KR20020024848A - Cu-Ni-Mn-Sn-Al, Si-Ce, La, Nd, Pr alloys for high strength wire or plate and its manufacturing method - Google Patents

Abstract

PURPOSE: A high strength alloy having new performance is provided in which some of principle alloy elements of Ni and Sn are reduced while elements having functions capable of supplementing material strength and controlling fine structure are added accordingly, and a method for manufacturing the Cu-Ni-Sn alloy is provided. CONSTITUTION: In a copper alloy for high strength wire rods and plates, the Cu-Ni-Mn-Sn-Al, Si-Ce, La, Nd and Pr based alloy comprises 1.0 to 10.0 wt.% of Ni, 0.1 to 10.0 wt.% of Mn, 0.1 to 10.0 wt.% of Sn, 0.1 to 5.0 wt.% of one or more elements selected from the group consisting of Al and Si, 0.01 to 1.0 wt.% of one or more elements selected from the group consisting of Ce, La, Nd and Pr, and a balance of Cu. The method for manufacturing the Cu-Ni-Mn-Sn-Al, Si-Ce, La, Nd and Pr based alloy for high strength wire rods and plates comprises the steps of weighing alloy elements; fusing the alloy elements by continuously injecting and agitating the elements well after the weighing step; manufacturing an ingot by continuously casting or die casting the sufficiently fused alloy elements into plates or rods; performing solution treatment on the manufactured ingot; and aging the solution treated rods or plates.

Description

Copper (nick) -nickel (manganese) -manganese (Ni) -tin (nium) -aluminium (A), silicon (cerium), cerium (ce), lanthanum (La) and nidium Nd), Promethium (Pr) alloy and its manufacturing method {Cu-Ni-Mn-Sn-Al, Si-Ce, La, Nd, Pr alloys for high strength wire or plate and its manufacturing method}

The present invention is a copper (Cu) -nickel (Ni) -manganese (Mn) -tin (Sn) -aluminum (Al), silicon (Si)-cerium (Ce), lanthanum (La), ni Odium (Nd), promethium (Pr) alloys and a method for producing the same.

Among the existing copper alloys, copper (Cu) -nickel (Ni) -tin (Sn) -based ternary alloys exhibit high strength as a spinodal decomposition strengthening effect. The typical composition of this alloy is 9% nickel by weight. (Ni) and 6% tin (Sn), with the remaining 85% composed of copper (Cu).

85% copper (Cu)-9% nickel (Ni)-6% tin (Sn) -based ternary alloy can obtain tensile strength of 1,000 MPa or more through processing heat treatment using spinodal decomposition strengthening effect. It is used for the purpose high strength spring.

However, in the case of copper (Cu) -nickel (tin) -tin (Sn) -based spinodal decomposition-reinforced alloys, when the tin content is 6% or more, the ingot is not available for hot working due to the precipitation of the columnar grain boundary of the tin. The plate, bar and wire rods are produced in part, but there are problems in manufacturing process difficulties, stability of quality, high cost, and mass production, which are very expensive.

An object of the present invention for solving the above problems, in the copper-nickel-tin alloy, nickel and tin as the main alloying element, but one part of the expensive nickel (Ni) and tin (Sn) reduced and thus the material strength The present invention relates to a new high-strength alloy and a method of manufacturing the same by adding elements having a function of complementing and controlling microstructure.

As described above, the alloy and the manufacturing method of the present invention are copper (Cu) -nickel (Ni) -manganese (Mn) -tin (Sn) -aluminum (Al), silicon (Si) -cerium (Ce) for high-strength wire and plate materials. ), Lanthanum (La), nidium (Nd), promethium (Pr) -based alloy manufacturing method, and to reduce some of the expensive nickel (Ni) and tin (Sn) and thereby complement the material strength And by adding elements having a function to control the microstructure.

That is, in the present invention, by adding manganese, the solid-solution strengthening effect, precipitation strengthening by addition of aluminum and silicon, and the addition of cerium, lanthanum, nidium, promethium, etc. Is achieved by improving the properties.

