DE2135741A1 - Nickel alloy - Google Patents

Description

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Dipping. Λ. Green sugar r.r.-ing. H. Kin :: c! Dey

Dr.-ing. '//. ^ - okr.cir Pq \ B Πtti ΠITlθ 1 ClUΠg 9 1 ^ S 7 £

Lr. rer. nut. ^ V. Fischer L IOO / HI

Munich 22, Moxiniiiinnstr. 43

P 4108-25 ■ July 16, 1971

Special Ketals Corporation Middle Se ~ t; lement Road Nev / Hartfcrd, New York

UNITED STATES.

¹¹ nickel alloy "

The invention relates, to a nickel alloy, and in particular eiiB nickel alloy, which is characterized by a superior combination of strength and ductility.

Nickel alloys and their use at elevated temperatures have been known for some time. Such alloys have already been used with different contents of niobium, iron, Cobalt, aluminum, titanium, boron, carbon, zirconium, chromium and molybdenum are described. Special nickel alloys are used in the U.S. Patent 3,107,167.

However, these known nickel alloys are not yet fully satisfactory in terms of their strength and / or ductility.

The invention is therefore based on the object of a nickel alloy to create a superior combination of properties so / ohl in terms of strength as well as ductility at room temperature and at elevated temperatures excels.

It has been found that this task is accomplished by nickel alloys lets solve that one within beoonderü more critical

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Areas lying content of niobium, cobalt, aluminum, titanium, Have iron, boron, zirconium, chromium, molybdenum, carbon, cerium, vanadium, hafnium and / or tantalum ii.

The invention is thus a nickel alloy consisting essentially of 10 to 15 fa cobalt, 1.2 to 2 ^ aluminum, 2 to 3.5 i "titanium, 0.1 to 2 ^c / o iron, from 0.0025 to 0 , 0125 56 boron, 0.05 to 0.2 fo zirconium, 15 to 19 1 ° chromium, 3 to 5 fo molybdenum »up to 0.15 $> carbon, up to 0.1 ^c / o cerium, up to, to 0.5 ^c ß> vanadium, up to 0.02 fo at least one metal from group II Ades of the periodic table of the elements and 0.2 to 1.2 $ carbide former, and, as the remainder, essentially nickel, with iliobium as the carbide former, tantalum and / or hafnium are present, of which niobium full, tantalum and hafnium, however, count as carbide formers with only half of the actual content in G-evfiohtsprozent ', as well as with the proviso that the sum of aluminum and titanium content is at least 3.6 ^ and the ratio of titanium to aluminum is less than 2.0.

The nickel alloys of the invention are particularly well suited for use in turbine wheels, particularly in the heavy hub portion and can also be used in other areas of turbine construction as well as sheet metal and for fastening means can be used.

Contains a preferred nickel alloy according to the invention (as carbide former) 0.2 to 1.2 percent by weight niobium.

As already mentioned, the niobium content of nickel alloys according to the invention can be between 0.2 to 1.2 ¹ Jo . A job salary

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of at least 0.2 ^c fo it is required to stabilize metal carbides present in arbitrary dispersion. The carbides presumably have the general formula MC, in which "M" is to be regarded as consisting primarily of titanium and molybdenum

is about and presumably has a titanium-molybdenum atomic ratio of VtJ 5:15. Without niobium (in the nickel alloy), the carbides decompose when the alloy is heated for hot working and / or subjected to high-temperature annealing, and precipitate again as a fine grain boundary ~ MC during cooling. It is believed that this fine-grained MC leads to a loss of ductility and strength. Amounts of niobium in excess of 1.2 fi promote the formation of an acicular phase which adversely affects ductility and strength. It is assumed that this phase consists of a nickel-niobium intermetallic compound with the approximate composition Ni ^ ITb. The niobium content of the kick alloys according to the invention is preferably between 0.4 and 0.8

