Patent Description:
Copper alloys with a combination of relatively high <NUM>% offset yield strength and high electrical / thermal conductivity are difficult to achieve. Copper-beryllium alloys have such properties, but there are many applications in which the presence of beryllium is undesirable. Hence, there is a need for additional copper alloys having such desired characteristics amongst others.

<CIT> discloses an alloy comprising Ni, Si, Zr, optionally < <NUM>% Cr, Mn and/or Zn, balance Cu. Such an alloy may be used for a mold material or an aircraft member.

Disclosed herein are copper-nickel-silicon alloys with a combination of high <NUM>% offset yield strength and high electrical / thermal conductivity. The alloys contain at least nickel, silicon, chromium, manganese, zirconium, and copper. The alloys are defined according to claim <NUM>. Desirably, the alloys do not contain beryllium and/or other certain metals. The alloys are cold worked and then solution annealed to produce fine grain sizes, then aged to form a variety of precipitates such as NiSi and CrZrSi precipitates. This creates a dislocation network with precipitates that come out on the grain boundaries, locking in the fine grain sizes. In particular embodiments, the alloys have a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and an electrical conductivity of at least <NUM>%IACS. Such alloys are useful in applications such as heat management and as high strength and performance electrical connectors, among others.

Disclosed herein are copper alloys, comprising: from <NUM> wt% to <NUM> wt% nickel; from <NUM> wt% to <NUM> wt% silicon; from <NUM> wt% to <NUM> wt% chromium; from <NUM> wt% to <NUM> wt% manganese; from <NUM> wt% to <NUM> wt%zirconium;; and balance copper; wherein the alloy has a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and a conductivity of at least <NUM>% IACS.

The copper alloys generally do not contain beryllium, titanium, iron, cobalt, magnesium, or boron.

The copper alloys may have an ultimate tensile strength of at least <NUM> MPa (<NUM> ksi). The copper alloys may have an elastic modulus of at least <NUM> GPa (<NUM> million psi). The copper alloys may have a % total elongation of at least <NUM>%. The copper alloys may have a ductility of at least <NUM>% to <NUM>%. The copper alloys may have a formability ratio of <NUM>/<NUM> or lower. The copper alloys may contain silicides formed from silicon, chromium, nickel, and manganese.

In some embodiments, the copper alloys have a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi), a conductivity of at least <NUM>% IACS, and a % total elongation to break (TE) of at least <NUM>%.

In other embodiments, the copper alloys have a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi), a conductivity of at least <NUM>% IACS, and an ultimate tensile strength of at least <NUM> MPa (<NUM> ksi).

Also disclosed herein are processes for making a copper alloy that does not contain beryllium and has a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and a conductivity of at least <NUM>% IACS. The processes comprise: cold working a copper-nickel-silicon-chromium-manganese-zirconium alloy to a percentage of cold working (% CW) of <NUM>% to <NUM>%; solution annealing the cold-worked copper-nickel-silicon-chromium-manganese-zirconium alloy; and aging the solution-annealed copper-nickel-silicon-chromium-manganese-zirconium alloy to obtain the copper alloy with a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and a conductivity of at least <NUM>% IACS.

The solution annealing may be performed at a temperature of <NUM> to <NUM> for a time period of <NUM> minutes to <NUM> minutes.

The aging may be performed at a temperature of <NUM> to <NUM> for a time period of <NUM> hours to <NUM> hours. In more specific embodiments, the aging is performed at a temperature of <NUM> to <NUM> for a time period of <NUM> hours to <NUM> hours. The copper alloys formed by these processes are also disclosed.

Also disclosed herein are articles formed from a copper-nickel-silicon-chromium-manganese-zirconium alloy, wherein the alloy has a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and a conductivity of at least <NUM>% IACS.

Amongst other things, the article can be a heat sink; an electrical connector; an electronic connector; a wiring harness terminal; an electric vehicle charger contact; a high voltage/current/power terminal contact; a power connector contact; a midplane connector; a backplane connector; a card edge connector; a photovoltaic system connector; an appliance power contact; a computer power contact; a heat spreader; a bushing or bearing surface; or a component for an electronic device or an electrical device.

Also disclosed are processes of using a copper-nickel-silicon-chromium-manganese-zirconium alloy that has a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and a conductivity of at least <NUM>% IACS, comprising: stamping an article from a strip of the copper-nickel-silicon-chromium-manganese-zirconium alloy.

