US2430306A

US2430306A - Precipitation hardenable copper, nickel, tantalum (or columbium) alloys

Info

Publication number: US2430306A
Application number: US389871A
Authority: US
Inventors: Smith Cyril Stanley
Original assignee: American Brass Co
Current assignee: American Brass Co
Priority date: 1941-04-23
Filing date: 1941-04-23
Publication date: 1947-11-04
Anticipated expiration: 1964-11-04

Description

Nov. 4, 1947. c. 5. SMITH 2,430,306

PRECIPITATION HARDENABLE COPPER, NICKEL,' TANTALUM (OR COLUMBIUM) ALLOYS Filed April 23, 1941 3 Sheets-Sheet 1 Fig.1,

NlcKeL PER CENT INVENTOR Cyril Stanley Smifh BY PM, D ATTORNEYS ALPHA- PHASE BOUNDARIES IN COPPER-NIMEL-TZNTALUM SYSTEM Nov. 4, 1947. c. 5. SMITH PRECIPITATION HARDENABLE COPPER, NICKEL,

TANTALUM (0R COLUMBIUM). ALLOYS Filed April 23, 1941 3 Sheets-Sheet 2 ..c o n w. 0 M n m w 0L. 6 mN 9 L o 0 MW 0 N s u N A k 0 0 o o O 0 0 m 8 6 4 2 mwmz@ m ju5om 0C mu l o n N 2 I o M 4 r. w o n I 0 .9 W i 0 w I. 0 F 6 Y o w 0 L s A 7 M 0 o o 0 0 o 0 w 8 6 4 2 wnuzamwz zdizuor -o--o-- Denotes Alloy Quenched from "00C. and Reheatad. 3 Hours at Temperatures Indicated,

H Denotes Alloy Quenchedfrom 00C., Cold-Rolled 50% Reduction and. ther Reheated -3Hours at Temperatures Indicated.

Fig. 5,

k v x d w 4 wwuz jmkfiom M m m m5 TV, E Wm M [m w ATTORNEY5 Patented Nov. 4, 1947 PRECIPITATION HARDENABLE COPPER,

NICKEL, TANTALUM (OR COLUMBIUM) ALLOYS Cyril Stanley The American Brass Company,

Connecticut Smith, Cheshire, Conn, assigncr to a corporation of Application April 23, 1941, Serial No. 389,871 15 Claims. (Cl. 75159) by the fact that they retain these properties at I unusually high temperatures. The alloys are further particularly characterized by being precipitation hardenable, so that it is possible by heat treatment to improve their physical properties. When cold worked, the alloys are remarkably resistant to softening at elevated temperatures.

The alloys of the invention are composed of about 10% to 50% nickel, about 0.1% to tantalum (or columbium), and the balance chiefly copper. At least about nickel is necessary to provide a copper-nickel base alloy in which an efiective amount of tantalum will dissolve, and more than about 50% nickel gives a base alloy in which tantalum is so soluble that effective heat treatment is not feasible. The combined amounts of copper plus nickel constitute at least about 80% by weight of the alloy, as pointed out more fully below. Within the range stated, alloys composed of about to 35% nickel and about 0.4% to 3% tantalum, with the balance chiefly copper, are generally most useful, and especially satisfactory alloys are composed within the still narrower range of about to nickel, about 1% to 1.75% tantalum, and the balance chiefly copper.

In preparing heat-treatable alloys in accordance with the invention, the amount of tantalum employed within the range specified should be sufficient, in proportion to the amount of nickel present. to render the alloy susceptible to precipitation hardening. The amount of tantalum necessary for this purpose increases with increasing amounts of nickel, and should be sufficient in relation to the amount of nickel to full on the tantalum-rich side of the 800 C. isothermal line of l of the. accompanying drawings. Fig. 1 of the drawings is described more fully below) If co-lumbium, which is the equivalent of tantalum in the new alloys, replaces all or part of the tantalum, then the combined percentage of tantalum and columbium should be sufficient in relation to the amount of nickel so that the numerical value of said combined percentage falls on 'be tolerated in the new the tantalum-rich side of the 800 C. isothermal line of Fig. 1 of the accompanying drawing. 1

Impurities commonly associated with nickel, copper and tantalum in commercial forms may alloys, and additions of other elements may be made, either without detriment to the alloy, or with the attainment of some modification or improvement of its properties. Chief among the elements advantageously added in small amounts are silicon and aluminum. About 0.1% to 2% silicon, and about 0.1% to 2% aluminum, enhance the hardening characteristics of the alloy upon heat treatment.