As already mentioned, nickel alloys according to the invention contain 10 to 15 ^c ß> cobalt. A minimum cobalt content of $ 10 »is required for the alloy to have good high temperature strength properties. Higher contents maintain the strength achieved with a cobalt alloy of $ 10 and at the same time increase the ductility of the alloy. Cobalt contents of more than 15 % are too high as they make the alloy susceptible to the formation of harmful acicular phases, for example Ni ^ Nb, which adversely affect ductility and strength. Too high a cobalt content leads to a reduction in the nickel content or balance and initiates the formation

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of Ni * Nb, Ni ₅ Nb is formed when there is not enough nickel to hold the remainder of the niobium not bound in carbides. The cobalt content of the nickel alloys according to the invention is preferably in a range from $ 12 to $ 14.

The aluminum or titanium content of nickel alloys according to the invention is, as already mentioned, 1.2 to 2.0 ^l / o, or 2 to 3 »5 i» · Furthermore, nickel alloys according to the invention must contain aluminum and titanium in a total amount of at least Ϊ 3.6 io included. A minimum salary of $ 1.2> aluminum is

\ required in order to give the alloy sufficient strength. Alloys with an aluminum content of more than 2.0 $ do not have sufficient strength at low temperatures and at elevated temperatures under high tensile loads. A minimum of 2 # titanium is required to ensure the formation of a sufficient amount of / 'phase to give strength to the alloy. The j [ 'phase probably has a composition corresponding to the general formula Μ' * (Al, Ti), in which M 'apparently consists mainly of nickel,

^ which has been replaced to some extent by chromium and molybdenum, with nickel, chromium and molybdenum likely being in an approximate ratio of 95: 3: 2. Nickel alloys containing more than 3.5 # titanium tend to form Ni ₅ Ti, which reduces ductility. As already mentioned, the ratio of titanium to aluminum must be less than 2.0, since the probability that Ni, Ti will form increases as the ratio of titanium to aluminum increases. The minimum content of aluminum + titanium should therefore be 3 »6 ^l / o to ensure that the alloy always

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has a high strength ". The preferred range for the aluminum or titanium content of nickel alloys according to the invention is between 1.3 and 1.8 " / o "or 2.4 and 2.3 fo.

As previously mentioned, the nickel alloys of the invention contain 0.10 to 2 fo iron. The ductility of the alloys increases with increasing iron content from $ 0.10 to $ 2. Iron contents of over $ 2 are disadvantageous insofar as they lead to a loss of high-temperature strength without the ductility increasing further.

The boron content according to the invention nickel alloys is, as already mentioned, from 0.0025 to 0.0125 ^C J> · A boron content of 0.0025 i "is necessary to impart sufficient strength to the alloy. Boron contents of more than 0.0125 ^C J> are detrimental as they increase the likelihood of the formation of boride clusters during solidification which are not eliminated during the subsequent heat treatment. Boride grapes cause a local restriction or limitation of the grain, ie they impede grain growth, which leads to the formation of an uneven grain structure or a non-uniform structure. Uneven structure is disadvantageous with regard to the tensile strength properties perpendicular to the direction of deformation. The boron content of nickel alloys according to the invention is preferably between 0.0050 and 0.0100 ^c ß> *

As already mentioned, nickel alloys according to the invention contain 0.05 to 0.2 ^c /> zirconium. A minimum zirconium content of 0.05 ° ß is necessary in the interest of good deformability and warning ductility. Zirconium contents of more than 0.2 ^ are each

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but disadvantageous because they lead to the formation of nickel-zirconium intermetallic compounds favor that reduce the hot ductility. These intermetallic compounds form because the solubility of zirconium in nickel is limited. The zirconium content nickel alloys according to the invention is preferably in a range from $ 0.06 to $ 0.09.

