DE1608099A1 - Nickel-containing copper-based alloys - Google Patents

Description

PATENT LAWYERS

ß, w. Schalk · dipl-inc. peter Wirth - | 008029

DIPL.-ING. G.E. M. DANNENBERC DR. V. SCHMIED-ROWARZIK

Dr. P. Wa

6 FRANKFURT AM MAIN

GR. ESCHEMHEIMER STR, S9

BA 12 868 American Metal Ölimax, Ine *

1270 Avenue of the Ameficaa IJew York- Ι.Ϊ. / ü S i

Nickel-containing alloys on copper baaia

The present invention relates also to alloys, if more particularly on nickel nibs on copper feaaia.

kaüeft Kupferaickeliegierungen with einöm nominal Niekelgeiialt 30 ^ a high resistance to attack duföh alkalis, inabesöndere against korifödiedrende effect of siöh sons Bewegeadöitt sea ^ aööer and anaeren Sälzeole-'artigen! solutions * piping Properties' and their äusgezeiöhiiete Beständig- * ness against Crack formation due to coating corrosion make it suitable for use in coolers, as distillation devices, evaporators and warfare tubes and ala clamps. "

Eiae other _t mögllöhe use dej? 7Ot3O copper'iiiökel- ⁱⁱ l »egierungen beateht in Entaalzungsvorrichtungen * DIEA could be a very large-scale Vefwehdung Ain _f inabeaondere, as demand for Ffiaöhwasser constantly waöhBt * However aicherzuatallen the usability for Meerwaaaerumwandlung and around

₂ _ 1608029

constant use in coolers, evaporators, heat exchangers and other corrosion resistant heat transfer devices To preserve, attempts were made to improve the properties of the copper-nickel alloys at high temperatures, so that such devices at the higher temperatures, which are necessary for more economical work can be used. At the moment, for example, the multi-level Flash distillation is one of the more promising procedures for the conversion of sea water · to be «This process requires great heat and large volume handling of the very corrosive, hot sea water with a minimum damage the system for an effective production of fresh water *

The creation of a material with the dual function of durability to high temperatures plus resistance to a highly corrosive environment was difficult and has led to experiments with other metals and alloys. The attempts to replace the TOOO copper-nickel alloys with rust-free Steel de? Types 304 and '5t6, which have fairly good properties

to replace, having shafts at high temperature / were not however special successful, because these steels tend to desalination

("_ ,. it oorrouio-:") necessary high temperatures to be eaten. In order to solve the problems, the technique has therefore once again been of improvement facing the copper-Kickel alloys.

BATH ORIGINAL

45/0378

3 1'6080SS

The previous attempts to improve copper-nickel-alloys were not particularly successful, since it is not sufficient for the material to only have the above-mentioned, white-gold properties. It should also be easy to weld and easy to process hot and cold into bars, tubes, tube plates, grooves, bolts, etc. While many attempts have been made to create such copper-nickel alloys, none have been entirely successful when used on an industrial scale. was put into practice _o

It has now been found that 70: 3R-copper-nickel Legierun2en with üoher strength at temperatures up to 600 ⁰ O. and more, corrosion resistance to hot seawater and fresh water as well as good weldability and machinability economically additional relatively small amounts Ligierun .jSubstanzen can be obtained.

The demand for new 70: "copper-nickel alloys is best with a unique combination of properties, such as improved aging-hardening properties, 'good properties at room temperature and elevated temperatures and / or good properties in forged form and good weldability.

There is also a demand for copper-based alloys with good casting properties and for Lupfer-nickel alloys excellent strength at room temperature and increased Temperatures, which at the same time can easily be processed into the usual and conjugated shapes and structures.

009845/037

- 4 - 1608098

There is also a demand for copper-nickel alloy with good strength in the tension-relieved ("solution annealed") and tempered ("aged") condition as well as in cold-processed and tempered condition.

The present invention relates to improving strength of the 701-30 copper-nickel alloys by adding one or several selected alloy components in relatively small quantities without adversely affecting the processability, Corrosion resistance and / or weldability of these Alloys.

The present invention relates generally to manufacturing easily weldable and machinable copper-nickel alloys with unexpectedly good metallurgical, physical and mechanical properties over a wide temperature range including temperatures up to 6üO ° C. and more, e.g.