To explain in more detail, the solid solution of copper is added to obtain solid solution, and aluminum and silicon are added for the purpose of precipitation strengthening, but the refining effect of the strong deoxidation in the molten metal is improved and the fluidity of the molten metal is improved. Cerium, rintan, nidium, promethium, etc., added in a small amount, refine the columnar tissues by inoculation effect, and further refine the matrix structure by inhibiting crystal growth during annealing heat treatment after plastic processing in the manufacturing process. In particular, high strength was maintained without deterioration even when exposed to a temperature of 450 ° C. or higher, which is a high temperature aging temperature, and the alloy composition range was 1.0 to 10.0 wt% (% by weight) of nickel (Ni), and 0.1 to 10.0 wt. % Or 1% by weight of manganese (Mn), 0.1 to 10.0 wt% (wt. Percent) tin (Sn), and aluminum (Al) and silicon (Si). 0.1-5.0 wt% (weight percentage) is added by mixing and selecting the above elements, and one or more elements are mixed and selected from the group consisting of cerium, lanthanum, nidium, and promethium, and 0.01 to 1.0. wt% (weight percent) is added, and the remainder is made of copper (Cu) to obtain a high strength copper alloy having a tensile strength of 1,000 Mpa or more, an elongation of 5 to 10%, and an electrical resistivity of 7 to 14 dxcm. Is achieved.

When explaining the configuration and the operation of the embodiment of the present invention to accomplish the object as described above and to perform the task for compensating the conventional drawbacks in detail as follows.

The copper alloy composition for the high strength wire rod and the plate according to the present invention is 1.0 to 10.0 wt% (weight percentage) nickel (Ni), 0.1 to 10.0 wt% (weight percentage) manganese (Mn), and 0.1 to 10.0 wt here. 0.1% to 5.0% by weight (% by weight) of tin (Sn) and one or more elements selected from the group consisting of aluminum (Al) and silicon (Si). 0.01-1.0 wt% (weight percent) was added by mixing one or more elements from the group consisting of cerium, lanthanum, nidium, and promethium, and the remainder was composed of copper (Cu).

In the above, manganese was added to enhance the solid solution.

In the above, aluminum and silicon were added for precipitation strengthening.

In the above, cerium, lanthanum, nidium, promethium and the like were added to improve the properties of the material by finely controlling the crystal structure.

In more detail, manganese, an employment element, was added to copper to obtain a solid solution strengthening effect.

In addition, aluminum and silicon were added for the purpose of precipitation strengthening, but were also added to improve the fluidity of the molten metal as well as the refining effect of the strong deoxidation in the molten metal.

In addition, cerium, lanthanum, nidium, promethium, etc., added in a small amount, refine the columnar tissues by the inoculation effect, and refine the matrix structure by inhibiting crystal growth during annealing heat treatment after plastic processing in the manufacturing process. In order to maintain the high strength without deterioration even when exposed to a temperature of 450 ° C. or higher, which is a high temperature aging temperature, it was added. As a result, the tensile strength of 1,000 Mpa or more and the elongation of 5-10% were obtained through appropriate processing and heat treatment, and the electrical resistivity was 9-17 dxcm.

As a result of the experiments, nickel, which is an excellent element employed in copper alloys, is expensive, but some of them can be replaced by inexpensive manganese having similar performance.

Among the elements with excellent aging reinforcing effect, aluminum and silicon have excellent refining effect.

As a method for crystallization effect, various experiments were selected as cerium, lanthanum, niodidium, promethium, etc. for the inoculation effect of controlling the columnar tablet from the ingot state to the shape of a fine, non-oriented polyhedron. It also has the advantage of being easy and affordable.

And these elements are good for alloying in the case of composite composite master alloys, with low loss of components.

On the other hand, in the case of the present invention, it is necessary to finely control the grains from the casting structure of the ingot to the processing structure as well as the addition of an age hardening element in order to improve the workability up to thin plates and thin wires and the strength of the material. As an inoculation treatment, the elements were found to be effective from the casting ingot stage.

The reason for limiting the nickel (Ni) to 1.0 to 10.0 wt% (weight percentage) in the composition of the present invention is that it is difficult to hot and cold work over a limited composition range, and for this purpose, it has a capacity comparable to that of steel that requires a large force. There is a disadvantage in that the equipment must be used, and below the composition range, there is a disadvantage that does not satisfy the properties of the target material, the numerical range is limited to the composition range of the present invention.

The reason for limiting the manganese (Mn) to 0.1 to 10.0 wt% (weight percentage) in the composition of the present invention is that the meltability worsens the fluidity of the molten metal at the time of the dissolution spirit, the workability is difficult, hot process in the process after the ingot process And cold processing is difficult, and in order to achieve this, there is a disadvantage in that a facility having a capacity comparable to that of steel is required, and below the composition range, there is a disadvantage that does not satisfy the characteristics of the target material, and thus the composition range of the present invention. Numerical limitation was made.