As already mentioned, nickel alloys according to the invention contain 15 to 19 i> chromium. A chromium content of 15 ^c ß> is required to give the alloy sufficient resistance to oxidation. However, the chromium content should not exceed 19 ° />, since the strength of the nickel alloys of the invention decreases with increasing chromium content. Chromium increases the / '- solution, which in turn reduces the content of J "phase. In the case of chromium content, nickel alloys according to the invention are preferably 16 to 18%

As already mentioned, the carbon content of nickel alloys according to the invention should not exceed $ 0.15. Higher carbon contents lead to the formation of too much MC which could decompose during heating for the purpose of deformation and / or during high temperature heat treatments and precipitate again during cooling as harmful, fine grain boundary MC which is believed to be a Loss of ductility and strength leads. However, a small amount of carbon is often desirable because carbon increases the tensile strength of the alloy. The carbon content of nickel alloys according to the invention is preferably between 0.03 and 0.07 $

As already mentioned, the molybdenum content according to the invention nickel alloys in the range of 3 to 5 should lie i>. A molybdenum

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content of at least 3 ^c ß> is necessary in the interest of high temperature strength. However, molybdenum contents of more than 5 ° k are disadvantageous insofar as molybdenum no longer acts as a solid solution element at higher contents and precipitates in the form of a molybdenum-like garbide. The formation of molybdenum-rich carbides increases the likelihood of the formation of harmful needle-shaped phases, such as Ni-zTi, as it changes the solution of the intermetallic compounds. As already mentioned above, the acicular phases have a disadvantageous effect both in terms of ductility and strength. The molybdenum content of nickel alloys according to the invention is preferably between 3.5 and 4.5 pounds.

In addition to the foregoing alloying additions to the inventive nickel alloys, as already mentioned, up to 0.1 cerium io that improves hot ductility, as well as small Vanadinmengen tend to improve the hot workability, up to 0.5 vanadium and #, as assumed is that metals of group HA improve Korngrenzduktilität and thus reduce the tendency for the formation of grain boundary cracks during creep during long operating or Sinsatzdauer, up to 0.02 i ° of at least one metal of group HA of the Perin contain Indic Table of elements.

Furthermore, the kick alloys of the invention, as already mentioned, instead of niobium, tantalum and / or hafnium, two parts of hafnium or tantalum are required to produce one Part to replace niobium. However, niobium is preferred over tantalum and hafnium.

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Further features, details and advantages of the invention emerge from the following description of exemplary embodiments with reference to the drawing.

It shows:

FIG. 1 shows a diagram of the strength at different ITiob contents;

FIG. 2 shows a diagram of the ductility at different niobium contents;

FIG. 3 a photomicrograph (enlargement factor 10000) a nickel alloy with a niobium content of 0.52 j6;

FIG. 4 shows a photomicrograph (magnification factor 1000) of a nickel alloy with a niobium content of 1.70 fo;

FIG. 5 shows a diagram of the strength, expressed by the breaking time, at different cobalt contents;

FIG. 6 shows a diagram of the ductility at different cobalt contents;

FIG. 7 shows a diagram of the strength, expressed by the breaking time, with different iron contents; and

FIG. 8 a diagram of the ductility at different iron contents,

The following examples illustrate the invention.

example 1

Several samples (A, B, C and D) are melted and closed 2.54 cm thick raw slabs are cast in order to reduce the

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to show the th effect. Sample A contains no mob, sample B 0.52 10 niobium, sample C 1.09 $ 6 niobium and sample D 1.70 YES niobium. The composition of the individual samples can be seen in Table I below.

