HIGH-STRENGTH COPPER ALLOY

Info

Publication number: 20120027638
Type: Application
Filed: Apr 16, 2010
Publication Date: Feb 2, 2012
Applicant: San-Etsu Metals Co., Ltd. (Toyama)
Inventors: Yoshiharu Kosaka (Toyama), Akimichi Kojima (Toyama), Katsuyoshi Kondoh (Osaka)
Application Number: 13/258,467

Abstract

A high-strength copper alloy contains 20 to 45% of zinc, 0.3 to 1.5% of iron, 0.3 to 1.5% of chromium, and a balance of copper, based on mass.

Description

Description

TECHNICAL FIELD

The present invention relates to high-strength copper alloys having excellent mechanical characteristics, and more particularly to high-strength copper alloys produced by a casting method. More preferably, the present invention is intended to provide high-strength copper alloys having strength characteristics improved by performing hot plastic working on cast copper alloys.

BACKGROUND ART

Copper alloys are widely used in automotive parts, parts of home electric appliances, electric, electronic, or optical parts, piping members (faucet fittings, valves), etc. In view of the recent measures against global warming, there has been a strong demand for reduction in size, weight, and thickness of products and members has been greatly desired, and the copper alloys having higher specific gravity than iron need to be increased in strength in order to meet such a demand.

Of the copper alloys, brass alloys containing zinc are often used in such parts as described above, due to their corrosion resistance. Japanese Unexamined Patent Publication No. 2000-119775 (Patent Literature 1) has been proposed as related art for increasing the strength of the brass alloys. Patent Literature 1 discloses that a brass alloy having tensile strength characteristics as high as about 600 to 800 MPa is obtained by hot extrusion of a cast copper alloy. Silicon (Si) as an added element has an advantage in that it forms γ-phase forming a matrix, and thus improves a cutting property of a copper alloy. However, since Si is hard, adding Si causes problems such as higher cutting resistance and a shorter tool life as compared to brass alloys as described in JIS H 3250-C3604, C3771, etc.

Other literatures disclosing high-strength copper alloys include Japanese Patent No. 3,917,304 (free-cutting copper alloy, Patent Literature 2) and Japanese Patent No. 3,734,372 (lead-free free-cutting copper alloy, Patent Literature 3). In the techniques disclosed in these patent literatures, it is proposed that a small amount of zirconium and phosphorus be added to obtain granular crystal rather than dendrite crystal formed by a normal casting method, and the granular crystal be refined to 10 μm, thereby implementing high strength and high ductility. However, in the brass alloys disclosed in these patent literatures, a matrix is significantly harder than conventional brass alloys, thereby causing problems such as a degraded cutting property and a shorter tool life.

Meanwhile, in Japanese Patent No. 4,190,570 (lead-free free-cutting copper alloy extruded material, Patent Literature 4), the inventors succeeded in improving the cutting property of a brass powder alloy extruded material and also obtaining high tensile strength thereof by producing brass alloy powder and adding graphite particles to the brass alloy powder instead of lead by using a powder metallurgy process. In a manufacturing method of a copper alloy disclosed in Patent Literature 4, copper alloy powder having fine crystal grains is produced by using a rapid solidification method, and this powder is formed and solidified by hot extrusion, whereby a copper alloy base material having a fine structure can be obtained. Thus, a copper alloy extruded material having high strength and high ductility is obtained. However, as compared to a typical manufacturing process of a brass alloy, the copper alloy powder need be first formed and solidified in order to prepare a billet body for extrusion. It is therefore difficult to apply this manufacturing method to a conventional process of extruding a cast billet, and a press forming machine, a compacting apparatus, etc. is required to solidify the copper alloy powder.

CITATION LIST Patent Literature

PTL1: Japanese Unexamined Patent Publication No. 2000-119775

PTL2: Japanese Patent No. 3,917,304

PTL3: Japanese Patent No. 3,734,372

PTL4: Japanese Patent No. 4,190,570

SUMMARY OF INVENTION Technical Problem

It is an object of the present invention to manufacture a copper alloy having high strength characteristics by a casting process. In order to achieve this object, the present invention proposes a copper-zinc alloy containing a proper amount of iron and chromium. Thus, the high-strength copper alloy according to the present invention is widely applicable to automotive parts, parts of home electric appliances, electric, electronic, or optical parts, piping members, etc.

Solution to Problem

A high-strength copper alloy according to the present invention contains 20 to 45% of zinc, 0.3 to 1.5% of iron, 0.3 to 1.5% of chromium, and a balance of copper, based on mass.