These and other characteristics of the disclosure are more particularly disclosed below.

The following is a brief description of the drawings, which are presented for the purposes of illustrating the exemplary embodiments disclosed herein.

A more complete understanding of the components, processes and apparatuses disclosed herein can be obtained by reference to the accompanying drawings. These figures are merely schematic representations based on convenience and the ease of demonstrating the present disclosure, and are, therefore, not intended to indicate relative size and dimensions of the devices or components thereof.

All ranges disclosed herein are inclusive of the recited endpoint and independently combinable (for example, the range of "from <NUM> grams to <NUM> grams" is inclusive of the endpoints, <NUM> grams and <NUM> grams, and all the intermediate values).

The present disclosure may refer to temperatures for certain process steps. It is noted that these generally refer to the temperature at which the heat source (e.g. furnace) is set, and do not necessarily refer to the temperature which must be attained by the material being exposed to the heat.

The present disclosure relates to copper alloys as defined in claim <NUM>; they contain nickel, silicon, chromium, manganese, and zirconium. Such alloys have a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and a conductivity of at least <NUM>% IACS, a combination of strength and electrical conductivity that is not readily available. This permits use in heat management applications. Desirably, the alloys are formable, stampable, and free of beryllium.

Nickel is present in the copper alloys in an amount of from <NUM> wt% to <NUM> wt% nickel.

Silicon is present in the copper alloys in an amount of from <NUM> wt% to <NUM> wt%.

Chromium is present in the copper alloys in an amount of from <NUM> wt% to <NUM> wt%.

Manganese is present in the copper alloys in an amount of from <NUM> wt% to <NUM> wt%.

Zirconium is present in the copper alloys in an amount of from <NUM> wt% to <NUM> wt%.

The balance of the copper alloy is copper, excluding impurities.

The copper alloys may also have some impurities, but desirably do not. Impurities include beryllium, titanium, magnesium, and boron. Some of these elements are sometimes added during processing for specific purposes. For example, boron and iron can be used to further enhance the formation of equiaxed crystals and also diminish the dissimilarity of the diffusion rates of Ni and Sn in the matrix during solution heat treatment. Magnesium can serve as a deoxidizer. In the manufacturing processes of the present disclosure, these elements are ideally not used. For purposes of this disclosure, amounts of less than <NUM> wt% of these elements should be considered to be unavoidable impurities, i.e. their presence is not intended or desired.

The Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure are processed to take advantage of multiple strengthening mechanisms. The alloys are cold worked and then solution annealed to keep grains small and fine. The alloys are then aged to bring out a variety of precipitates. Those precipitates can include Ni-Si precipitates, Cr-Zr-Si precipitates, and/or Cr-Ni-Mn-Si precipitates. The cold working creates a dislocation network that that causes the precipitates to come out on the grain boundaries, which locks in the fine grain size. The processes of the present disclosure generally comprise (<NUM>) cold working the Cu-Ni-Si-Cr-Mn-Zr alloy; (<NUM>) solution annealing the cold-worked alloy; and (<NUM>) aging the solution annealed alloy.

Cold working is a metal forming process typically performed near room temperature, in which an alloy is passed through rolls, dies, or is otherwise cold worked to reduce the section of the alloy and to make the section dimensions uniform. This increases the strength of the alloy. The degree of cold working performed is indicated in terms of % reduction in thickness, or % reduction in area, and is referred to in this disclosure as %CW. In the present processes, the alloy is provided as initially cast, and is then cold worked to a %CW of <NUM>% to <NUM>%.

Solution annealing involves heating a precipitation hardenable alloy to a high enough temperature to convert the microstructure into a single phase. A rapid quench to room temperature leaves the alloy in a supersaturated state that makes the alloy soft and ductile, helps regulate grain size, and prepares the alloy for aging. Subsequent heating of the supersaturated solid solution enables precipitation of the strengthening phase and hardens the alloy. In the present processes, after cold working, the cold-worked alloy is solution annealed at a temperature of <NUM> to <NUM>, or from <NUM> to <NUM>, or from <NUM> to <NUM>, or from <NUM> to <NUM>, or from <NUM> to <NUM>, or from <NUM> to <NUM>. The solution annealing may take place over a time period of <NUM> minutes to <NUM> minutes, or from <NUM> minutes to <NUM> minutes, or from <NUM> minutes to <NUM> minutes, or from <NUM> minutes to <NUM> minutes, or from <NUM> minutes to <NUM> minutes, or from <NUM> minutes to <NUM> minutes.