In heat treating alloys according to the invention, the alloy is first heated to'a temperature above about 950 Cf but below its melting point to cause the tantalumto gointo solid solution. The alloy is then rapidly cooled or quenched, and thereafter preferably is reheated to an elevated temperature of the order of 600 C. to 800 C. Such reheating causes precipitation of the tantalum from solid solution and thereby brings about precipitation hardening of the alloy with significant improvements in tensile properties and hardness. I f

Advantageously the alloy is cold worked after the rapid cooling or quenching and before reheating. Cold working at this stage materially improves hardness and tensile values achieved by subsequent reheating to effect precipitation hardening. Cold working at this stage has the eiiect of decreasing to some extent the temperature to whichit is necessary to reheat the alloy for precipitation hardening, and accordingly reheating to a temperature of 500 C. to 800 C. is contemplated if the alloy has been cold worked preparatory to reheating.

Cold working of the cooled or quenched alloy brings about such improvement in the physical properties of the alloy that in some cases reheating after cold working may be omitted. It is also possible materially to improve the physical propcrtics of the alloy by subjecting it to cold working after reheating to efiect precipitation hardening.

As hereinafter pointed out, precipitation hard"- ened alloys according to the invention are characterized by having a significant proportion of the tantalum (or columbium) present in the alloy in the form of a precipitated compound or phase.

The invention will be better understood from the following description considered in connection with the accompanying drawings, in which Fig. 1 is a plot of a series of isothermal sections through the ternary constitutional model of the system topper nickel-tantalum;

3 Figs. 2 to 5 are a series of charts showing the effect of heat treatment in accordance with the invention on the hardness of various of the new alloys;

Fig. 6 is a chart showing the efiect of corresponding heat treatment on a copper-nickel alloy containing no tantalum; and

Figs. 7 and 8 are charts showing the tensile properties of certain of the alloys of the invention.

Tantalum is not soluble in molten copper to an extent greater than about 0.04%. I have found, however, that tantalum may be dissolved in relatively larger quantities in alloys of copper and nickel. The solubility of the: tantalum in the copper-nickel alloy increases as the nickel concentration increases, and is greater at high temperatures than at low temperatures, as is shown in Fig. 1. The isothermal lines in Fig. 1 show the maximum extent of the alpha solid solution at the various temperatures indicated between 800 C. and 1150 C. On the tantalum-rich side of these lines, the tantalum exists in the form of a compound (or phase) that I believe to approximate NizTa in composition. Below these lines the tantalum is entirely in solid solution, andthe alloy is homogeneous in tructure at the stated temperature, when in equilibrium.

It is the change in solubility of tantalum in the alloy at different temperatures which renders the new alloy susceptible to precipitation hardening. Thus, as appears from Fig. l, a coppernickel alloy-containing 30% nickel will dissolve 2.7% tantalum at 1100 C., an amount that decreases to only 0.7% at 800 C. In order to take advantage of this difierence in the solubility of tantalum at dilferent temperatures to improve the properties of the alloy, the alloy is first heated to a high enough temperature to cause all of the tantalum to enter-solid solution. The alloy is then rapidly cooled or quenched to hold the tantalum in solution. The quenched alloy thereafter is reheated to a sufliciently high temperature and for a sufficient period of time to cause precipitation of the tantalum from the solid solution, thereby bringing about precipitation hardening and attendant improvement in the physical properties of the alloy.