Table I.

element A. sample C. D. (Wt .- ^) O B. 1.09 1.70 lib 0.037 0.52 0.033 0.024 Zr 13.8 0.036 14.2 14.8 Co 0.19 14.0 0.87 1.22 Pe 0.0047 0.52 0.0057 0.0060 B. 0.06 0.0050 0.05 C. 4.05 4.00 4.10, Mon 19.1 4.10 18.5 18.0 Or 1.33 18.7 1.25 1.26 Al 2.97 1.29 2.83 2.84 Si Heat 2.96 Heat Re at Hi rest

The samples are each

Sheeted 1) to a thickness of 11.68 to 12.19 mm, annealed 4 hours at 1204.4 ⁰ C, balanced at 1176.7 ° C and with a reduction of 15 $> a Bndstärke of about 10.16 nm brought,

2) subjected to a three-stage heat treatment, wherein

Annealed for 4 hours at 996.1 ⁰ C and quenched in oil, are then annealed for 4 hours at 843 »3 ° C and cooled in air and annealed for 16 hours at 76o achliesslich ⁰ C and cooled in air, and

3) checked for strength and ductility.

The test results obtained are shown in Table II below.

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Table II

sample Tensile strength
ability ₂
(kp / mm) ■ Q> r \ «" limit
0.2
(kp / mm) Fracture d
tion
(5Ä) Area allocation
reduction A. 126.9
127.6 87.5
86.8 15.7
15.3 15.2
16.4 B. 135.4
136.1 97.0
96.3 23.9
24.0 31.0
28.4 C. 140.0
140.0 100.5
99.8, 21.2
22.6 27.5
24.8 D. 138.6
127.3 98.9
99.1 14.8
8.1 13.3
9.7

Test results reported in Table II are shown graphically in FIGS. From FIG. 1 it can be seen how the addition of Hiob influences the strength of the alloy, while FIG. XI shows the influence of the addition of Hiob on the ductility of the alloy. Figures 1 and 2 recognize laosen such as strength and JDuktilität of the alloys are improved by Hiobzusätae in a 'range of 0.2 to 1.2 i ", and that _f by an alloying O 4 to 0.8 jijfiob optimum strength - and ductility properties can be achieved

The microphotographs are taken with a "magnification factor of 1000 CHgur 3 and 4" each! " D dar u "d suffer d" ii affect jsu liahtr liobiwngen. . The reproduced in Figure 5 ^ Prob »S has a" iobgehalt of 0.52 i _"y which is to say within dee erfindungsgeaasa proposed range, -during reproduced in Figure 4. Sample J) has a niobium content of 1.70 $ possesses the outside of the range proposed according to the invention. It can be seen from FIGS. 3 and 4 that the sample D is needle-shaped

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BATH ORIQiNAI.

Contains phase that adversely affects ductility and strength, while in the in'Figur 3 reproduced sample B no needle-shaped phase can be seen. The in Figure 4 again given acicular phase is presumably an intermetallic Nickel-Job compound of approximate composition

The production, preparation and testing of samples A, B and D are repeated as described above, with a differentiation however, there is no need to heat the samples for 4 hours at 1204.4 ° C or equalize the samples at 1176.7 ° C. The received Test results are given in Table III below.

Table III

sample Tensile strength
speed λ
(kp / mm) G ^ _{n 9} limit
t
η
(kp / mm) Elongation at break,
(*) Surface area
reduction A. 133.8
134.5 89.3
90.0 22.9
24.6 26.6
28.3 B. 134.0
138.9 89.2
94.5 26.1
23.4 32.6
30.4 D. 138.9
134.2 93.1
92.7 13.5
10.9 14.3
14.1

From the test results shown in Table III it can be seen that niobium has the properties of the alloy in this Case not much improved. Also, from a comparison Table III with Table II shows that alloy sample A according to Table III has better properties than alloy sample A according to Table II. Perhaps test values such as the above are the cause that the metallurgists previously believed that niobium was not a necessary one

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- 12 - or appropriate alloy component for nickel alloys

• -a—

of the type in question here. However, this view is inapplicable, i.e. niobium is required because the machining or deformation conditions, e.g. rolling and forging conditions, do not always depend on certain working methods, e.g. » the working conditions applied when determining the values in table ΠΙ, cut to size or can be adapted to these, and since the addition of niobium makes it superfluous, at the deformation or processing of the alloys so precisely - to comply with conditions. In addition, it should be noted that that the properties of sample B reported in Table II are equal to or better than those reported in Table III Properties of sample A are.