C, as well as good resistance to corrosion. “In the presence of hot salty solutions. ? s?

The copper-nickel alloy according to the invention contains 25-35% by weight / O _1, for example 27-33% by weight, nickel; up to 3% by weight of manganese, up to 1.5% by weight of iron; not more than 0.08 wt .- ^ j carbon 0.1-0.7 wt -. <fo titanium and up to 0.6 parts by weight 96 beryllium and beryllium the titanium content to each other and intended to Tenperatur for the alloy. Purpose of use in relation, do that at a use temperature below GOO ⁰ G. the beryllium is present in amounts of at least 0.3 wt .- #; at a use temperature of at least 600 ⁰ C.

BAD ORISiNAL 009845/0378 ~ ^J

16Q8Q8S

possibly the amount of titanium present plus the amount of / present "the beryllium" is at least 0.5 wt .- $ "but below 1.2. When using stones above 700 ⁰ G, the government is expediently practically free of beryllium, and the titanium content is between 0.5-0.7 Grew ..- $. The alloys according to the invention contain copper * which makes up the best of the alloys in addition to H & a, usual impurities and residual oxidizing agents * The copper used suitably has a purity of at least 99.5% *.

In the case of alloys * in accordance with the invention which have the components mentioned in the, indicated _t proportional, quantity ^ a. contained _t after Utelichen Sießereiverfahren, to produce and have a good £ IESS ~ behaves en ι so are Acc * all QBE ^ lächerii the alloy in the "wiö-gögosaeineß" state smoothly * lies © alloys are further characterized t gekemzeiohn & * that they altarungshäirtbar page- fc ^ Senabis are waA good strengths in the solution quality 2uatamd; and tempered guatand i <and also have in the cold-treated and tempered condition *

The Älterungshärtbarkeit or? Ergütbarkeit DER erflndungagemäßen alloys did the in them titanium or titanium contained plus beryllium zxizuaahraiben "assuming" that these elements _± Ά are present the amounts specified above "Thus always iat titanium in ai & n erfindungagemäßen alloys in long of at least" 0 _t t $ _t »iaht more than 0» 7 $% anwasenct * Are less than 0> t $> nwöaencl ^ »o have the; Alloys do not generally correspond

- An ί | ο? Βο & βΗ. on (iift aging ban "· ¥" rg & tiang * to optimal; BATH

- ⁶ - 1608098

to achieve business. If, on the other hand, more than 0.7% titanium is present, the alloys become brittle and difficult to work with. Furthermore, alloys with more than 0.7% titanium surprisingly have a lower strength than alloys which contain titanium in the amounts given above . Purpose the titanium is present in amounts of at least 0.15 ^c / <> . J titanium in amounts of at least 0.5 preferably at least 0.6 $ * fo _t before; If the alloy are, however, used in Teaperaturen than 600 ⁰ C. and is not beryllium present, is located there.

The beryllium significantly improves the properties of the copper-Kiekel alloys according to the invention when used in combination with titanium in the amounts specified above and under the conditions listed of at least>'5 ° f <> _t while the titanium is present in quantities of at least ena Q _t \ fo . However, is the Verweij-making temperature and at least 6QQ ° C _f ao does not need to be present beryllium, mlmgß least ,. Q _t 5 # titanium a & weaena aind "If the titanium content, however, is below 0.5 $ *, beryllium must be present at the same time in such quantities that the sum of beryllium plus titanium is at least 0 _r 5 _% but not more than 1 _t 2 ⁰ At, if α is expediently the alloys according to the invention are practically free of beryllium, d, li * ax contain less than 0.0t f> beryllium, if the use temperature is high, ie over 70O ⁰ Gf. or 7ii0 ° G. lies * Apparently the beryllium forms in öiuem aoloheti Lagierungsayatem bei YergütunciateutiJ.iratui'ea Kwiüciien 500-ο00 ^ο ΰ «© ine Auafalluny * Liegb the reimbursement- or wasting!