The reason for limiting the tin (Sn) to 0.1 to 10.0 wt% (weight percentage) in the composition of the present invention is that the price of the material rises above the limited composition range, problems occur in plastic processing, and the material properties are also deteriorated. There are disadvantages such as a tendency to appear, and below the composition range, there is a disadvantage that there is no additive effect, and the numerical range is limited to the composition range of the present invention.

In the composition of the present invention, the reason for limiting the selected element by mixing one or more elements from the group consisting of aluminum (Al) and silicon (Si) to 0.1 to 5.0 wt% (percent by weight) is more than a limited composition range. In this case, there is a disadvantage in that the ductility of the material decreases and a problem occurs in the plastic working, and in the below-mentioned composition range, there is a disadvantage in that the additive effect is insufficient.

In the composition of the present invention, the reason for limiting to 0.01 to 1.0 wt% (weight percent) by selecting one or more mixed elements from the group consisting of cerium, lanthanum, nidium, and promethium is limited. In the above, there is a disadvantage in that the ductility of the material is deteriorated and a problem occurs in the plastic working, and below the composition range, there is a disadvantage in that the ductility of the material is deteriorated and the problem occurs in the plastic working. .

In other words, there is almost no effect under the above-mentioned range, and above that, the mechanical properties are adversely affected, so the numerical value is limited to the claims.

The material strength in the copper-nickel-tin alloy may depend only on the spinodal cracking effect, but in the present invention, aluminum, silicon, cerium, lanthanum, nidium, promethium, etc. may be added in addition to the spinodal cracking effect. Precipitation strengthening and organizational micronization were introduced.

That is, aluminum and silicon are added for the purpose of precipitation strengthening, but the refining effect of the strong deoxidation in the molten metal is improved, and the fluidity of the molten metal is improved, and the small amount of cerium, lanthanum, nidium, promethium, etc. The inoculation effect makes the columnar tissues finer and suppresses the crystal growth during annealing heat treatment after plastic working in the manufacturing process to make the matrix tissues finer.

The production method of the present invention having the composition as described above is a copper alloy for high-strength wire and sheet metal alloy range of 1.0 to 10.0 wt% (weight percent) nickel (Ni), and 0.1 to 10.0 wt% (weight percent) manganese ( Mn), 0.1 to 10.0 wt% (weight percent) tin (Sn), and one or more elements selected from the group consisting of aluminum (Al) and silicon (Si) here, 0.1 to 5.0 wt% (% by weight) is added, and 0.01-1.0 wt% (weight percentage) is added by mixing one or more elements in a group consisting of cerium, lanthanum, niodidium, and promethium. The remainder is weighed with copper (Cu),

After weighing, lay the copper (Cu) at the bottom of the furnace, and add a layer of nickel (Ni) on it, cover the copper (Cu) again, cover the nickel (Ni) again, and then cover with copper (Cu). Charge it, and finally cover it with copper (Cu), and then start dissolution. When both copper and nickel are dissolved, slag is removed. Then, when the temperature of the molten metal reaches about 1,250 ℃, the heating is stopped or very After supplying and dissolving manganese (Mn) to a low heat source, and then to tin (Sn), cerium (Ce), lanthanum (La), nidium (Nd), and promethium (Pr) A molten alloy step of continuously adding and stirring the elements selected as additional elements from the crowd;

When alloy elements are sufficiently dissolved and the melt temperature is about 1100 ~ 1250 ℃ and the flowability of the molten metal is improved, in the case of an alloy method where tin can be hot-processed to 4% or less, a thick plate or a diameter of 70 mm or more ingot Ingots are manufactured by continuous casting or mold casting with large diameter rods of 100 mm or more, and in the case of an alloy method having 4% or more of tin, which is advantageous for cold working, a thin plate having a thickness of ingot of 30 mm or less or a diameter of 20 mm Making a ingot by continuous casting with the following small diameter rods,

In the ingot thus prepared, the ingot in the form of plate or small diameter rod is completely homogenized, and then completely removed from the cast structure by 85% or more plastic processing by cold rolling or cold drawing, and then maintained at a temperature of 850 ± 50 ° C. for 0.5 to 1.0 hours. After cooling, the solution is subjected to a solution treatment, and in the case of a plate or a wire produced by hot rolling or extrusion, the solution is subjected to a solution treatment by maintaining the solution at a temperature of 850 ± 50 ° C. for 0.5 to 1.0 hours, followed by solution treatment.