Preferably, in the high-strength copper alloy, a content ratio (Fe/Cr) of the iron to the chromium is 0.5 to 2 based on mass.

In one embodiment, the high-strength copper alloy further contains at least one kind of element selected from the group consisting of 0.05 to 4% of lead, 0.02 to 3.5% of bismuth, 0.02 to 0.4% of tellurium, 0.02 to 0.4% of selenium, and 0.02 to 0.15% of antimony, based on mass. The high-strength copper alloy may further contain 0.2 to 3% of tin, based on mass. The high-strength copper alloy may further contain 0.2 to 3.5% of aluminum and 0.3 to 3.5% of calcium, based on mass. The high-strength copper alloy may further contain at least one kind of element selected from a lanthanoid group consisting of lanthanum, cerium, neodymium, gadolinium, dysprosium, ytterbium, and samarium, and a total content of the at least one kind of element may be 0.5 to 5%, based on mass. The high-strength copper alloy may further contain at least one kind of element selected from the group consisting of 0.5 to 3% of manganese, 0.2 to 1% of silicon, 1.5 to 4% of nickel, 0.1 to 1.2% of titanium, 0.1 to 1.5% of cobalt, and 0.5 to 2.5% of zirconium, based on mass.

Preferably, the high-strength copper alloy includes iron-chromium compound particles at grain boundaries. The iron-chromium compound particles are particles precipitated at the grain boundaries during solidification in a casting method, and preferably have a particle size of 10 to 50 μm.

Preferably, the copper alloy is a copper alloy subjected to hot plastic working after being produced by a casting method. The hot plastic working is, e.g., a working method selected from the group consisting of extrusion, forging, rolling, drawing, and pulling.

The configurations, functions, advantageous effects, etc. of the present invention described above will be described below in “Description of Embodiments.”

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a stress-strain diagram in a tension test.

FIG. 2 shows images showing a result of structure observation by an optical microscope.

FIG. 3 shows an image showing a result of SEM-EDS analysis of a brass alloy extruded material.

FIG. 4 is a diagram illustrating a hole drilling test method.

DESCRIPTION OF EMBODIMENTS

[Addition of Iron and Chromium]

In a copper alloy of the present invention, iron and chromium are essential elements to be added. The iron content is 0.3 to 1.5%, and the chromium content is 0.3 to 1.5%, based on mass. Since chromium has low solid solubility in copper, a copper-chromium mother alloy is prepared, and is added to molten pure copper melted in a crucible, thereby adjusting the chromium content. Next, a predetermined weight of iron is added. Then, other element or elements are added as required, and lastly, zinc is added. The mixture is stirred and poured into a casting mold. Zinc tends to evaporate as compared to other elements due to its high vapor pressure. Thus, zinc is lastly added to the molten copper alloy.

The molten copper alloy is cooled and solidified in the casting mold. During the cooling and solidification, chromium slightly solid-solved in copper is crystallized at copper grain boundaries, and then iron is crystallized near the crystallized chromium. Thus, chromium-iron compound particles having a size (particle size) of about 10 to 50 μm are present at the grain boundaries, and strength of the brass alloy is increased due to dispersion strengthening by the compound particles at the grain boundaries.

In Japanese Patent No. 4,190,570 (lead-free free-cutting copper alloy extruded material) as well, the inventors describe the effect of improving strength of the brass alloy by adding iron and chromium. However, the invention described in this patent is based on a powder metallurgy process by a rapid solidification method as a basic manufacturing method, chromium and iron, supersaturatedly solid-solved in copper alloy powder, are precipitated during an extrusion process, and are precipitated at grain boundaries or inside crystal grains as an iron-chromium compound as small as several hundreds of nanometers to several microns. Such submicron fine iron-chromium compound particles that are precipitated based on the powder metallurgy process are completely different in a grain size and a production mechanism from the iron-chromium particles (compound particles) crystallized at the grain boundaries during solidification by a casting method as proposed in the present invention.

Regarding the iron content and the chromium content that are suitable for strengthening the brass alloy, it is desirable that the brass alloy contain 0.3 to 1.5% of iron and 0.3 to 1.5% of chromium, based on mass. The effect of improving the strength of the brass alloy as described above is not sufficient if the iron content and the chromium content are less than 0.3%. On the other hand, ductility of the brass alloy is reduced if the iron content and the chromium content are more than 1.5%. Corrosion resistance of the brass alloy is reduced if the iron content is more than 2%.

It is desirable that the content ratio (Fe/Cr) of iron to chromium be 0.5 to 2, based on mass. The proportion of the chromium-iron compound at the grain boundaries described above increases in the case where the content ratio of iron to chromium is in this range. In other words, if the content ratio of iron to chromium is less than 0.5 or more than 2, iron or chromium is independently crystallized at the grain boundaries, whereby the effect of improving the strength is reduced.