BATH ORIGINAL Q09845 / 037I

however, above 600 ° C, the alloys are apparently aged too much and the beryllium appears to agglomerate at the grain boundaries, weakening the alloy. In contrast, the titanium alloy prof acneint the ^ ssystem a fortäauerndes response to allowances in the Tem ^ erdturen between giving Boue-650 C. and larger it at temperatures above 700 ⁰ C. if no

Beryllium is present at the same time.

vVie stated above, the erf indungs common alloys can also nocii up to j Gev /.- yo manganese and up to 1.5 wt .- ^ M sen to the regulations of the US Verteiaigungsministeriums, MII G

contain up to 1.5 wt .- ^ o, e.g. 1 Gevi.-yä, manganese and require 0.4-0.7% by weight of iron. The manganese is added to the Improve weldability and eliminate the disadvantageous Effects of the possible sulfur, which may be present as a deoxidizing agent. Of course, iron carries contributes to the strength of the alloy.

In the alloys according to the invention, silicon can be used in quantities not more than 0.5% by weight, e.g. 0.2 wt .- ^, and expediently not over 0.1 wt. ~? B, can be tolerated. Caused in an amount in excess of 0.3% by weight Silicon hot brittleness

making the alloys difficult to work with and their Use is limited to casting processes only.

0 9 8 4 5/0 37 8,

16080SS

"~ ο -,

The copper-nickel alloys according to the invention are expediently practically free from carbon and elements with a low melting point such as zinc, bismuth, lead, sulfur, tin and phosphorus, since they have a detrimental effect on the otherwise good metallurgical and / or / or physical properties of these alloys to have. Zinc, for example, appears to have a tendency to concentrate in the grain boundaries and thus affects the alloys. Therefore, the tolerable amount of zinc is below about ü, ü1 f °; it is expediently not present in any amount that can be determined by spectral analysis.

Bismuth makes the alloys according to the invention brittle and should be kept below 0.001 fo , while lead, which also has an embrittling effect and can seriously impair the forging behavior, should be kept below 0.01 fo. Tin should not be present at greater than 0.1 fo, as it steiiiperaturen the alloy, especially at the higher Verwendun ^, softens. Furthermore, the presence of tin worsens the otherwise good welding properties of the alloys according to the invention

Phosphorus is another element with an adverse effect on the alloy system and should be kept below $ 0.01 to ensure good hot workability. Therefore should the use of copper waste deoxidized with phosphorus for the production of these alloys can be avoided. carbon Not only causes hot brittleness, just like phosphorus

'■ .-. D ORIGINAL

0098A5 / 0378

rather, it has an adverse effect on the cold workability of the alloys according to the invention. The amount of carbon should preferably be less than 0.08 <fo _t, for example 0.05 ° / °.

Sulfur in amounts as small as 0.01 fi renders the nickel-containing copper alloys unworkable, presumably due to the presence of a nickel-nickel sulfide eutectic with a relatively low scam-melting point that deposits on the grain boundaries. However, the adverse effects of sulfur can be reduced by including either magnesium or manganese during melting. Each of these elements has an affinity for sulfur and combines with any sulfur present to form small globules that do not embrittle during hot working to have.

In practicing the present invention, more advantageous Results obtained when the ingredients used in the melt have a purity of at least $ 99.5 each and when these ingredients are used in the preferred amounts for the particular use temperatures indicated in Table 1 are present.

Table 1

less than

Usage components; $ (the rest is copper and / 0.05 $ temp .; ° C.. carbon)

nickel

titanium

Beryllium Ti & Be

below 600
600-700 °

over 750 *

27-33

27-33

27-33

0.15-0.7 0.15-0.7

0.5-0.7

0.3-0.6 up to 0.6

at least 0.5 Ms 1.2

BATH

0098 * 5 / 037.8

- ίο - 16080SS

Each of these alloys shown in Table 1, which optionally may also contain up to 1.5 ° / ° manganese and up to ι ^l / o iron, has unpaid an ultimate tensile strength (IJTS) than 6300 kg / cm, but cold machined condition if the amount of cold working is at least 50 fo , and a "0.1 ⁰ Jo offset" yield point (IS) of at least 2800 kg / cm after one hour tempering at the very high temperature of 75O ⁰ Co and a yield point (IS ) of at least 6300 kg / cm after tempering for one hour at 600 ^° C.