The bar or plate in the intermediate state, which has been solvated, is rolled or drawn as much as the cold working amount according to the target property, and then maintained at 300 to 550 ° C. for 1 to 10 hrs. Reinforcement effect of (Cu _x Ni _y ) _z Sn type spinoidal decomposition products in) -nickel (Ni) -tin (Sn) -based alloys and copper (Cu) -nickel (Ni) -aluminum (Al), silicon ( It undergoes an aging treatment step to obtain reinforcing effect by Cu _x Al, Cu _y Ni _z Al, Ni _x Al, Cu _x Si, Cu _y Ni _z Si and Ni _x Si type precipitates in Si) alloy.

As described above, the present invention is a copper (Cu) -nickel (Ni) -manganese (Mn) -tin (Sn) -aluminum (Al), silicon (Si) -cerium (Ce), and lanthanum (La) for high-strength wire and plate. ), Nidium (Nd), Promethium (Pr) -based alloy manufacturing method, nickel (Ni), manganese (Mn), tin (Sn) as the main alloying elements, expensive nickel and tin Particularly, aluminum (Al), silicon (Si), cerium (Ce), and lanthanum (La) were added, which had a function of compensating the material strength and controlling the microstructure.

That is, in the present invention, by adding manganese, the solid-solution strengthening effect, precipitation strengthening by addition of aluminum and silicon, and the addition of cerium, lanthanum, nidium, promethium, etc. This is an improvement in characteristics.

That is, the solid solution is added to copper to obtain solid solution strengthening effect. Aluminum and silicon are added for the purpose of precipitation strengthening, but the refining effect by the strong deoxidation effect in the molten metal improves the fluidity of the molten metal. The added cerium, lanthanum, nidium, promethium, etc. have the effect of miniaturizing columnar tissues as an inoculation effect, and minimizing the matrix structure by inhibiting crystal growth during annealing heat treatment after plastic processing in the manufacturing process. In particular, even when exposed to a temperature of 450 ° C. or higher, which is a high temperature aging temperature, an advantage of maintaining high strength without deterioration was achieved.

As a result, a high-strength copper alloy having a tensile strength of 1,000 Mpa or more and an elongation of 5 to 10% and an electrical resistivity of 9 to 17 dxcm was obtained as a result of proper processing and heat treatment.

The following Table 1 is an example of the alloys presented in the present invention, Tables 2 and 3 are changes in tensile strength and elongation according to the processing heat treatment, Table 4 is a change in the electrical resistivity value according to the processing heat treatment.

In Table 2, Table 3 and Table 4, in the case of the present invention, copper (Cu) -nickel (Ni) -tin (Sn) -aluminum (Al), silicon (Si) -cerium (Ce), lanthanum ( La), nidium (Nd), and promethium (Pr) -based alloys have a tensile strength of 1,000 Mpa or more and an elongation of 5 to 10%, and a high-strength copper alloy having an electrical resistivity of 9 to 17 dxcm can be produced. Can be.

In particular, in the case where alloy elements such as aluminum (Al), silicon (Si), cerium (Ce), lanthanum (La), nidium (Nd), and promethium (Pr) are added, 450 is added. Even at high temperature aging treatment, many alloys maintain high strength over 900 MPa.

The above results show that new high strength materials such as copper (Cu) -nickel (Ni) -tin (Sn) -aluminum (Al), silicon (Si) -cerium (Ce), and lanthanum (La), which can obtain tensile strength of 1000 MPa or more ), Nidium (Nd), Promethium (Pr) -based alloys have the effect of developing, in particular, the alloy has the advantage of maintaining high strength without deterioration even when exposed to temperatures higher than 450 ℃ high temperature aging temperature It is

Table 1 Types of Alloys and Alloy Components (wt%)