The effect of such heat treatment on the hardness of some typical alloys is shown in Figs. 2 to 5. These alloys were quenched from 1100 C. and reheated at the temperatures shown. The dotted lines show the hardness of the various alloys as reheated directly from the quenched condition, and the solid lines show the hardness of the same alloys treated by cold rolling 50% reduction after quenching but before reheating. The duration of the reheating treatment was three hours. For comparison, the hardness of a similarly heattreated 70/30 cupronickel alloy without tantalum is shown in Fig. 6. The behavior of the alloys containing tantalum is more or less characteristic of precipitation hardening alloys, except for the astonishingly high temperature at which the hardening occurs. Thus, maximum hardness is developed in the quenched alloy of the invention by reheating between 700 C. and 800 C., which may be compared with a temperature of less than 100 C. for aluminum alloys, about 300 C. for beryllium-copper alloys, and about 500 C. for chromium-copper alloys. The latter temperature was the highest heretofore recorded for any alloys of copper.

Related to the high temperature of precipitation of the quenched alloys is the fact that the alloys, when cold worked after quenching, do not commence to soften on annealing until very high temperatures are reached. This is shown clearly in Figs. 2 to 5, and has been confirmed by microscopic examination of alloys with 20% and.30% nickel containing tantalum, which alloys showed no signs of recrystallization after annealing for three hours at temperatures as high as 800 C. A cold-worked 30% copper-nickel alloy without tantalum will recrystallize at 500 C. to 550 0., as shown in Fig. 6. This high softening temperature is obtained with the new alloy whether or not it is reheated for hardening prior to the cold working, but it is advisable that the alloy be initially cooled rapidly from a temperature above about 950 C. to put tantalum in solution if the greatest effect is desired.

Figs. 7 and 8 show the tensile properties of alloys with 20% and 30% nickel, respectively, and with increasing amounts of tantalum. The increase in yield point and tensile strength produced by heat-treatment does not commence until over 1% tantalum is present in the 30% alloy, or about 0.6% in the 20% alloy.

Although particular reference has been made above to copper-nickel alloys containing tantalum, I have found that columbium is substantially the equivalent of tantalum in the new alloys, and that all or part of the tantalum may be replaced by a substantially equal amount by weight of columbium, with the production of an alloy having substantially the same physical properties and susceptibility to the same type of heat treatment as if tantalum alone is employed. I have found that some alloys prepared with the major part of the tantalum replaced by columbium are somewhat less ductile than corresponding alloys made with ferro-tantalum and containing the same total amount of tantalum plus columbium. The base hardness of the former alloy, moreover, was somewhat higher than the base hardness of the alloy prepared from ferro-tantalum, but the hardness, strength, and ductility after heat treatment was practically the same for both alloys.

In preparing the new alloys, no particular difficulties will be encountered by one familiar with the production of cupronickel. Many different practices may be employed. I have generally melted the copper and nickel together, then deoxidized by the addition of a small amount of manganese or magnesium, or both, and added the tantalum. The latter may be in the form of metalli tantalum, a nickel-tantalum alloy containing, for example, 50% tantalum, or as ferrotantalum or ferro-columbium.

Commercial ferro-tantalum contains about 55% tantalum and about 13% columbium, but since columbium is substantially the equivalent of tantalum, the presence of columbium in the ferro alloy may be considered simply as that much more tantalum, insofar as its effect on the physical properties and heat treatment of the alloy is concerned. The addition of the ferro alloy is preferred at the present time, as they are relatively inexpensive and quite satisfactory as long as the tantalum plus columbium content is over about 60% and the aluminum impurity is not too high. When metallic tantalum is used, it may be added in the form of a powder mixed with a small quantity of flux (potassium tantalum fluoride is suitable for this purpose) and slowly poured on to a clean surface of the molten alloy. The tantalum may also be added as briquettes formed by compressing mixed powders of tantalum with copper or nickel, or other elements or alloys. Columbium may be added in a manner similar to tantalum, or tantalum or columbium may be used together, as indicated above.