Example 2

Several samples (E, P, G and H) are melted to demonstrate the effect that can be achieved by adding cobalt to the alloy. Sample E contains 8.2, sample P 10.1, sample G 12.1 and sample H 14.1 $ cobalt. The composition of these samples is can be seen from Table IV below.

Table IV Element

Co Zr Pe B

sample G H E. "P 12.1 14.1 8.2 10.1 0.074 0.080 0.070 0.078 4.05 3.99 5.85 3.95 0.0062 - 0.0056 0.0056 0.05 - 0.05 0.05 4.15 4.2o 4.00 4.05 18.9 19.1 19.0 18.8 1.40 1.38 1.32 1.33 3.02 3.00 2.92 2.98 rest rest rest rest

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The samples are each processed or deformed, a three-stage heat treatment, the 4-hour of annealing at 1079.4 ⁰ C and cooling in air for 24 hours annealing at 843.3 ⁰ C and cooling in air and for 16 hours annealing at 76O ⁰ C and cooling in air, subjected and then a tear test at 815.6 C and with a tensile stress of 33.1 kp /

mm subjected. The results of this test are based on the

standing Table Y can be seen. Table V Cross-sectional
reduction (yi) Strain,
(si) 27.2
26.1 sample Travel season
<Hours) 22.0
24.6 26.5
27.3 E. 25.5
32.2 20.8
19.8 35.3
33.0 P. 39.7
34.4 23.9
26.0 33.5
28.0 & 34.1
30.2 22.7
22.8 H 32.0
39.5

The test results compiled in Table V are shown graphically in FIGS. In this context, FIG. 5 shows the influence of the addition of cobalt on the high-temperature strength and FIG. 6 shows the influence of the addition of cobalt on the ductility of the alloy. It can be seen from these figures that a minimum cobalt content of 10 <fo achieves good high temperature strength and the ductility is improved with increasing cobalt content.

B G i a ρ i e 1 3

To the effect obtained by aluminum ala Lef.i jrungseLei.iont to show nonrere specimens (I, J, K, L and H) ^ ea

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Sample ^ JC contains 1.20, sample J 1.40, sample K 1.60, sample L 1.80 and sample M 2.0 fa aluminum. The composition of these samples is shown in Table VI below (all values except for those for Pe, B and 0 are target analytical values).

Table VI

element I. Per J b e K L. M. (Wt. - ^c / o) 1.20 1.40 1.60 1.80 2.00 Al 0.075 0.075 0.075 0.075 0.075 Zr 14.0 14.0 14.0 14.0 14.0 Co 0.12 0.13 0.12 0.13 0.12 Pe 0.0048 0.0057 0.0054 0.0059 0.0055 B. 0.04 0.05 0.06 0.07 0.06 C. 4.25 4.25 4.25 4.25 4.25 Mon 19.3 19.3 19.3 19.3 19.3 Cr 3.05 3.05 3.05 3.05 3.05 Ti ■ rest rest rest rest rest Ni

The samples are processed or deformed, heat-treated and subjected to five different tests. The samples for the first four tests are subjected to the following three-stage heat treatment subject to:

4-hour annealing at 996.1 C and quenching in oil, 4-hour annealing at 843 »3 ° C and cooling in air and for 16 hours annealing at 76o ⁰ C with subsequent cooling in air, the samples for the fifth test also subjected to a three-stage heat treatment with the following steps: 4-hour annealing at 1079.4 ° C and cooling in air, 24-hour annealing at 843.3 G and cooling in air and 16-hour annealing at 760 C and cooling in Air. The first test is a tensile test at 732.2 G and with a tensile stress of

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49 kp / ima, as' firmly 2 a tear test "at 815.6 ⁰ C and with

a tensile stress of 26.2 kp / m, as test 3 another Tear test at 815.6 ° C. with a tensile stress of 33.1 lcp / mm, as test 4 a tensile strength test at room temperature and, as Test 5, a tensile strength test at room temperature was also carried out. The one with the individual samples Results obtained from these five tests are shown in Tables VII below with XI.