[Addition of Element for Improving Cutting Property]

In order to improve the cutting property of the brass alloy, it is desirable that the brass alloy contains at least one kind of element selected from the group consisting of 0.05 to 4% of lead, 0.02 to 3.5% of bismuth, 0.02 to 0.4% of tellurium, 0.02 to 0.4% of selenium, and 0.02 to 0.15% of antimony, based on mass. If the content of each element is less than the lower limit of the above range, a sufficient cutting property cannot be obtained, and a brass alloy base material has a rough surface after a cutting process, and the tool life is reduced. On the other hand, if the content of each element is more than the upper limit of the above range, mechanical characteristics such as strength and ductility are degraded because the element serves as an origin of fracture. Note that in view of the recent environmental problems, since the use of lead is restricted, it is more preferable to select bismuth as an element for improving the cutting property.

[Various Added Elements]

Tin is effective not only in forming γ-phase in the matrix, but also in increasing the strength of the alloy by forming a compound with copper. A preferred tin content is 0.2 to 3% based on mass. The effect described above is not sufficient if the tin content is less than 0.2%. On the other hand, adding more than 3% of tin reduces the ductility of the brass alloy. Adding more than 2% (the content) of tin improves dezincing resistance of β-phase.

Aluminum forms an intermetallic compound with copper, and its spherical particles are dispersed in the matrix, thereby improving mechanical characteristics such as strength and hardness, and high-temperature oxidation resistance of the copper alloy. A preferred aluminum content is 0.2 to 3.5% based on mass. The above effect of aluminum is not sufficient if the aluminum content is less than 0.2%. On the other hand, adding more than 3.5% of aluminum coarsens the compound with copper, resulting in reduced ductility of the brass alloy. Moreover, since aluminum, together with calcium described below, forms an intermetallic compound Al₂Ca, thereby contributing to improvement in strength and hardness.

Calcium, contained together with aluminum in the copper alloy, forms the intermetallic compound Al₂Ca, thereby contributing to improvement in strength and hardness. A preferred calcium content is 0.3 to 3.5% based on mass. The above effect is not sufficient if the calcium content is less than 0.3%. On the other hand, adding more than 3.5% of calcium coarsens the intermetallic compound Al₂Ca, resulting in reduced ductility of the brass alloy.

A lanthanoid group (lanthanum, cerium, neodymium, gadolinium, dysprosium, ytterbium, and samarium) is effective as each element of the lanthanoid group is precipitated at grain boundaries as a compound with copper or is independently crystallized at the grain boundaries, and thus strengthens the matrix. It is desirable that the total content of the lanthanoid element group be 0.5 to 5% based on mass. The effect of the lanthanoid element group is not sufficient if the total content thereof is less than 0.5%. Adding more than 5% of the lanthanoid element group reduces the ductility, and also excessively hardens the copper alloy, thereby reducing extrusion workability.

The strength and hardness of the copper alloy can be improved by adding at least one kind of element selected from the group consisting of 0.5 to 3% of manganese, 0.2 to 1% of silicon, 1.5 to 4% of nickel, 0.1 to 1.2% of titanium, 0.1 to 1.5% of cobalt, and 0.5 to 2.5% of zirconium as a transition metal element group, based on mass. The above effect of improving the characteristics is not sufficient if the content of each element is less than the lower limit of the above range. On the other hand, the ductility of the copper alloy is reduced if the content of each element exceeds the upper limit of the above range.

[Manufacturing Method]

A molten copper alloy having the above composition is produced, and an ingot material is produced by a method in which the molten copper alloy is poured into a casting mold, or a continuous casting method. Moreover, hot plastic working, such as an extrusion, forging, rolling, drawing, or pulling, is performed on the ingot material as necessary. At this time, the heating temperature that allows the ingot to be sufficiently plastic-deformed is in the range of 600 to 850° C. In particular, the heating temperature is desirably 750° C. or less in order to suppress evaporation of zinc during heating.

EXAMPLES (1) Example 1

Cast copper alloy ingots containing elements shown in Tables 1 and 2 were prepared. Each ingot was subjected to a hot extrusion process immediately after heating and keeping the ingot at 700° C. The extrusion process was performed at an extrusion ratio of 37. Tensile test pieces were obtained from each copper alloy extruded material, and a tensile test was conducted at room temperature at a strain rate of 5×10⁻⁴/s. The result is shown in Tables 1 and 2. Sample Nos. 1 to 16 are examples of the present invention, and Sample Nos. 17 to 19 are comparative examples.