-minum constitute particularly beneficial additions. Silicon in an amount from 0.1% to 2% increases the extent of hardening of the alloy and is a desirable addition because it aids in the production of gOOd castings, increases the strength and hardness of the alloy, and furthermore makes the resulting alloy somewhat more resistant to oxidation. Preferably about 0.75% silicon is added to achieve these benefits. Aluminum additions from 0.1% to 2% also improve the hardness of the alloy in the heat treated condition and are desirable when maximum hardness is sought. Ordinarily I prefer to add about 0.5% aluminum for this purpose, and if possible, avoid additions of more than 1%, because more than 1% aluminum makes the alloy hard to roll. It is possible, however, to add up to 2% aluminum and yet roll the alloy successfully if proper care is i taken.

Many other elements may be added to the alloy in small amounts, or maybe present as impurities, without adversely affecting the alloy. For example, it is possible to have in the alloy, without particularly disadvantageous results, up to 5.0% iron, up to 0.5% zirconium, up to 5% chromium, up to 3% manganese, up to 1% magnesium, up to cobalt, up to 2% tin, up to 1% arsenic, up to 5% vanadium, up to 5% molybdenum, and up to 5% mm. The foregoing elements in the amounts indicated have little or noeffect on the properties of the alloy, and such elements probably can be tolerated in even larger amounts than specified. It is, of course, contemplated that the aggregate amount of impurities or addrtlons such as those listed will be relatively small and will not exceed about by weight of the alloy, and that the balance of the alloy over and above the nickel and tantalum (or columbium), will be chiefly copper. Generally, not less than about 45% copper will'be present in "the alloy even when high percentage of nickel are employed, and the total of the nickel and copper together will equal at least about 80% to 85% by weight of the alloy.

Alloys in the entire range disclosed above may be used either in the cast or worked condition, and either with or without heat treatment. The

new alloys lend themselves readily to working,

either hot or cold. Unlike many precipitationhardening alloys, the copper-nickel-tantalum alloys may be worked in a fully precipitated condition. In general it is preferableto perform all hot rolling operations and processing anneals at temperatures of about 800 C. to 950 0., at which temperatures the alloys are soft and plastic although the tantalum-rich compound is largely precipitated in the alloy.

When it is desired to heat treat the alloy to develop maximum hardness or strength, the alloy is heated to a temperature preferably between about 950 C. and 1150 C., advantageously about 1050 C to permit all or at least the greater part of tantalum to dissolve. A heating period of fifteen minutes to one hour more or less (ordinarily about thirty minutes), at this temperature is generally sufficient.- This treatment is followed by rapid cooling or quenching of the alloy Ordinarily it. is most convenient to quench the alloy in water, but it may be quenched in oil or in a blast of air or other gas, or it may simply be allowed to cool in air or other gas at ordinary room temperatures. In this manner the'tantalum is held insolid solution. The alloy may then be further treated by reheating for an appropriate period of time at a temperature that will cause the desired precipitation hardening. A reheating temperature in the neighborhood of 600 C. to 800 C. isv usually most satisfactory. The time required for the reheating treatment depends largely on the particular temperature chosen, and also to some extent on the composition of the particular alloy. As an example, however, an alloy containing 20% to 30% nickel and 1% to 2% tantalum has been subjected to successful reheating treatment by reheating at 700 C. to 800 C. for about three hours.

Frequently it is desirable to combine work hardening with precipitation hardening, and to this end the alloy may be cold worked after the high temperature quench and before the precipitation treatment. Such cold working is alone sufficient materially to increase the strength and hardness of the alloy, and moreover, it has the effect of increasing the strength and hardness achieved upon reheating to effect precipitation of the tantalum. The alloy may also be cold worked after the precipitation treatment, and in general the greatest possible strength is obtained by cold working at this stage. It is, of course, obvious that various combinations of working and heating treatment may be employed to enhance the properties of the alloy.

Although the greatest benefit from the addition of tantalum is secured after heat treatment, there is some advantage even when the heat treatment is omitted or when the amount of tantalum is below that necessary for hardening. The strength of copper-nickel alloys is slightly increased by tantalum in solid solution and to a greater extent by the particles of tantalum compounds that are formed without the special heat treatment. The addition of minor amounts of tantalum or columbium has a desirable scavenging effect in copper alloys. The well-known annealing embrittlement of cupronickel containing traces of carbon can be prevented by tantalum or columbium which convertthe carbon to an insoluble harmless carbide.