Aging is a heat treatment technique that produces ordering and fine particles (i.e. precipitates) of an impurity phase that impedes the movement of defects in a crystal lattice. This hardens the alloy. In the present processes, after solution annealing, the alloy is aged at a temperature of <NUM> to <NUM> ( <NUM>°F to <NUM>°F), or from <NUM> to <NUM>, or from <NUM> to <NUM>, or from <NUM> to <NUM>, or from <NUM> to <NUM>. The aging may take place over a time period of <NUM> hours to <NUM> hours, or <NUM> hours to <NUM> hours, or <NUM> hours to <NUM> hours, or <NUM> hours to <NUM> hours, or <NUM> hours to <NUM> hours, or <NUM> hours to <NUM> hours It is noted that the aging can be performed in multiple steps, with the temperature of each step being within these stated ranges and the total time of the multiple steps being within these stated ranges. Desirably, the aging is performed in a <NUM>% hydrogen atmosphere.

The resulting copper-nickel-silicon-chromium-manganese-zirconium (Cu-Ni-Si-Cr-Mn-Zr) alloy has a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and an electrical conductivity of at least <NUM>% IACS. In some embodiments, the alloy has a combination of a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) and an electrical conductivity of at least <NUM>% IACS. The <NUM>% offset yield strength is measured according to ASTM E8. In particular embodiments, the alloy has a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi) to <NUM> MPa (<NUM> ksi), or at least <NUM> MPa (<NUM> ksi), or at least <NUM> MPa (<NUM> ksi). In some more specific embodiments, the alloy has an electrical conductivity of at least <NUM>% IACS, or at least <NUM>% IACS, or at least <NUM>% IACS. In other embodiments, the alloy has an electrical conductivity of at least <NUM>% IACS to <NUM>% IACS.

The Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure also have an elastic modulus of at least <NUM> GPa (<NUM> million psi). The elastic modulus is measured according to ASTM E111-<NUM>. The elastic modulus may go up to <NUM> GPa (<NUM> Msi). The Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure may also have an ultimate tensile strength (UTS) of at least <NUM> MPa (<NUM> ksi), or at least <NUM> MPa (<NUM> ksi), or at least <NUM> MPa (<NUM> ksi). The ultimate tensile strength is measured according to ASTM E8. The Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure may also have a thermal conductivity of at least <NUM> W/m·K.

The Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure may also have a % total elongation to break (%TE) of at least <NUM>%, or at least <NUM>%, or at least <NUM>%, or at least <NUM>%. This value measures how much the alloy can be stretched before it breaks, and is a rough indicator of formability. The %TE is also measured according to ASTM E8. Alternatively, the Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure may have a ductility of at least <NUM>% when measured at room temperature (<NUM>). In more particular embodiments, the alloys have a ductility of at least <NUM>% to <NUM>%.

The Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure may alternatively have a formability ratio of <NUM>/<NUM> or lower. Good formability is usually measured by the formability ratio or R/t ratio. This specifies the minimum inside radius of curvature (R) that is needed to form a <NUM>° bend in a strip of thickness (t) without failure, i.e. the formability ratio is equal to R/t. Materials with good formability have a low formability ratio (i.e. low R/t), in other words a lower R/t is better. The formability ratio can be measured using the <NUM>° V-block test, wherein a punch with a given radii of curvature is used to force a test strip into a <NUM>° die, and then the outer radius of the bend is inspected for cracks. The formability ratio can also be reported as the ratio of the formability in the longitudinal (good way) direction to the formability in the transverse (bad way) direction, or as GW/BW.

Any combination of the <NUM>% offset yield strength, electrical conductivity, elastic modulus, ultimate tensile strength, %TE, ductility, and formability ratio discussed above is contemplated for the Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure.

In particular embodiments, the Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure have a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi), a conductivity of at least <NUM>% IACS, a %TE of at least <NUM>%, and a tensile modulus of at least <NUM> GPa (<NUM> Msi).

In particular embodiments, the Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure have a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi), a conductivity of at least <NUM>% IACS, and a UTS of at least <NUM> MPa (<NUM> ksi).