Alloy type Ni Mn Sn Al Si Ce La Cu N6S4Ms.01 6 - 4 - - 0.005 0.002 Remainder N6S4Ms.1 6 - 4 - - 0.05 0.025 Remainder N6S4A.5Ms.01 6 - 4 0.5 - 0.005 0.002 Remainder N6S4A.5Ms.1 6 - 4 0.5 - 0.05 0.025 Remainder N6S4A.5S.5Ms.1 6 - 4 0.5 0.5 0.05 0.025 Remainder N4M2S6A.5S.5Ms.01 4 2 6 0.5 0.5 0.005 0.002 Remainder N4M2S6A.5S.5Ms.03 4 2 6 0.5 0.5 0.015 0.007 Remainder N4M2S6A.5S.5Ms.05 4 2 6 0.5 0.5 0.025 0.012 Remainder N4M2S6A.5S.5Ms.07 4 2 6 0.5 0.5 0.035 0.017 Remainder N6M2S4A.5S.5Ms.01 6 2 4 0.5 0.5 0.005 0.002 Remainder N6M2S4A.5S.5Ms.03 6 2 4 0.5 0.5 0.015 0.007 Remainder N6M2S4A.5S.5Ms.05 6 2 4 0.5 0.5 0.025 0.012 Remainder N6M2S4A.5S.5Ms.07 6 2 4 0.5 0.5 0.035 0.017 Remainder N6M2S2A2Ms.05 6 2 2 2 - 0.025 0.012 Remainder

Table 2 Change in Tensile Strength by Heat Treatment (Unit: MPa)

Sample Name Cold working condition 73% 3 hours aging 300 ℃ 350 ℃ 400 ℃ 450 ℃ N6S4Ms.01 781 775 869 832 730 N6S4Ms.1 764 796 857 847 806 N6S4A.5Ms.01 755 845 952 941 912 N6S4A.5Ms.1 814 845 914 962 905 N6S4A.5S.5Ms.1 970 997 1,027 1,030 970 N4M2S6A.5S.5Ms.01 996 1,131 1,200 1,140 1,068 N4M2S6A.5S.5Ms.03 1,003 1,166 1,171 1,180 1,089 N4M2S6A.5S.5Ms.05 1,000 1,059 1,180 1,132 1,039 N4M2S6A.5S.5Ms.07 1,005 1,111 1,120 1,090 1,000 N6M2S4A.5S.5Ms.01 932 1,010 1,188 1,100 1,063 N6M2S4A.5S.5Ms.03 930 1,016 1,110 1,080 1,000 N6M2S4A.5S.5Ms.05 933 980 1,060 1,055 1,054 N6M2S4A.5S.5Ms.07 930 1,000 1,033 1,082 1,020 N6M2S2A2Ms.05 719 826 867 900 -

Table 3 Change in elongation due to heat treatment (Unit:%)

Sample Name Cold working condition 73% 3 hours aging 300 ℃ 350 ℃ 400 ℃ 450 ℃ N6S4Ms.01 7 11 13 10 10 N6S4Ms.1 6 13 12 12 12 N6S4A.5Ms.01 4 11 9 11 10 N6S4A.5Ms.1 3 9 7 9 9 N6S4A.5S.5Ms.1 4 3 4 4 7 N4M2S6A.5S.5Ms.01 5 4 3 5 5 N4M2S6A.5S.5Ms.03 5 5 5 4 9 N4M2S6A.5S.5Ms.05 4 4 3 5 9 N4M2S6A.5S.5Ms.07 4 4 4 4 3 N6M2S4A.5S.5Ms.01 6 7 4 5 5 N6M2S4A.5S.5Ms.03 6 8 4 3 5 N6M2S4A.5S.5Ms.05 5 7 4 4 6 N6M2S4A.5S.5Ms.07 5 6 4 3 7 N6M2S2A2Ms.05 5 5 4 3 -

Table 4 Variation of Electrical Resistivity by Heat Treatment (Unit: цΩcm)

Sample Name Cold working condition 73% 3 hours aging 300 ℃ 350 ℃ 400 ℃ 450 ℃ N6S4Ms.01 14 12 11 9 9 N6S4Ms.1 13 12 11 10 9 N6S4A.5Ms.01 14 13 12 11 10 N6S4A.5Ms.1 14 13 12 10 10 N6S4A.5S.5Ms.1 17 15 14 12 10 N4M2S6A.5S.5Ms.01 19 17 15 13 13 N4M2S6A.5S.5Ms.03 19 17 15 14 14 N4M2S6A.5S.5Ms.05 19 17 15 14 14 N4M2S6A.5S.5Ms.07 19 17 15 13 14 N6M2S4A.5S.5Ms.01 19 16 14 12 10 N6M2S4A.5S.5Ms.03 18 16 15 12 11 N6M2S4A.5S.5Ms.05 19 16 15 12 11 N6M2S4A.5S.5Ms.07 18 16 13 12 10 N6M2S2A2Ms.05 9 10 9 9 -