The tensile properties of various of the new alloys, after being subJected to various heat and work treatments, are given in the following Table I in comparison with a cupronickel alloy containing no tantalum or columbium. All alloys listed in the table contained small amounts of manganese and magnesium as deoxidizers, with the balance copper. The values given in the table represent the average of two tests on a strip 0.05 inch thick. The key to the symbols used to denote treatment of the alloy is as follows:

H=Specimen quenched from 1050 9., rolled 6 B & S numbers, not reheated HR specimen quenched from 1050 0., rolled 6 B & S numbers, reheated three hours at 650 C.

R:Spec1men quenched from 1050 0., rolled 6 B 82; S numbers, reheated three hours at 725 C.

RH=Specimen quenched from 1050 C., reheated three hours at 725 0., cold rolled 6 B dz S numbers.

Q=Specimen quenched from 1050 0., not reheated.

QR=Specimen quenched from 1050 C., reheated three hours at 725 C.

Table I Composition by Analysis Yield Point l Tieab (0.5% Elonga- Tensile Elongation Alloy No. mam tion dll)l1(11l Strength, lb. 111i: 2 hches,

Loa per sq. in. er ent M To Cb Fe Al 81 per m I 2648 29. 61 0. 39 H 78, 300 81, 400 2. 8 R 18, 250 51, 000 42. 5 29.80 1.75 H 0.64 Q 24,400 60,150 33.3 QR 52, 950 91, 700 19. 5

RH

100, 600 119, 350 2. 5 HR 98, 150 114, 350 7. 8 2703 29. 71 2. 03 0. l 0. 55 Q 26, 850 67, 1 0 33. 3 QR 71,850 115,300 16.3 RH 103,600 131,450 1.5 HR 110, 550 135, 950 4. L2704. 29. 81 2. 09 0.10 0. 84 Q 39, 750 33, 250 32.8 QR 80. 450 123, 500 15. 8 RH 104, 750 151, 550 2.0 HR 118, 550 150, 700 5. 5 2649 l 29. 92 1.30 0.30 0. 49 0.89 Q 24, 750 66,100 37- 0 QR 65, 750 1, 000 17. 5 RH 103, 100 136,150 3. 0 HR 134. 650 6. 5 H 94, 950 103, 500 2. 8 2650 29.88 1.45 0.34 0.56 1.19 QR 73,050 97,700 6.0 2705 29.73 1.53 0.36 0.20 0.59 0.86 RH 103,450 164, 550 2.3 HR 109, 350 160, 700 2. 3 2567 30.0 0.36 1.04 0.88 0.22 Q 42,800 77, 33.5 R 200 114, 800 17.5 2070 2 30.0 0. 72 3. 28 1. 70 0. 44 Q 55, 400 95, 300 19. 5

I Tantalum and colum 1 Columbium and tan hium added as term-tantalum.

In Table II are given the tensile strengths at listed in Table I.

talum added as ierro-columbium. (Nominal composition given.)

of wire, cable, rod, sheet, strip, tube, pipe, special shapes, and various formed or machined articles made from such items. They may be hot-forged,

Table II [Tensile Strength at. .1

Alloy No. -1oo 200 j 400 500 5 00 700 I l l Lb. per sq. in. Lb. per sq. in. Lb. per s m. 1 Lb per sq. m 1 Lb per sq. in. 1 Lb. per sq. in. Lb. per sq. in. 2618. 57, 200 49. 500 41. 700 I as. 500 30, 500 I 22, 200 I 15.300 2649 118, 800 110, 200 I 103, 800 i 74 00!) 57,000 I 40,000 i 28.500 2650 99,800 101,000 95,200 73,000 200 26. 200 I 20, 500 2652 102,800 95, 200 as, 700 l as. non o coo 28, 000 j 18, 000

1 Tests on inch diameter rods; Alloy 204$ annealed at 550 C. and air cooled. others annealed at 1,100 3., quenched and reheated three hours at 725 C.