The present invention also relates to a method for improving physical and metallurgical properties including the strength of copper-based alloys containing 25-35% nickel and optionally up to 3% manganese and up to 1.5 Gev /.- f »contain iron. This predecessor consists in improving the strength of the alloys by hardening and tempering with 0.1-0.7 wt , 3 wt .- $ is present if the alloy is used at temperatures below 600 C. If the alloy is to be used at temperatures above 60O ⁰ C., the sum of titanium and any beryllium present is at least 0.5 wt. - '/', but not more than 1.2 wt .- ^. In a Verwendungstem ^ perature over 700 ⁰ C, such as 75O ⁰ C. z is the ^alloy. Eckuäßi-added _b · beryllium, however, titanium is added in amounts of from 0.5-0.7 wt .- ^.

BATH

009845/0378

- £ 11 - 16080S

To "better understand the present invention and its Advantages are given in the following examples with different amounts of the alloying constituents. In each of these Examples a number of copper-nickel alloys were made, by, can copper and nickel at a temperature of about 1400 ° 0. melted together in a graphite crucible. Every Melt was stirred until all of the nickel was dissolved. Then the temperature of each melt was raised to 135O ° C. decreased, and it the other alloying elements were added and held at this temperature for 5 minutes.

The nickel used in these examples was electrolytic Ilielcel, while the titanium addition was in the form of a copper-titanium alloy which was nominally 24 wt% titanium each Beryllium was also added to the melt in the form of a Copper based alloy nominally containing 4 wt% beryllium. The copper used was of high purity; of course it also uses lower induline copper Purity, e.g. a purity of $ 99.5> usable.

After melting, the copper-based alloys became Formation of castings poured into shapes of "2.5 cm in diameter. The castings were characterized by good, clean, smooth surfaces. Melting and pouring took place under a Söhutz blanket made of argon. According to the invention, the melting and / or Of course, pouring can also be successfully carried out in the air will.

009845/0378

16080SS

Each of the above castings was used to obtain samples for chemical analysis; the composition is given in the following table 2:

Table 2

leg. composition in wt. -Jq

Nickel titanium. Beryllium. copper

1 29.5 0.64 - rest 2 30th 0.19 0.37 rest 3 30th 0.65 0.1 rest 4th 29.9 0.67 0.31 rest VJl 29.95 0.14 0.39 rest 6th 30.1 0.57 - rest 7th 30.8 0.66 - rest 8th 30.2 0.76 - rest 9 * 30.1 0.67 - rest 10 30th 0.15 0.4 rest

* Also contained $ 0.88 iron and 0.98 fi magnesium

According to the procedure used for alloys 1 to 10 became four other copper-nickel alloys not falling under the scope of the present invention, but those of the present invention Alloys appear to be similar, processed into cast blanks 2.5 cm in diameter. According to chemical analysis these four other alloys have the following composition:

Table 3

Leg. Composition in weight - ⁰ Jq

^Nr * Nicifael Titan Beryllium Silioium Niobium Tin Copper

11 29.4 - - 0.52 0.17 - Reat

12 29.2 1.4 - - - - remainder

13 28.9 i, 38 ~ ~ - 2.44 Heat

14 29 1.51 0.07 - - 2.5 Heat

BATH 009845/0378

- ¹ ? - 16Q80S9

Then all 14 alloys were hot rolled by preheating each blank to 95O ⁰ C. for 1 hour. Alloys 1-10 of the invention were successfully rolled down to 0.65 cm diameter bars, while alloys 11-14 not in accordance with the invention splintered. It is therefore clear that the alloys according to the invention are hot workable and valuable in forged form. Furthermore, it can be seen that the increase in the age beyond the upper part of the ranges given above, e.g. as with alloy 12, has a disadvantageous, brittle-making effect.

The hot worked alloys of the present invention were then made subjected to various treatments including heat treatments such as solution heat treatment and quay treatments. These treatments were as follows:

Treatment A ; Solution annealing at 1040 ⁰ C. Holzkonle for 30 minutes and then quenching with water; 71 ^a ! ° cold machined to wire 0.338 cm in diameter; then solution heat treated again at 1040 ^° C. for 30 minutes under charcoal and quenched with water.