[Table 1]

[Table 2]

Since Sample Nos. 1 to 5 as examples of the present invention contain a predetermined amount of iron and chromium, tensile strength (TS) of the extruded material is higher than Sample No. 19 as a comparative example by about 130 to 210 MPa. This is because iron-chromium compound particles made of iron and chromium are dispersed at grain boundaries, and thus the strength of the copper alloy is significantly increased. It is also recognized that the tensile strength is increased as the amount of iron and chromium is increased.

Sample Nos. 6 to 8 as examples of the present invention are copper alloys containing bismuth (Bi), and Sample Nos. 9 to 11 as examples of the present invention are copper alloys containing lead (Pb). Bismuth and lead are the elements that are added to improve the cutting property of the copper alloy. The tensile strength of the copper alloys of Sample Nos. 9 to 11 is slightly lower than Sample No. 2 as an example of the present invention containing neither bismuth nor lead, but is higher than Sample No. 17 or 18 as a comparative example by about 160 to 190 MPa. Thus, adding bismuth or lead to the brass alloy containing iron and chromium can improve the cutting property while maintaining high tensile strength.

In Sample Nos. 12 and 13 as examples of the present invention, it can be verified that the strength is increased by adding tin (Sn).

Sample Nos. 14 to 16 as examples of the present invention contain aluminum (Al) and calcium (Ca). Thus, the tensile strength is significantly increased by dispersion of an intermetallic compound Al₂Ca in the matrix of the copper alloy.

(2) Example 2

As in Example 1, cast copper alloy ingots containing elements shown in Tables 3 and 4 were prepared. Each ingot was subjected to a hot extrusion process immediately after heating and keeping the ingot at 700° C. The extrusion process was performed at an extrusion ratio of 37. Tensile test pieces were obtained from each copper alloy extruded material, and a tensile test was conducted at room temperature at a strain rate of 5×10⁻⁴/s. The result is shown in Tables 3 and 4. Sample Nos. 20 to 24 and 28 to 33 are examples of the present invention, and Sample Nos. 25 to 27, 34, and 35 are comparative examples.

[Table 3]

[Table 4]

Each of Sample Nos. 21, 22, 23, and 24 as examples of the present invention contains a lanthanoid element. Thus, the tensile strength of these samples reaches 640 to 680 MPa, which is higher than Sample No. 20 as an example of the present invention containing no lanthanoid element.

Each of Sample Nos. 29 and 30 as examples of the present invention is also a brass alloy containing a lanthanoid element. It can be verified that the tensile strength of these samples is significantly higher than Sample No. 28 as an example of the present invention containing no lanthanoid element.

Sample No. 31 as an example of the present invention is a brass alloy containing a proper amount of silicon (Si), Sample No. 32 as an example of the present invention is a brass alloy containing a proper amount of nickel (Ni), and Sample No. 33 as an example of the present invention is a brass alloy containing a proper amount of titanium (Ti). It can be verified that the tensile strength of these samples is higher than Sample No. 28 as an example of the present invention containing none of these elements.

Although Sample Nos. 25 to 27, 34, and 35 as comparative examples contain iron and chromium, the content ratio of iron to chromium is not in the range of 0.5 to 2, based on mass. Thus, it is recognized that the tensile strength of these samples is higher than Sample No. 19 as a comparative example containing neither iron nor chromium. However, the tensile strength of these elements is lower than the brass alloys as examples of the present invention whose content ratio of iron to chromium is in the range of 0.5 to 2 (Sample Nos. 1 to 5 as examples of the present invention in Table 1, Sample No. 20 as an example of the present invention in Table 3, and Sample No. 28 as an example of the present invention in Table 4).

(3) Example 3

Tensile test pieces were obtained from the brass alloy extruded materials of Sample Nos. 3 and 5 as examples of the present invention and the brass extruded material of Sample No. 19 as a comparative example, and a tensile test was conducted. FIG. 1 shows a stress-strain diagram in this tensile test. It can be seen from the figure that Sample Nos. 3 and 5 as examples of the present invention have higher tensile strength and higher endurance strength (yield strength) than Sample No. 19 as a comparative example.

(4) Example 4

FIG. 2 shows the result of structure observation of Sample No. 3 as an example of the present invention by an optical microscope. It can be seen from the figure that Fe—Cr compound particles having a particle size of about 20 to 50 μm are uniformly dispersed in the brass alloy matrix.