Claims (2)

In the copper alloy for high strength wire and plate, 1.0 to 10.0 wt% (wt%) nickel (Ni), 0.1 to 10.0 wt% (wt%) manganese (Mn), 0.1 to 10.0 wt% (wt%) tin (Sn), and 0.1-5.0 wt% (percent by weight) of one or more elements are mixed and selected from the group consisting of aluminum (Al) and silicon (Si), and cerium, lanthanum, nidium, and promethy are added thereto. 0.01-1.0 wt% (weight percent) is added by mixing and selecting one or more elements from a crowd of um, and the remainder is copper-nickel-tin-aluminum, silicon- Cerium, lanthanum, nidium, promethium-based alloys. In the manufacturing method of high strength wire rod and copper alloy for plate, The composition range of the copper alloy for high strength wire and sheet metal is 1.0 to 10.0 wt% (weight percentage) nickel (Ni), 0.1 to 10.0 wt% (weight percentage) manganese (Mn), and 0.1 to 10.0 wt% ( Weight percent) 0.1% to 5.0 wt% (weight percentage) of tin (Sn) and one or more elements selected from the group consisting of aluminum (Al) and silicon (Si) are added thereto. Mixing 0.01 to 1.0 wt% (weight percent) of one or more elements by mixing and selecting one or more elements from a crowd consisting of lithium, lanthanum, nidium, and promethium, and weighing the rest with copper (Cu), After weighing, lay a proper amount of copper (Cu) on the bottom of the melting furnace, add nickel (Ni) on top of it, cover copper (Cu) again, then add nickel (Ni) and cover with copper (Cu). Charge it, but at the end cover it relatively thickly with copper (Cu), start dissolution, and remove both slag when both copper and nickel dissolve, and then stop heating or lower when the temperature of the molten metal reaches about 1,250 ℃. After supplying and dissolving manganese (Mn) to the extent of supplying a heat source, it is then composed of tin (Sn), cerium (Ce), lanthanum (La), nidium (Nd), and promethium (Pr). A molten alloy step of continuously adding and stirring the elements selected as additive elements from the crowd; When alloy elements are sufficiently dissolved and the melt temperature is about 1100 ~ 1250 ℃ and the flowability of the molten metal is improved, in the case of an alloy method where tin can be hot-processed to 4% or less, a thick plate or a diameter of 70 mm or more ingot Ingots are manufactured by continuous casting or mold casting with large diameter rods of 100 mm or more, and in the case of an alloy method having 4% or more of tin, which is advantageous for cold working, a thin plate having a thickness of ingot of 30 mm or less or a diameter of 20 mm Making a ingot by continuous casting with the following small diameter rods, In the ingot thus prepared, the ingot in the form of plate or small diameter rod is completely homogenized, and then completely removed from the cast structure by 85% or more plastic processing by cold rolling or cold drawing, and then maintained at a temperature of 850 ± 50 ° C. for 0.5 to 1.0 hours. After cooling, the solution is subjected to a solution treatment, and in the case of a plate or a wire produced by hot rolling or extrusion, the solution is subjected to a solution treatment by maintaining the solution at a temperature of 850 ± 50 ° C. for 0.5 to 1.0 hours, followed by solution treatment. The bar or plate in the intermediate state, which is solvated, is rolled or drawn as much as the cold working amount according to the target property of the target, and then maintained at 300 to 550 ° C for 1 to 10 hours as an aging treatment. Reinforcement effect of (Cu _x Ni _y ) _z Sn type spinoidal decomposition products in) -nickel (Ni) -tin (Sn) -based alloys and copper (Cu) -nickel (Ni) -aluminum (Al), silicon ( It is manufactured through an aging treatment step to obtain the strengthening effect by Cu _x Al, Cu _y Ni _z Al, Ni _x Al, Cu _x Si, Cu _y Ni _z Si, Ni _x Si type precipitates appearing in the Si) alloy Copper-nickel-tin-aluminum, silicon-cerium, lanthanum, nidium, and promethium-based alloys for high strength wire and plate