Treatment B ; Under charcoal löaimgageglüht 30 minutes at 1040 ⁰ C and quenched with water; Machined to 78 1 ° cold into wire 0.295 cm in diameter; 30 minutes at 1040 ⁰ O. below

e solution agqgM-iht and quenched with water; then worked to 51 »2 % cold to wire 0,201 cm in diameter. Treatment O t 30 minutes with charcoal at 98O ⁰ C. löaungageglüht and abgesohrecktj with water to 90 $ cold worked into wire of 0.201 om diameter x

BAD ORIGINAL ^

003845/0378

Treatment D ; Air-annealed under charcoal for 30 minutes at 90 ° C and quenched with water; 71 % cold to 0.338 cm wire. Machined diameter; then again for 30 minutes under charcoal at 90 ° C. The solution is heated and quenched with water. Treatment E : One hour under charcoal at 104u ° G. solution annealed and quenched with water; to 71 "/ ο cold worked into wire of 0.338 cm diameter; and quenched then again for 30 minutes with charcoal at 1040 ⁰ C. lÖsungegtgLüht and with water.

Treatment ff ; Lösungsgelülit- one hour under Holzko Ie at 1040 ⁰ C. and quenched with water and pulled to yo ° / o to cold wire of 0.201 cm in diameter.

Example 2

To .the properties of the copper-Nici.el alloys according to the invention at room temperature in the non-tempered, but Izalt-machined To show condition, samples of these alloys were made physically tested for breakage; the UTS and IS values in kg / cm were also determined for each sample. The stretch percentages were external orders found in 5) 1 ODi. The results are in Table 4 given;

Table 4

Leg. Treatment of UTS _{or similar} kg / cm YS ₂ strain ~ * BATH ORIGINAL No. 6510 k ^ / cm i ° 1 B. 7650 6000 4th 2 B. 6980 7220 4th 3 B. 8150 6630 3 4th B. 8850 7650 4th 5 C. 6850 8000 3 6th ff 7000 6300 3 7th ff 6950 6510 4th 8th ff 7360 6630 4th 9 ff 7000 4th

009845/037 8

- 15 - 1608QCC

Table 4 shows that the alloys according to the invention have a good strength at room temperature as well as a satisfactory Ductility in the cold worked but not tempered condition to have.

Example 3

In order to take advantage of the favorable properties of the cold machined according to the invention To show alloys at high temperatures, samples of these alloys were made according to that listed in Table 3 Treatment reimbursed. Each alloy was left at the aging temperature for 1 hour held and quenched with water. The results mechanical testing after tempering at the specified temperatures and quenching with water are given in the table listed:

600 Table 5 7000 I 700 ^u erature 7130. 75O ^u 0-. 5050 Leg.
Mr. ₀ Good t erap 7280 G. J 424Ό UTS 2 ^YS
kg / cm 3150 ^u c. I. 8000 UTS ϊ |
kg / cm 5910 7280 4870 1 UTS ₂ IS
kg / cm 7500 7980 4380 5370 3470 2 7800 8440 6050 3150 6440 - 3 8950 7100 7300 6160 5880 5280 4th 9160 7300 6480. 6580 - 5630 5 9300 7280 5420 6090 6510 4870 6th 9900 7280 7430 6550 6830 5630 7th 7630 7770 5150 8th 7980 7140 6830 9 7800 7630 7900

Au3 the test data of Table 5 show that the inventive alloys at temperatures above 600 ° 0, for example, 75O, very valuable Pestigkeitseigenschaften have ⁰ C. In fact, Alloy 1 had an ultimate tensile strength of 6230 kg / cm

009845/037 *

- ie - 16080S9

and a yield strength of 4830 kg / cm when they were tested for cracks after the alloy is first heated to 78o ⁰ C., held for one hour at this temperature and quenched with water \ var <> The alloy 5 had a äuü ^ etting tensile strength

of 4800 kg / cm when tested for breakage after first heated to the very high temperature of 600 C. for one hour and then, had been quenched with water "

As a comparison and to further illustrate the excellent properties of the alloys according to the invention, a number known Eupfer-Nickel alloys and not under the present one Invention of falling alloys made and in above tested as described. These comparison alloys and their composition are given in Table 6:

Table 6

Leg. Components in wt .- $ (the remainder is copper)

* Wrap titanium beryl iron manganese niobium other

lium

15th 30.4 - ■ - 16 28.9 - .15 - 17th 29.4 - , 21 0, 18th 50.4 0; - 19th 29.4 0, - 20th 30.27 - - 21 29.67 - .45 - 22nd 30th - 23 30th 0, - —- -

0.16

0.14 zirconium 0.1 zirconium 0.52 silicon

0.3 chromium -. 0.52 chromium 0.86 1.02

Then, the alloys with the exception of Nos. 21 and 2R of the treatments A to F einor subjected, for one hour at 700 ⁰ C. and 75O ⁰ C. wärmebeliandelt, quenched with water and tested for Bruoh. The results are shown in Table 7. alloy

iärmebehandel BATH ORIGINAL

and 21 St \ were just tired wjirmebehandelt at 600 ^0C.