For compositions of the above alloys, see Table I. The foregoing of the new alloys for elevated temperature service. For example, alloy N0. 2649 in the heat treated condition is approximately twice as strong at any given temperature as the cupronickel alloy without tantalum (alloy No. 2648). It will be remembered that cupronickel is the strongest of the commercial alloys of copper that are regularly utilized for elevated'temperature service.

The superiority of the new alloys has also been shown by creep or relaxation tests. Strips of various compositions 0.04 inch thick, were bent over a cast-iron block machined to a radius of 20 inches (computed maximum fibre stress approximately 20,000 lb. per sq. in. on material with a modulus of 20x10 lb. per sq. in.) and the assembly heated to 350 C. for various periods of time. After 184 hours at 350 C. a /30 copper-nickel alloy had taken a permanent set of 67% of the maximum possible, while alloys of similar composition but containing tantalum had taken only between 12% and 23% of the maximum possible set. The cold worked tantalum alloys were slightly superior in resistance to creep to the same alloys in the annealed condition,

although the straight copper-nickel alloy followed the usual behavior of being less resistant to creep when cold worked. This behavior is undoubtedly due to the very high recrystallization temperature of the alloys containing tantalum The new alloys may be produced in -tl.e iorm Table II shows the suitability 45 hot -pressed, or extruded. They may be made into bolts, screws, nuts, etc., where bending, forming, heading or other operations (either hot or cold) are required. They may be welded either autogenously or by electric or gas methods. They may be resistance welded, brazed, or furnace brazed with copper or materials of lower melting point. The alloys also serve as welding rods to provide filler material for electric and gas welding, not only for welding material of the same composition but also for welding iron and steel, cast iron, nickel-base alloys, and other material.

Alloys of copper, nickel and tantalum form an oxide scale on exposure to air at elevated temperatures, but do so to a less extent than alloys of the same nickel content without tantalum. Additions of silicon have in some cases further reduced the scaling to only one-fourth of that of a comparison copper-nickel alloy. Corrosion tests have shown that the addition of 2% tantalum to a 30% cupronickel alloy does not lessen its resistance to corrosion by alternate immersion in a salt spray or by impingement of sea salt solution. The same tantalum-bearing alloy containing 1% silicon has slightly improved corrosion resistance in hydrochloric and sulphuric acids.

The alloys are useful ior many applications which require high strength combined with corrosion res1stance and ready workability. They are particularly suitable for uses at elevated temperatures under corrosive conditions, and may be employed in the cast or worked condition (with or without heat treatment) for power plant components and accessories such as pipes or conveyors for steam, turbine blades, valve bodies, valve stems and seats, boiler, superheater and condenser tubes and tube plates, and expansion joints. Other uses include Bourdon tubes; instrument springs; support wires, grids, plates and other parts for electron tubes; electrical. resistance elements; internal combustion engine parts such as sparkplug electrode wires, valve seats, piston inserts, exhaust pipes; furnace and oven parts; wire screen cloth; a component of thermostatic bi'metal; and many other applications.

The high recrystallization temperature of the alloy permits it to be silver soldered in the cold worked condition without loss of work hardness.

Assemblies in which this alloy is combined with steel can be heat treated for hardening the steel without causing loss of work hardness or softening of the copper-nickel-tantalum alloy, and conversely the steel can be annealed to its minimum hardness without softening the copper alloy. Vitreous enamels fusing at about 800 C. may be applied to the work hardened or precipitation hardened alloy without softening, or enamels or glazes can also be applied during the heatin -to a temperature above 950 C. for solution heat treatment.

Although special reference is made in the foregoing specification and in the appended claims to tantalum-bearing alloys, it is of course apparent from what has been said above that columbium is an equivalent of tantalum in alloys according to the invention and that consequently I contemplate the substitution of columbium for all or a part of the tantalum, if circumstances should make such substitution desirable,

Throughout the foregoing specification and in the appended claims percentages are given by weight.