(5) Example 5

FIG. 3 shows the result of scanning electron microscopy-energy dispersive spectroscopy (SEM-EDS) analysis of the brass alloy extruded material of Sample No. 12 as an example of the present invention described in Example 1. It can be seen from the figure that main components of the compound that is dispersed are iron (Fe) and chromium (Cr).

(6) Example 6

Cast copper alloy ingots containing elements shown in Tables 5 and 6 are prepared. Tensile test pieces were obtained from each copper alloy ingot, and a tensile test was conducted at room temperature at a strain rate of 5×10⁻⁴/s. The result is shown in Tables 5 and 6. Sample Nos. 1 to 16 are examples of the present invention, and Sample Nos. 17 to 19 are comparative examples. It can be seen that the strength of the examples of the present invention is higher than the comparative examples even in the cast ingot materials before the protrusion process, because the examples of the present invention contains a proper amount of predetermined elements.

[Table 5]

[Table 6]

(7) Example 7

The cutting property of the brass alloy extruded materials of Sample Nos. 5 to 11 as examples of the present invention and Sample Nos. 17 to 19 as comparative examples described in Examples 1 and 2 were evaluated by conducting a drilling test. Note that as a test method, the time it takes to drill a hole having a depth of 5 mm in each copper alloy extruded material with constant load (in this example, with a weight of 1 kg) applied to a drill as shown in FIG. 4 was compared. Shorter processing time means a more satisfactory cutting property. Note that the drilling test was conducted for 10 samples per extruded material by rotating a high-speed steel drill having a diameter of 4.8 mmφ at a rotational speed of 1,000 rpm under dry conditions (with no cutting oil), and a mean value was obtained from the measurement values. The result is shown in Table 7.

[Table 7]

As shown in Table 7, in Sample No. 5 as an example of the present invention containing none of the elements that improve the cutting property such as bismuth and lead, a hole having a depth of 5 mm was not able to be formed under the above conditions even if the drilling was performed for three minutes. Sample Nos. 6 to 8 as examples of the present invention are brass alloys containing bismuth. In Sample Nos. 6 to 8, a hole was able to be formed, and the processing time decreases as the amount of bismuth is increased. Sample Nos. 9 to 11 as examples of the present invention are alloys containing lead, and the cutting time decreases as the lead content is increased. Thus, it was verified that adding bismuth or lead can significantly improve the cutting property while maintaining high tensile strength.

(8) Example 8

Cast copper alloy ingots containing elements shown in Table 8 were prepared. Each ingot was subjected to a hot extrusion process immediately after heating and keeping the ingot at 650° C. The extrusion process was performed at an extrusion ratio of 37. Tensile test pieces were obtained from each copper alloy extruded material, and a tensile test was conducted at room temperature at a strain rate of 5×10⁻⁴/s. Regarding evaluation of the cutting property, mean processing time was calculated by a method similar to that of Example 7 described above. The result is shown in Table 8. All of Sample Nos. 40 to 56 are examples of the present invention.

[Table 8]

As can be seen from Table 8, copper alloys having high tensile strength, high elongation (ductility), and a high cutting property can be obtained by adding to brass a proper amount of element that improves the strength and a proper amount of element that improves the cutting property.

(9) Example 9

Molten copper alloys containing elements shown in Table 9 were prepared, and powders having a powder particle size of 150 μm or less (a mean particle size of 112 to 138 μm) were produced by a water atomizing method. Each powder was heated and pressed (with a pressure of 40 MPa) in a vacuum atmosphere at 750° C. by a discharge plasma sintering apparatus to produce a dense sintered compact. Each sintered compact was subjected to a hot extrusion process immediately after heating and keeping (for 15 minutes) the sintered compact at 650° C. in a nitrogen gas atmosphere. The extrusion process was performed at an extrusion ratio of 37. Tensile test pieces were obtained from each copper alloy extruded material, and a tensile test was conducted at room temperature at a strain rate of 5×10⁻⁴/s. Regarding evaluation of the cutting property, mean processing time was calculated by a method similar to that of Example 7 described above. The result is shown in Table 9. All of Sample Nos. 60 to 69 are examples of the present invention.

[Table 9]

As can be seen from Table 9, copper alloys having high tensile strength, high elongation (ductility), and a high cutting property can be obtained by adding to brass a proper amount of element that improves the strength and a proper amount of element that improves the cutting property. In particular, in the case of using powder produced by the water atomizing method, a grain refining effect is additionally provided, and thus the tensile strength of the extruded material is further increased as compared to the case of producing the extrusion ingot by the casting method.

INDUSTRIAL APPLICABILITY

The present invention can be advantageously used as a high-strength copper alloy having excellent mechanical characteristics.

