending workability were investigated. The heat resistance was evaluated at the softening temperature, and the punching properties and bending workability were evaluated based on the occurrence of burrs, occurrence of cracks, and occurrence of wrinkles. Machinability was evaluated by the weight of the chips. Tables 8 to 10 show the evaluation results.
Copper alloys A to J each showed better characteristics than copper alloys U and V containing no S.

[0049]

[Table 8]

[0050]

[Table 9]

[0051]

[Table 10]

The copper alloy C of the present invention (Ti: 2.0 mass%, S: 0.8
FIG. 12 shows an example of a chip shape of (mass%). For comparison, an example of a chip shape of pure copper is also shown. Although long chips are generated with pure copper, short chips are generated with the copper alloy of the present invention.
Therefore, the copper alloy of the present invention has good machinability.
FIG. 13 shows an example of the metal structure of the copper alloy of the present invention. FIG.
As is apparent from the above, extremely fine TiS is generated in the metal structure of the copper alloy of the present invention.

Here, an example in which Ti sulfide is dispersed in a copper alloy (copper alloys A to D), an example in which Zr sulfide is dispersed (copper alloys E to H), and an example in which Ti carbosulfide is dispersed ( The copper alloy I) and the example of dispersing the Zr carbosulfide (copper alloy J) have been described .

Next, a Ti powder as a metal forming a sulfide is mixed with the Cu powder, and CuS and Cu ₂ S powders are further mixed. Aging treatment was performed at various temperatures. The aging time was 1 hour. The components of the obtained copper-based sintered alloy are as shown in Table 11. Also, as a metal that forms sulfide in Cu powder
The Zr powder was mixed, and the CuS and Cu ₂ S powders were further mixed. The resulting mixed powder was compacted, sintered, and aged at various temperatures. The aging time was 1 hour. The components of the obtained copper-based sintered alloy are as shown in Table 12.

[0055]

[Table 11]

[0056]

[Table 12]

The Vickers hardness (Hv) and the electrical conductivity (% IACS) of the copper-based sintered alloys K to Q thus obtained were measured. The results are shown in Tables 13 and 14. The electrical conductivity (% IACS) is 17.241 × volume resistivity of international standard annealed copper.
It is a ratio of 10 ⁻⁹ μΩ · m divided by the volume resistivity of the material.

[0058]

[Table 13]

[0059]

[Table 14]

FIGS. 8 to 11 show the relationship between the aging temperature (° C.) and the Vickers hardness (Hv) and the relationship between the aging temperature (° C.) and the electrical conductivity (% IACS) in the measurement results shown in Tables 13 and 14.
Shown in In the copper-based sintered alloy of the present invention, the aging temperature
Although it is necessary to set the temperature in the range of 250 to 600 ° C., in order to significantly increase the hardness by the aging treatment, it is preferable to perform the aging treatment in the range of 300 to 500 ° C. as shown in FIGS. 8 and 10. Further, aging treatment at a temperature in the range of 400 to 500 ° C is most effective. In order to remarkably improve the conductivity by the aging treatment, as shown in FIGS. 9 and 11, it is preferable to perform the aging treatment in the range of 300 to 500 ° C., and further to perform the aging treatment in the range of 400 to 500 ° C. It is most effective if done.

[0061] In the copper-based sintered alloy of the present invention, it is necessary to contain one or two of Ti contact and Zr total 0.1 to 30% by weight in the sintered body, strength and conductivity, etc. In order to remarkably improve the content, as shown in Tables 11 and 12, the content is preferably set to 4.5 to 28.5% by mass. Further, in the copper-based sintered alloy of the present invention, it is necessary to contain S in an amount of 0.01 to 20% by mass or a total of S and C in an amount of 0.01 to 20% by mass. Table 11
And as shown in Table 12, the content is preferably 3.0 to 15.0% by mass.

Here, an example in which Ti sulfide is dispersed in the matrix structure of the copper-based sintered alloy (copper-based sintered alloys K to M) and Zr
An example has been described for dispersing the sulfide (Domotosho-alloy P to Q), the same effect can be obtained by dispersing the base tissue in the copper-based sintered alloy the double Gosumi sulfide.

[0063]

According to the present invention, the strength and conductivity of the copper alloy are simultaneously improved, and the punching property and the heat resistance are also improved, so that the size and weight of the electronic / electric product can be reduced.

[Brief description of the drawings]

FIG. 1 is a graph showing the relationship between the aging temperature and Vickers hardness of the copper alloy of the present invention.

FIG. 2 is a graph showing the relationship between the aging temperature and the electrical conductivity of the copper alloy of the present invention.

FIG. 3 is a graph showing the relationship between the aging time and Vickers hardness of the copper alloy of the present invention.

FIG. 4 is a graph showing the relationship between the aging temperature and Vickers hardness of the copper alloy of the present invention.

FIG. 5 is a graph showing the relationship between the aging temperature and the electrical conductivity of the copper alloy of the present invention.

FIG. 6 is a graph showing the relationship between the aging temperature and Vickers hardness of the copper alloy of the present invention.