Iclaim:

1. A precipitation hardenable alloy comprising about 20%, to 30% nickel, about 1% to 1.75% tantalum, and the balance chiefly copper, the combined amounts of copper plus nickel constituting at least about 80% by weight of the alloy, and the amount of tantalum present in the alloy in relation to the amount of nickel therein bein sufiicient to fall on the tantalum-rich side of the 800 C. isothermal line of Fig. 1 of the drawings forming part of the accompanying specification, whereby the amount of tantalum in relation to the amount of nickel is sufficient to render the alloy precipitation hardenable.

2, A precipitation hardenable alloy comprising about to 50% nickel, tantalum in an amount between about 0.1% and 5%, and the balance chiefly copper, the combined amounts of copper plus nickel constituting at least about 80% by weight of the alloy, and the amount of tantalum present in the alloy in relation to the amount of nickel therein being sufficient to fall on the tantalum-rich side of the 800 C. isothermal line of Fig. 1 of the drawings forming part of the accompanying specification, whereby the amount of tantalum in relation to the amount of nickel is sufiicient to render the alloy precipitation hardenable.

3. A precipitation hardenable alloy comprising about to 35% nickel, tantalum in an amount between 0.4% and 3%, and the balance chiefly copper, the combined amounts of copper plus nickel constituting at least about 80% by weight of the alloy, and the amount of tantalum present in the alloy in relation to the amount of nickel therein being sufficient to fall on the tantalumrich side of the 800 C. isothermal line of Fig. 1 of the drawings forming part of the accompanying specification, whereby the amount of tantalum in relation to the amount of nickel is suflicient to render the alloy precipitation hardenable.

4. A precipitation hardenable alloy comprising about 10% to 50% nickel, tantalum in an amount between about 0.1% and 5%, about 0.1% to 2% silicon, and the balance chiefly copper, thecombined amounts of copper plus nickel constitutin at least about 80% by weight of the alloy, and the amount of tantalum present in the alloy in relation to the amount of nickel therein being suflicient to fall on the tantalum-rich side of the 800 C. isothermal line of Fig. 1 of the drawings. forming part of the accompanying specification, whereby the amount of tantalum in relation to the amount of nickel is sufficient to render the alloy precipitation hardenable.

5. A precipitation hardenable alloy comprising about 10% to 50% nickel, tantalum in an amount between about 0.1% and 5%, about 0.1% to 1% aluminum, and the, balance chiefly copper, the combined amounts of copper plus nickel constituting at least about 80% by weight of the alloy, and the amount of tantalum present in the alloy in relation to the amount of nickel therein being sufficient to fall on the tantalumrich side of the 800 C. isothermal line of Fig. 1 of the drawings forming part of the accompanying specification, whereby the amount of tantalum in relation "to the amount of nickel is sufficient to render the alloy precipitation hardenable.

6. A precipitation hardenable alloy composed of about 30% nickel, about 1.75% tantalum, and the balance substantially all copper.

7. A precipitation hardenable alloy composed of about 30% nickel, about 1.75% tantalum, about 0.5% aluminum, and the balance substantially all copper.

8. A precipitation hardenable alloy composed of about 30% nickel, about 1.75% tantalum, about 0.75% silicon, and the balance substantially all copper.

9. A precipitation hardenable alloy comprising about 10% to 50% nickel, at least one metal of the group consisting of tantalum and columbium in an amount between about 0.1% and 5%, and the balance of the alloy being chiefly copper, the combined amounts of copper plus nickel constituting at least about by weight of the alloy, and the combined percentage of tantalum and columbium being sufficient in relation to the amount of nickel so that the numerical value of said combined percentage falls on the tantalumrich side of the 800 C. isothermal line of Fi 1 of the drawings forming part of the accompanying specification, whereby the combined amount of tantalum plus columbium in relation to the amount of nickel is suflicient to render the alloy precipitation hardenable.