TABLE 1 Sample No. 1 2 3 4 5 6 7 8 9 10 11 Zn 39.8 40.2 40.4 39.9 40.0 40.1 39.8 40.0 39.8 40.1 39.9 Fe 0.42 0.63 0.98 1.23 1.41 0.68 0.73 0.70 1.05 1.09 1.06 Cr 0.38 0.58 1.02 1.17 1.38 0.73 0.90 0.97 0.98 1.12 1.19 Sn 0.02 — 0.03 — 0.02 0.04 — — 0.01 — 0.02 Bi — — — — — 0.57 1.26 2.28 — — — Pb 0.03 0.02 0.01 0.02 0.03 0.02 0.01 0.02 0.45 0.92 2.08 Al — — — — — — — — — — — Ca — — — — — — — — — — — Cu Balance Balance Balance Balance Balance Balance Balance Balance Balance Balance Balance Fe/Cr Ratio 1.11 1.09 0.96 1.05 1.02 0.93 0.81 0.72 1.07 0.97 0.89 TS 587 609 624 647 665 598 589 580 609 600 587 ε 30.2 29.1 27.9 26.4 25.2 31.2 29.3 27.8 28.7 27.4 26.1 TS; Tensile Strength (MPa), ε; Breaking Elongation (%)

TABLE 2 Sample No. 12 13 14 15 16 17 18 19 Zn 40.2 40.7 39.7 39.4 39.2 40.1 39.8 40.4 Fe 0.72 0.69 0.82 0.99 0.87 0.02 0.03 0.01 Cr 0.97 0.87 0.98 1.19 1.03 — — — Sn 0.98 2.13 — — — — — — Bi — — — — — 2.27 — — Pb 0.01 0.02 0.02 0.03 0.02 0.02 2.78 0.02 Al — — 0.43 0.64 0.88 — — — Ca — — 0.37 0.55 0.69 — — — Cu Balance Balance Balance Balance Balance Balance Balance Balance Fe/Cr Ratio 0.74 0.79 0.84 0.83 0.84 — — — TS 644 662 644 658 668 402 411 453 ε 26.3 25.1 26.2 25.3 24.4 39.8 38.7 48.9 TS; Tensile Strength (MPa), ε; Breaking Elongation (%)

TABLE 3 Sample No. 20 21 22 23 24 25 26 27 Zn 40.1 40.4 39.8 39.3 40.2 40.2 40.0 40.3 Fe 0.97 0.89 0.88 0.93 0.90 0.84 0.86 0.92 Cr 0.89 0.83 0.88 0.86 0.83 0.23 0.31 0.33 Sn 0.01 0.02 0.03 0.02 0.03 0.03 0.01 0.02 Pb 0.03 0.02 0.01 0.02 0.03 0.02 0.01 0.02 La — 1.09 2.54 — — — — — Ce — — — 0.78 — — — — Nd — — — — 0.65 — — — Gd — — — — — — — — Yb — — — — — — — — Si — — — — — — — — Ni — — — — — — — — Ti — — — — — — — — Cu Balance Balance Balance Balance Balance Balance Balance Balance Fe/Cr Ratio 1.09 1.07 1.00 1.08 1.08 3.65 2.77 2.79 TS 618 641 683 662 652 554 563 567 ε 28.2 25.7 21.2 23.3 24.8 33.6 32.1 32.6

TABLE 4 Sample No. 28 29 30 31 32 33 34 35 Zn 39.4 40.3 39.6 40.1 40.4 39.5 39.3 40.4 Fe 0.62 0.58 0.59 0.62 0.60 0.64 0.57 0.60 Cr 0.60 0.59 0.62 0.61 0.62 0.65 0.21 0.17 Sn 0.01 — 0.02 0.02 0.03 — 0.02 — Pb 0.45 0.92 2.08 0.01 0.02 0.02 0.03 0.02 La — — — — — — — — Ce — — — — — — — — Nd — — — — — — — — Gd — 1.65 — — — — — — Yb — — 1.32 — — — — — Si — — — 0.38 — — — — Ni — — — — 1.87 — — — Ti — — — — — 0.44 — — Cu Balance Balance Balance Balance Balance Balance Balance Balance Fe/Cr Ratio 1.03 0.98 0.95 1.02 0.97 0.98 2.71 3.53 TS 601 653 646 634 639 633 549 555 ε 29.6 25.3 26.1 26.2 27.4 28.1 34.4 34.1