0098 4 5/0378

Treat, 3 UTS - 17 - 750 ⁰ p. UTS 1608098 70 ( 3180 Table 7 i150 _Lay 6230 temperature 4Ο6Ο Ir / B. 4730 ) ° σ. 4620 B. 3710 ₂ is 3710. 15th B. 6230 875 4030 1000 16 B. 4620 1510 - 945 17th B. 5950 • 2490 - 2660 1b 0 4340 1440 4270 1400 19th 0 4270 1820 6230 1640 20 * 2520 - 21 * 4900 - · 22nd 1720 1580 23 2070 1580

* Heated for 1 hour at 600 ⁰ O. and quenched with water

It can be seen from Tables 5 and 7 that each of the alloys 1 to (according to the invention) has better properties at high temperatures had 15 to 23 than the alloys not according to the invention. Alloys 1 and 9, for example, have a yield strength that is twice as high as the highest value of one when subjected to higher temperature treatment Yield strength of alloy 15 to 23, not falling under the present invention.

A Yergleich of Tables 5 and 7 also shows clearly the effect of the change in the titanium content or titanium plus Bervlliuingehaltee also only slightly below the lower part of the inventively stated range if the intended use temperature is above about 600 G. ^0. This effect is best shown by the alloy 1 according to the invention and the alloy 23 not according to the invention. The yield point of alloy 1

after "a heat treatment at 750 ⁰ O. 5950 kg / cm is something more

0098 4 5/0378

- is - 16080S9

than three times the yield strength value of 1580 kg / cm for alloy 23, which contains 0.45 f> titanium, although alloy 23 was cold worked to 35 1 ° more than alloy 1.

Example 4

The effect of titanium in connection with beryllium in amounts of at least 0.4 was fo (unpaid) by comparing the temperature Zimmert en samples of Alloy 2, the $ 0.19 titanium and 0.37 ^c / o beryllium contained, and alloy 5 containing 0.14 i ° titanium and beryllium containing 0.39 io, shown with alloy 19

Titan ·: ic; -jvut

0.21 </ & / and 0.1 $ beryllium for ins contained only 0.31 f ° titanium and beryllium. Alloy 19 had a yield strength of

2 2

only 6130 kg / cm compared to 7210 kg / cm for alloy 2 and 7980 kg / cm for alloy 5. Alloy 19 was subjected to treatment B like alloy 2 and then subjected to one hour at 700 C. tempered and quenched with water, all showed a yield point of only 1820 kg / cm, while alloy 2 after an identical one Treatment had a yield strength of 4240 kg / cm, which was more than 100% above the value for alloy 19.

Example 5-

To those not obscured by any cold working To show the effect of the remuneration treatment,

"Dead soft" according to and not according to the invention / alloys 2 hours

tempered at different temperatures, quenched with water and tested for breakage. The results are shown in the table. Furthermore, the meohatfnisolien test results were given in the "dead yoft" state and in the unexpected ^ u

BATH ORIGINAL

0098 4 E / 037 8-

■. Treat. "0.1 ⁰ Jo Tabel - 19 - 650 1 608099 un- 8th 3010 Leg. good offset "yield point 2980 in kg / cm ^; (is) Ur. A. 1020 Tempering temperature 3760 in ⁰ G. A. 1960 600 5880 700 750 1 A. 1260 4230 - 3640 2730 2 A. 2700 5180 2380 2480 2240 3 D. 2070 3530 2520 3320 3840 4th E. 1 050 6550 2450 4130 3400 VJl E. 980 3150 2280 - - 6th E. 1190 1960 740 3180 2560 ■ 7th E. - 2030 1260 3180 2560 8th A. co '} 0 2u30 1650 2940 2520 9 A. 1300 2000 1120 2940 2420 15th A. 1610 770 1230 770 810 Ί6 A. 1 u50 1300 - 1260 1230. 17th A. 1260 1680 - 1650 1510 18th D. 1U2Ü. 1120 1020 1050 1050 19th D. 1470 1400 2030 1370 1190 20th JE 1120 1190 - - 21 E. 1330 1510 - 22nd 1120 1190 1120 23 1940 1260 1120