FIG. 7 is a graph showing the relationship between the aging temperature and the electrical conductivity of the copper alloy of the present invention.

FIG. 8 is a graph showing the relationship between the aging temperature and Vickers hardness of the copper-based sintered alloy of the present invention.

FIG. 9 is a graph showing the relationship between the aging temperature and the electrical conductivity of the copper-based sintered alloy of the present invention.

FIG. 10 is a graph showing the relationship between the aging temperature and Vickers hardness of the copper-based sintered alloy of the present invention.

FIG. 11 is a graph showing the relationship between the aging temperature and the electrical conductivity of the copper-based sintered alloy of the present invention.

FIG. 12 is a photograph showing an example of a chip shape.

FIG. 13 is an electron micrograph showing an example of a metal structure of the copper alloy of the present invention.

────────────────────────────────────────────────── ⁷ Continued on the front page (51) Int.Cl. ⁷ Identification code FI C22F 1/00 C22F 1/00 630J 630K 661 661A 682 682 683 683 683 685 685Z 687 687 691 691B (72) Inventor Katsunari Oikawa Shibata Miyagi Pref. 4-1-34 Nishifunako, Shibata-cho, Gunma (72) Inventor Hiroshi Mitsui 18-10 Kadono, Mochina, Taishiro-ku, Sendai-shi, Miyagi (72) Inventor Ryosuke Kainuma 172-15, Kurane-jirin, Natori, Miyagi, Japan (72) Inventor Ikuo Onuma 146, Murata-cho, Murata-cho, Shibata-gun, Miyagi (56) References JP-A-63-149344 (JP, A) JP-A-7-258776 (JP, A) JP-A 8-41612 (JP) , A) JP-A-10-265873 (JP, A) JP-A-8-503022 (JP, A) (58) Fields investigated (Int. Cl. ⁷ , DB name) C22C 9/00-9/10

Claims (12)

(57) [Claims] Total one or two of 1. A Ti Contact and Zr
0.1 to 30% by mass, 0.01 to 20% by mass of S or 0.01 to 20% by mass of S and C in total, the balance being Cu and unavoidable impurities, and metal sulfide and / or metal in the Cu base An easily machined high-strength copper alloy having a structure in which a complex carbosulfide is dispersed. 2. The method according to claim 1, wherein the metal sulfide is Ti ₃ S, Ti ₂ S, Ti
S, Zr ₃ easy machining high strength copper alloy according to claim 1, characterized in that S ₂ and one or more of Zr S. 3. The method according to claim ₂ , wherein the metal complex carbosulfide is Ti ₂ CS and
Easy machining high strength copper alloy according to claim 1 or 2, characterized in that one or two of fine Zr ₂ C S. 4. A total of 0.1 to 30 wt% of one or two of the sintered body Ti Contact and Zr, a total 0.01 to 20% by weight containing a 0.01 to 20% by weight or S and C a S And an easy-to-work high-strength copper-based sintered alloy characterized by having a composition comprising the balance of Cu and unavoidable impurities, and a structure in which a metal sulfide and / or a metal complex carbosulfide is dispersed in a matrix structure. . 5. The method according to claim 1, wherein the metal sulfide is Ti ₃ S, Ti ₂ S, Ti
S, easy machining high strength copper base sintered alloy according to claim 4, characterized in that Zr ₃ S ₂ and one or more of Zr S. 6. The method according to claim 6, wherein the metal complex carbosulfide is Ti ₂ CS and
Easy machining high strength copper base sintered alloy according to claim 4 or 5, characterized in that one or two of fine Zr ₂ C S. 7. One or two of Ti us and Zr in dissolved Cu added total 0.1 to 30 wt%, even more in the copper alloy
S is then added <br/> pressurizing the S source or S source and the C source as the 0.01 to 20% by weight or S and C are contained equivalent total 0.01 to 20% by weight, and characterized by performing the casting Method for producing high-strength copper alloy that is easy to process. 8. After performing a solution treatment on the ingot obtained by performing the casting, hot rolling or cold rolling is performed,
8. The method for producing an easily workable high-strength copper alloy according to claim 7, further comprising aging at a temperature in the range of 250 to 600 [deg.] C. 9. The S source according to claim 7, wherein said S source is one or more of S, CuS and Cu ₂ S.
Or the method for producing an easily processable high-strength copper alloy according to 8. 10. One or two powders of the Ti contact and Zr were mixed 0.1 to 30 wt% of Cu powder, further Domotosho bond
0.01-20% by mass of S or 0.01% by mass of S and C in gold
S source or S source and C source so as to be contained up to 20% by mass
And press-molding the resulting mixed powder into a predetermined shape, followed by sintering. 11. The easy-working high-strength copper-based sintered alloy according to claim 10, wherein the sintered body obtained by performing the sintering is subjected to an aging treatment in a range of 250 to 600 ° C. Production method. 12. The method according to claim 1, wherein the S source is one or more of S, CuS and Cu ₂ S.
12. The method for producing an easily processed high-strength copper-based sintered alloy according to 10 or 11.