TABLE 5 Sample No. 1 2 3 4 5 6 7 8 9 10 11 Zn 39.8 40.2 40.4 39.9 40.0 40.1 39.8 40.0 39.8 40.1 39.9 Fe 0.42 0.63 0.98 1.23 1.41 0.68 0.73 0.70 1.05 1.09 1.06 Cr 0.38 0.58 1.02 1.17 1.38 0.73 0.90 0.97 0.98 1.12 1.19 Sn 0.02 — 0.03 — 0.02 0.04 — — 0.01 — 0.02 Bi — — — — — 0.57 1.26 2.28 — — — Pb 0.03 0.02 0.01 0.02 0.03 0.02 0.01 0.02 0.45 0.92 2.08 Al — — — — — — — — — — — Ca — — — — — — — — — — — Cu Balance Balance Balance Balance Balance Balance Balance Balance Balance Balance Balance Fe/Cr Ratio 1.11 1.09 0.96 1.05 1.02 0.93 0.81 0.72 1.07 0.97 0.89 TS 442 449 464 477 482 437 441 422 449 452 426 ε 36.2 32.3 29.7 28.9 28.1 33.7 32.1 29.8 30.3 30.1 29.4 TS; Tensile Strength (MPa), ε; Breaking Elongation (%)

TABLE 6 Sample No. 12 13 14 15 16 17 18 19 Zn 40.2 40.7 39.7 39.4 39.2 40.1 39.8 40.4 Fe 0.72 0.69 0.82 0.99 0.87 0.02 0.03 0.01 Cr 0.97 0.87 0.98 1.19 1.03 — — — Sn 0.98 2.13 — — — — — — Bi — — — — — 2.27 — — Pb 0.01 0.02 0.02 0.03 0.02 0.02 2.78 0.02 Al — — 0.43 0.64 0.88 — — — Ca — — 0.37 0.55 0.69 — — — Cu Balance Balance Balance Balance Balance Balance Balance Balance Fe/Cr Ratio 0.74 0.79 0.84 0.83 0.84 — — — TS 473 481 467 482 485 301 308 332 ε 28.9 27.9 28.5 27.5 26.2 42.5 44.2 51.4 TS; Tensile Strength (MPa), ε; Breaking Elongation (%)

TABLE 7 Sample No. 5 6 7 8 9 10 11 17 18 19 Mean Cutting Time Unable to Cut 36.85 29.94 24.24 36.61 28.62 21.79 22.6 18.83 45.26 n = 1 >180 38.7 31.1 24.4 33.2 29.2 21.2 22.4 19.2 38.2 n = 2 >180 34.5 29.8 24.6 36.4 28.4 22.3 23.1 18.7 39.2 n = 3 >180 36.6 30.2 24.3 38.3 28.1 21.8 23.7 18.3 40.2 n = 4 >180 35.7 30.8 23.3 37.2 29.6 21.7 22.2 18.9 41.0 n = 5 >180 37.2 28.8 24.1 34.3 28.4 21.5 22.6 19.0 42.0 n = 6 >180 36.8 29.7 24.7 37.9 29.4 21.9 22.8 19.1 43.4 n = 7 >180 36.6 29.2 25.1 38.2 28.3 22.1 22.3 18.7 46.6 n = 8 >180 37.5 28.6 23.8 36.8 27.9 22.3 21.8 18.6 48.4 n = 9 >180 37.7 30.4 23.9 37.6 28.8 21.7 22.5 19.1 54.4 n = 10 >180 37.2 30.8 24.2 36.2 28.1 21.4 22.6 18.7 59.2 Drilling Load: 1 kgf, Drill Diameter; 5 mm φ, Hole Depth; 5 mm

TABLE 8 Tensile Endurance Mean Sample Added Element (wt %) Strength Stress Breaking Cutting No. Zn Fe Cr Sn Ti Bi Pb Fe/Cr MPa MPa Elongation % Time s 40 40.57 0.54 0.70 0.65 2.37 0.77 610.2 311.6 31.3 33.21 41 40.81 0.23 0.26 0.60 0.99 0.89 596.7 290.7 29.4 36.12 42 40.64 0.23 0.26 0.60 2.02 0.88 595.8 293.4 27.4 14.77 43 40.83 0.22 0.22 0.58 2.85 1.00 622.4 284.1 22.2 18.10 44 40.30 0.61 0.88 0.66 1.90 0.69 606.2 298.2 28.1 28.06 45 39.22 0.47 0.45 0.62 1.89 1.04 523.1 302.3 32.2 27.45 46 39.26 0.40 0.58 0.62 2.12 0.69 506.5 282.9 29.4 31.50 47 37.30 0.68 0.83 0.79 2.55 0.82 547.2 339.9 16.4 29.18 48 37.30 0.68 0.83 0.79 2.98 0.82 600.1 348.9 28.8 43.04 49 39.65 0.65 0.98 0.63 1.51 0.66 629.7 294.8 29.3 25.13 50 40.50 0.63 0.98 0.65 2.19 0.64 624.4 334.8 31.8 33.08 51 40.31 0.51 0.73 0.66 2.45 0.70 600.8 291.0 34.8 26.89 52 40.44 0.33 0.49 0.64 2.28 0.67 613.7 322.9 33.6 35.73 53 40.86 0.22 0.34 0.59 2.97 0.65 582.1 284.8 36.8 22.37 54 40.03 0.43 0.54 0.98 2.03 0.80 629.7 294.8 28.5 35.08 55 39.81 0.38 0.67 0.65 0.99 2.95 0.57 604.6 222.3 34.4 29.52 56 39.43 0.31 0.37 0.64 0.89 3.24 0.84 550.4 245.0 36.8 20.82