The Cu-Ni-Si-Cr-Mn-Zr alloys of the present disclosure have a combination of good yield strength and high electrical conductivity. The alloys can be provided as strip, wire, rod, tube, and bar. The alloys are also highly solderable and easily plated with other materials. Articles can be formed, for example, by stamping a strip into the desired shape of the final article or an intermediate shape that can be bent into the shape of the final article. The articles can be overcoated, for example with tin or gold or other materials, to provide additional desired properties, either before or after being formed.

The alloys can be used to make, for example, electrical connectors; electronic connectors, terminal contacts, or power contacts, where high strength and high electrical conductivity are desired. Examples of specific articles may include a heat sink in a cellphone; wiring harness terminals; electric vehicle charger contacts; high voltage/current/power terminal contacts; power connector contacts; midplane connectors; backplane connectors; card edge connectors; photovoltaic system connectors; appliance power contacts; computer power contacts; heat spreaders; bushing or bearing surfaces; and generally any component for an electronic device or an electrical device.

The following examples are provided to illustrate the alloys, processes, articles, and properties of the present disclosure.

A Cu-Ni-Si-Cr-Mn-Zr alloy was cast and processed as described above to obtain a strip with a width of <NUM> (<NUM> inches). Its properties were measured at six (<NUM>) locations across the width of the inner and outer wraps, and then averaged. The values were <NUM>% offset yield strength of <NUM> MPa (<NUM> ksi), %TE of <NUM>%, tensile modulus <NUM> GPa (<NUM> Msi), and conductivity of <NUM>% IACS. The R/t ratio was <NUM>/<NUM>.

<FIG> is an optical image of the alloy after processing. Typical grains and some indications of work are visible. Some Ni-Cr silicides are visible.

<FIG> is a BSE SEM image. The dark spots are Cr-Ni-Mn-Si silicides. These silicides have particle sizes on the order of <NUM> nanometers to <NUM>. Their presence is unique, and their small size is unusual. It is noted that these silicides are not visible in <FIG>.

A Cu-<NUM>. 23Ni-<NUM>. 38Si-<NUM>. 23Cr-<NUM>. 08Mn-<NUM>. 02Zr alloy was cast, cold worked to a %CW of <NUM>% to <NUM>%, solution annealed at a temperature of <NUM>° to <NUM>, and then aged twice. The first aging was performed for <NUM> hours at either <NUM>°F, <NUM>°F, or <NUM>°F (<NUM>, <NUM>, <NUM>). The second aging was performed for six hours at <NUM>°F (<NUM>). The <NUM>% offset yield strength (YS) and the electrical conductivity (%IACS) of the alloy were measured at various time points during the second aging, and are illustrated in three graphs.

<FIG> shows the measured YS and %IACS during the second aging, when the first aging was at the temperature of <NUM>°F (<NUM>). At <NUM> hours into the second aging, the YS was <NUM> MPa (<NUM> ksi) and the conductivity was <NUM> %IACS. After <NUM> hours, the YS had fallen to <NUM> MPa (<NUM> ksi), but the conductivity had increased to <NUM> %IACS.

<FIG> shows the measured YS and %IACS during the second aging, when the first aging was at the temperature of <NUM>°F (<NUM>). At <NUM> hours, the YS was <NUM> MPa (<NUM> ksi) and the conductivity was measured at <NUM> %IACS. At <NUM> hours, the YS was <NUM> MPa (<NUM> ksi) and the conductivity was measured at <NUM> %IACS.

Selected results for the tensile and conductivity tests are in Table <NUM> below. Longer aging at <NUM> (<NUM>°F) resulted in higher conductivity as measured by %IACS and decreased <NUM>% offset yield strength.

A chemical analysis was performed to determine the composition of a Cu-Ni-Si-Cr-Mn-Zr alloy as used herein. The analysis indicated a composition of: <<NUM> wt% beryllium, <NUM> wt% cobalt, <NUM> wt% nickel, <NUM> wt% iron, <NUM> wt% silicon, <<NUM> wt% aluminum, <<NUM> wt% tin, <<NUM> wt% zinc, <NUM> wt% chromium, <<NUM> wt% lead, <NUM> wt% manganese, <NUM> wt% zirconium, and balance copper. Amounts listed are reported to the hundredths decimal place. Thus, rounding may affect reported amounts of each element as listed herein.