10. .A precipitation hardenable alloy comprising copper, nickel and at least one metal of the group consisting of tantalum and colurnbium in proportions within the following ranges:

Per cent Nickel 10 to 50 Tantalum, columbium 0.1 to 5 Copper 45 to 89.9

the combined amounts of copper plus nickel constitutlng at least about 80% by weight of the alloy, and the combined percentage of tantalum and columbium being sufiicient in relation to the amount of nickel so that the numerical value of said combined percentage falls on the tantalum-rich side of the 800 C. isothermal line of Fig, 1 of the drawings forming part of the accompanying specification, whereby the combined amount of tantalum plus columbium in relation to the amount of nickel is sufficient to render the alloy precipitation hardenable.

11. A cupronickel containing about 0.1% to 0.8% of columbium.

12. A precipitation hardened alloy comprising about 10% to 50% nickel, tantalum in an amount between 0.1% and 5%, and the balance chiefly copper, the combined amounts of copper plus nickel constituting at least about 80% by Weight of the alloy, and the amount of tantalum present in the alloy in relation to the amount of nickel therein being sufficient to fall on the tantalumrich side of the 800 C. isothermal line of Fig, 1 of the drawings forming part of the accompanying specification, and characterized in that a significant proportion of the tantalum is present in the alloy in the form of a precipitated phase.

13. A precipitation hardened alloy comprising about to 50% nickel, columbium in an amount between 0.1% and 5% and the balance chiefly copper, the combined amounts of copper plus nickel constituting at least about 80% by weight of the alloy, and the percentage of columbium being sufiicient in relation to the amount of nickel so that the numerical value of such percentage falls on the tantalum-rich side of the 800 C. isothermal line of Fig. 1 of the drawings forming part of the accompanying specification, and characterized in that a significant propor tion of columbium is present in the alloy in the form of a precipitated phase.

14. A cold worked precipitation hardenable alloy comprising about 10% to 50% nickel, tantalum in an amount between 0.1% and 5%, and the balance chiefly copper, the combined amounts of copper plus nickel constituting at least about 80% by weight of the alloy, and that amount of tantalum present in the alloy in relation to the amount of nickel therein being sufiicient to fall on the tantalum-rich side of the 800 C. isothermal line of Fig. 1 of the drawings forming part of the accompanying specification, whereby the amount of tantalum in relation to the amount of nickel is suflicient to render the alloy precipitation hardenable, said cold worked alloy being characterized in that it does not become appreciably softened by prolonged heating at temperatures up to about 800 C.

15. A cold worked precipitation hardenable alloy comprising about 10% to 50% nickel, columbium in an amount between 0.1% and 5%,

and the balance chiefly copper, the combined amounts of copper plus nickel constituting at least about by weight of the alloy, and the percentage of columbium being sufiicient in relation to the amount of nickel so that the numerical value of such percentage falls on the tantalumrich side of the 800 C. isothermal line of Fig. 1 of the drawings forming part of the accompanying specification, whereby the amount'of columbium in relation to the amount of nickel is sufilcient to render the alloy precipitation hardenable, said cold worked alloy being characterized in that it does not become appreciably softened by prolonged heating at temperatures up to about 800 C.

CYRIL STANLEY SMITH.

REFERENCES CITED The following references are of record in the file of this patent:

UNITED STATES PATENTS Number Name Date 2,137,281 Hensel Nov. 22, 1938 2,153,978 Wilkins Apr. 11, 1939 1,992,118 Brownsdorn Feb. 19, 1935 2,012,450 Hook Aug. 27, 1935 961,217 Driver June 14, 1910 1,556,953 Parr Oct, 13, 1925 1,990,168 Corson Feb. 5, 1935 2,281,691 Hansel et a1. May 5, 1942 1,992,325 Schaarwachter Feb. 26, 1935 FOREIGN PATENTS Number Country Date 627,291 Germany Mar, 12, 1936 521,927 Great Britain June 4, 1940 295,971 Great Britain Aug. 21, 1928 OTHER REFERENCES Age Hardening of Metals, 1940, Am. Soc. for Metals, Cleveland, Ohio, pages 321 and 322.