Table 8 shows that alloys 1 "to 9 have a clear response to the tempering, while this" is not the case with the alloys not according to the invention, with the exception of No. 23. Although alloy 23 acheint heat treatable ", its strength decreases scnnell from a tempering temperature of 650 0. upwards from. For example, in the annealing temperature of 75O ⁰ C., the yield strength of only 1120 kg / cm, which is less than half the value of the alloys 1 to 9. The ultimate tensile strengths of the alloys according to the invention are also higher than those of the non-GrfiadungiJije ^ ulseii alloys

009845/0378

Compared to 3 o 20 kg / cm for alloy 18. B eis ρ ie 1 6

16080S9

The properties of "high temperature of erfindungsgeniLucen alloys were represented by Zeitstandverfanren tests with alloy contains 10. At a temperature of 30O ⁰ C. and a load of 5941 kg / cm" did not break the sample even after 2470.4 hours. The minimum smell value for this sample

η cm per
was 1.2 χ 10 / cm / h. That means it would take over 11 years for a 2.5 cm sample to stretch by $ 1 «

In a Testteu perature of 400 ^ ⁰ G. and had the same load another sample at break:; eit of 77 hours and a Mindestkrie-chwert of 1.6 χ 10 cm / cm / hr. With a load of 4571 k; / cm, the rupture time increased to 533.5 hours.

BATH ORIGINAL

') 0 r- /; B / 0 3 7 P.

Claims (9)

- 21 - 1606099 Pat ent claims 1.- alloy Kupferbaais, characterized in that they 25-35 wt .- ^ nickel, up au 3 parts by weight fo manganese, up to 1.5 wt -. $> Iron, not more than 0.08 wt. - $ carbon, 0.1-0.7 wt .- ^ titanium, up to 0.6 wt .- ^ beryllium and the remainder copper, the amount of beryllium at least 0.3 wt .- $ or the amount of Titanium plus any beryllium present is at least 0.5 wt% but less than 1.2 wt%. 2.- Alloy according to claim 1, characterized in that the amount of nickel present is 27-33 wt .- $ and carbon is present in an amount below 0.05 wt .- ^ _o 3. Alloy according to claim 1 and 2, characterized in that the titanium amount 0.1-0.7 wt. % , Preferably 0.15-0.7 wt.% And the beryllium amount 0.3-0 , 6 wt .- ^ for a use ^ temperature of the alloy below 600 ° 0. amounts to. 4.- Alloy according to claim 1 and 2, characterized in that the amount of titanium 0.1-0.7 wt .- ^, preferably 0.15-0.7 wt .- ^, and the amount of titanium plus any beryllium present at least 0.5 wt .- $, but less than 1.2 wt .- $, for a use ^{temperature of the alloy of at least 600 0} G. is. 5. - Alloy according to claim 4, characterized in that the amount of titanium is 0.5- ^{ -i7 wt .- $, the amount of beryllium is below 0.01 and preferably no beryllium is present when the use temperature of the alloy is above 700 ^° C. 6.-Method of making an improved copper-based alloy containing 25-35 wt .- ^ nickel, up to 3 wt .-% & manganese, and up to 1.5 Gey /.- ⁱ ; & iron, the remainder is made of copper, characterized in that it limits the amount of carbon present at less than 0.08 wt .- $, and up to 1.2 wt -. ° / o of the copper present by 0.1-0.7 wt. -? & Titanium and up to 0.6 wt .- ^ o beryllium, with the beryllium amount being either 0.3-0.6 wt .-% or the amount of titanium plus any beryllium present at least 0.5 wt .-? ü, but less than 1.2 wt .-? £ is 7 · - The use of alloys according to claim 3 in machined molds that have been subjected to temperatures below 600 0. 8.- The use of alloys Ansxjrucn 4, the temperatures were subjected mindestaas of 600 ⁰ C. in accordance with the processed form. 9.- The use of alloys according to claim 5 in machined forms that have been subjected to ^{temperatures above 7OU 0 C. »} The patent attorney * BAD ORJ © 1NAL 009.8 4-5 / 0378