Strips of the Cu-Ni-Si-Cr-Mn-Zr alloy described in Reference Example <NUM> were rolled to <NUM> (<NUM> inches). The alloy strips were then aged at approximately <NUM> (<NUM>°F) for three hours. Ultimate tensile strength (UTS) in MPa (ksi), <NUM>% offset yield strength (YS) in MPa (ksi), percent elongation to break (%TE), conductivity (measured by %IACS and resistivity), and hardness were assessed for the Cu-Ni-Si-Cr-Mn-Zr alloy, as well as three other copper alloys: C18150 (Cu-<NUM>. 25Zr); C18140M (Cu-<NUM>. 07Si); and C18070 (Cu-<NUM>. 05Ti-<NUM>. The results are outlined in Table <NUM> below. The Cu-Ni-Si-Cr-Mn-Zr alloy had improved tensile strength and <NUM>% offset yield strength when compared with the other alloys tested. The alloy of the present disclosure also had increased resistivity and hardness compared with the other alloys.

Samples of C18140M (Cu-<NUM>. 07Si) alloy, Cu-Ni-Si-Cr-Mn-Zr (composition amounts in Reference Example <NUM>), C18070 (Cu-<NUM>. 05Ti-<NUM>. 02Si) alloy, and C18150 (Cu-<NUM>. 5Zr) alloy were cold-worked to a %CW of <NUM>%. Ultimate tensile strength, <NUM>% offset yield, and % elongation were measured at room temperature. Each alloy was in the form of a long strip, which was coiled up. Measurements were taken at the inner diameter (ID) and the outer diameter (OD) of each strip, corresponding to the beginning of the casting run (ID) and the end of the casting run (OD). The results of these tests are listed in Table <NUM> below. After annealing, the alloy of the present disclosure had an ultimate tensile strength greater than that of the other alloys except the Cu-<NUM>. 5Zr ID alloy. The yield strength and percent elongation were also similar to the other alloys post-annealing.

The alloys were then aged in a furnace at <NUM> (<NUM>°F)REFERENCE for three hours. The samples were water quenched upon removal from the furnace. Results of strength and conductivity testing is listed in Table <NUM>. All alloys had improved ultimate tensile strength when rolled and aged as compared to post-annealing. The Cu-Ni-Si-Cr-Mn-Zr alloy had the highest tensile strength as compared with the other alloys. The alloy also had the lowest %IACS and highest resistivity compared with the other alloys. The alloy of the present disclosure was the only alloy to exhibit <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi).

Hardness of each alloy was also assessed using the Rockwell Hardness 15T Test (15T) and the Vickers Hardness Test (HV). Results are listed in Table <NUM> below. After annealing, the alloy of the present disclosure had a similar average hardness, as measured by the Rockwell 15T Scale, as the C18150 (Cu-<NUM>. 5Zr) alloy. As measured by the Vickers Hardness Test, the Cu-Ni-Si-Cr-Mn-Zr alloy had the highest average hardness post-annealing (as compared with the other alloys post-annealing), and after rolling and aging (as compared with the other alloys after rolling and aging).

Four samples of the Cu-Ni-Si-Cr-Mn-Zr (composition amounts in Reference Example <NUM>) alloy were placed in a furnace at <NUM> (<NUM>°F). After three hours, two of the samples were removed from the furnace and water quenched. The other two samples were removed from the furnace after a total of six hours and subsequently water quenched. Several properties were assessed after processing and aging, including ultimate tensile strength, yield strength, %TE, %IACS, hardness, and resistivity. Results of these tests are in Table <NUM> below. Aging the alloy for six hours resulted in ultimate tensile strength measurements of <NUM> and <NUM> MPa (<NUM> and <NUM> ksi), <NUM>% offset yield measurements of <NUM> and <NUM> MPa (<NUM> and <NUM> ksi), and average hardness of <NUM> HV. Additionally, six hours of aging resulted in the alloy having resistivity measurements of <NUM>µΩ-cm and <NUM>µΩ-cm.

Six samples of the Cu-Ni-Si-Cr-Mn-Zr (composition amounts in Reference Example <NUM>) alloy were placed in a furnace at <NUM> (<NUM>°F). Two samples were removed at each of the intervals of three, six, and twelve hours and water quenched upon removal. Several properties were assessed including ultimate tensile strength, yield strength, elongation, %IACS, hardness, and resistivity. Results for these tests are listed in Table <NUM> below. Ultimate tensile strength and yield strength tended to decrease with longer aging. %IACS tended to increase with longer aging. After aging <NUM> hours, the alloy had the highest average hardness as measured by the Vickers Hardness Test. Resistivity tended to decrease with longer aging.