TABLE 9 Tensile Endurance Mean Sample Added Element (wt %) Strength Stress Breaking Cutting No. Zn Fe Cr Sn Ti Bi Pb Fe/Cr MPa MPa Elongation % Time s 60 40.57 0.54 0.70 0.65 1.01 1.23 0.77 605.6 379.9 16.2 33.45 61 40.30 0.61 0.88 0.66 1.90 1.32 0.69 586.5 363.4 12.9 32.05 62 40.30 0.61 0.88 0.66 1.90 1.28 0.69 586.6 378.4 9.7 36.07 63 40.50 0.63 0.98 0.65 2.98 0.64 626.7 364.4 25.2 24.56 64 40.50 0.63 0.98 0.65 2.65 0.64 646.2 393.2 19.1 29.61 65 40.31 0.51 0.73 0.66 3.13 0.70 604.1 365.0 23.6 22.17 66 40.86 0.22 0.34 0.59 3.53 0.65 580.0 332.0 33.6 19.25 67 40.03 0.43 0.54 0.98 2.45 0.80 626.4 324.4 25.7 28.29 68 40.03 0.43 0.54 0.98 2.34 0.80 646.2 389.9 19.1 31.87 69 39.81 0.30 0.56 0.65 0.99 2.54 0.54 654.3 457.1 19.3 27.25

Claims

1. A high-strength copper alloy containing 20 to 45% of zinc, 0.3 to 1.5% of iron, 0.3 to 1.5% of chromium, 0.2 to 3.5% of aluminum, 0.3 to 3.5% of calcium, and a balance of copper, based on mass.

2. The high-strength copper alloy according to claim 1, wherein a content ratio (Fe/Cr) of said iron to said chromium is 0.5 to 2 based on mass.

3. The high-strength copper alloy according to claim 1, wherein said high-strength copper alloy further contains at least one kind of element selected from the group consisting of 0.05 to 4% of lead, 0.02 to 3.5% of bismuth, 0.02 to 0.4% of tellurium, 0.02 to 0.4% of selenium, and 0.02 to 0.15% of antimony, based on mass.

4. The high-strength copper alloy according to claim 1, wherein said high-strength copper alloy further contains 0.2 to 3% of tin, based on mass.

5. (canceled)

6. The high-strength copper alloy according to claim 1, wherein said high-strength copper alloy further contains at least one kind of element selected from a lanthanoid group consisting of lanthanum, cerium, neodymium, gadolinium, dysprosium, ytterbium, and samarium, and a total content of said at least one kind of element is 0.5 to 5%, based on mass.

7. The high-strength copper alloy according to claim 1, wherein said high-strength copper alloy further contains at least one kind of element selected from the group consisting of 0.5 to 3% of manganese, 0.2 to 1% of silicon, 1.5 to 4% of nickel, 0.1 to 1.2% of titanium, 0.1 to 1.5% of cobalt, and 0.5 to 2.5% of zirconium, based on mass.

8. The high-strength copper alloy according to claim 1, wherein said high-strength copper alloy includes iron-chromium compound particles at grain boundaries.

9. The high-strength copper alloy according to claim 8, wherein said iron-chromium compound particles are particles precipitated at said grain boundaries during solidification in a casting method.

10. The high-strength copper alloy according to claim 9, wherein said iron-chromium compound particles have a particle size of 10 to 50 μm.

11. The high-strength copper alloy according to claim 1, wherein said copper alloy is a copper alloy subjected to hot plastic working after being produced by a casting method.

12. The high-strength copper alloy according to claim 11, wherein said hot plastic working is a working method selected from the group consisting of extrusion, forging, rolling, drawing, and pulling.