Four samples of the Cu-Ni-Si-Cr-Mn-Zr (composition amounts in Reference Example <NUM>) alloy were cold worked and annealed. The samples were placed in a furnace at <NUM> (<NUM>°F) for six hours. Then, the furnace temperature was lowered to <NUM> (<NUM>°F), which took <NUM> minutes to <NUM> minutes. Two of the samples remained in the furnace for an additional six hours after the <NUM> (<NUM>°F) heating, totaling twelve hours time-in-furnace. The remaining two samples remained in the furnace for twelve hours after the <NUM> (<NUM>°F) heating, totaling eighteen hours time-in-furnace. Tensile strength, hardness (average of five measurements), and conductivity were assessed and the results are listed in Table <NUM> below. At <NUM> hours aging, the alloy had <NUM>% offset yield strength measurements of <NUM> and <NUM> MPa (<NUM> ksi and <NUM> ksi), the alloy had conductivity of <NUM>% IACS and <NUM> IACS. Longer aging tended to result in lower ultimate tensile strength, yield strength, and hardness. Eighteen hours of aging resulted in increased resistivity and percent elongation as compared with <NUM> hours. At both <NUM> and <NUM> hours of aging, the alloy had greater than <NUM>% IACS.

Four samples of each of C18140M (Cu-<NUM>. 07Si), C18070 (Cu-<NUM>. 05Ti-<NUM>. 02Si), and C18150 (Cu-<NUM>. 25Zr) alloys were cut. Conductivity and tensile measurements were taken on the as-received alloys. The remaining samples were then heated for three hours at <NUM> (<NUM>°F). Tensile strength and conductivity measurements were then taken on these samples. Results of these tests are listed in Table <NUM> below. None of the alloys tested had a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi). Only after aging did the alloys have a conductivity of at least <NUM>% IACS.

Two samples of C18070 (Cu-<NUM>. 05Ti-<NUM>. 02Si) alloy of approximately <NUM> inch thickness were heat treated for six hours. One of the samples was heat treated at <NUM> (<NUM>°F). The other sample was heat treated at <NUM> (<NUM>°F). Upon removal from the furnace, both were water quenched, and their tensile and conductivity properties were assessed.

Eight samples of C18150 (Cu-<NUM>. 25Zr) alloy were taken and heat treated as follows: two were heated at <NUM> (<NUM>°F) for one hour and water quenched; two were heated at <NUM> (<NUM>°F) for two hours and water quenched; two were heated at <NUM> (<NUM>°F) for one hour and water quenched; two were heated at <NUM> (<NUM>°F) for two hours and water quenched. Conductivity and tensile measurements were taken. The results are summarized in Table <NUM> below. None of the alloys tested had a <NUM>% offset yield strength of at least <NUM> MPa (<NUM> ksi). All alloys tested had a conductivity greater than <NUM>% IACS.

Strips comprising from <NUM> wt% to <NUM> wt% nickel; from <NUM> wt% to <NUM> wt% silicon; from <NUM> wt% to <NUM> wt% chromium; from <NUM> wt% to <NUM> wt% manganese; from <NUM> wt% to <NUM> wt% zirconium; and balance copper were made according to the present disclosure and tested.

The alloys were cold worked and annealed. The samples were placed in a furnace at <NUM> (<NUM>°F) for six hours. Then, the furnace temperature was lowered to <NUM> (<NUM>°F), which took <NUM> minutes to <NUM> minutes. The samples were then heated for an additional six hours after the <NUM> (<NUM>°F) heating, totaling twelve hours time-in-furnace. The ultimate tensile strength (UTS), <NUM>% offset yield strength (YS), total elongation to break (%TE), elastic modulus (EM), electrical conductivity (%lACS)Several properties were measured (UTS, Yield Strength, and the formability in both directions (GW, BW). The results are listed in Table <NUM> below, as well as the gauge for each strip.

Claim 1:
A copper alloy, comprising:
from <NUM> wt% to <NUM> wt% nickel;
from <NUM> wt% to <NUM> wt% silicon;
from <NUM> wt% to <NUM> wt% chromium;
from <NUM> wt% to <NUM> wt% manganese;
from <NUM> wt% to <NUM> wt%zirconium; and
balance copper and unavoidable impurities;
wherein the alloy has a <NUM>% offset yield strength of at least <NUM> MPa and a conductivity of at least <NUM>% IACS.