Table VII (Test 1)

sample Tearing time,
(Hours.) Tabel Tabel strain
(#> Cross section
reduction ('/ ο) I. 170.8 Tearing time,
(Hours.) Tearing time,
(Hours.) 15.4 22.7 J 199.7 146.4 35.3 23.7 30.1 K 202.5 232.2 41.1 25.4 37.3 L. 181.8 326.3 45.0 27.9 30.8 M. 169.9 429.0 50.9 22.6 34.5 660.1 67.8 VIII (test 2) sample strain
(Jt) Cross-sectional
failure ($) I. 29.9 32.6 J 22.5 26.6 K 18.1 22.1 1 23.0 25.8 M. 20.6 23.4 IX (test 3) sample strain
(%) Cross section
reduction ( ^c / o) I. 15.2 29.8 J 25.5 34.5 K 24.6 28.1 L. 25.5 33.4 M. 23.2 36.8

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Tensile strength
ability 2
(kp / mm) - 16 - X (test 4) Cross-sectional
depletion 119.0 Tabel strain 30.8 sample 131.6 ^ "Limit
ρ
(kp / mm) 28.8 25.8 I. 132.0 75.1 24.4 16.9 J 133.0 84.7 18.7 _v 22.5 K 131.6 86.1 24.0 17.2 L. 85.7 20.4 M. Tensile strength
ability 2
(kp / mm) 84.3 XI (test 5) Cross-section
reduction
(*) 117.7 Tabel strain
(tf) 23.2 sample 128.0 *
2
(kp / mm) 25.4 21.1 I. 132.2 66.8 22.7 19.6 J 126.7 75.5 12.0 17.7 K 125.5 79.9 18.2 18.1 L. 78.8 15.3 M. 79.9

The test results shown in Tables VII, X and XI show that the strength of the alloys decreases when the aluminum ^{content rises above 1.60 c} ß> and often becomes too low when the aluminum content exceeds ^{2 c} ß>. The test results shown in Table VII are based on a high temperature, high tensile test, whereas the test results shown in Tables X and XI are based on tensile tests carried out at room temperature. From the further test results given in Tables VIII and IX it can be seen that and how aluminum contents of up to 2 $ and more increase the strength of alloys tested at elevated temperatures and under medium tensile stress. In the past, these test values would have consisted of one for alloys that had high strength in rough

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temperature and / or at elevated temperatures and high tensile loads must have, like that of ~ the inventive Nickel alloys are required to result in unsuitable Al content.

Example 4

In order to demonstrate the effect achieved by using iron as an alloy component, several additional samples (N, O, P and Q) are melted. The sample N has an iron content of 0.14 $, the sample 0 an iron content of 1.82 $, the sample B has an iron content of 3.99 ° f Q, and the sample has an iron content of 5.85 / o. The composition of the individual samples can be seen from Table XII below.

Table XII

element N sample P. -2- (Wt .- ^) 0.14 . 0 3.99 5.85 Fe 0.085 1.82 0.080 0.082 Zr 13.6 0.078 14.1 13.7 Co 0.0043 13.8 - - B. 0.06 - - 0.06 C. 4.05 - 4.20 4.30 Mon 19.2 4.15 19.1 19.3 Cr 1.34 18.8 1.38 1.38 Al 2.98 1.38 3.00 3.04 Ii rest 3.00 rest rest M. rest

The samples are processed or deformed, subjected to three-stage heat treatment in which it is annealed for 4 hours at 1079.4 ° C and cooled in air and then annealed for 24 hours at 843.3 ⁰ C and cooled in air, and finally 16 hours at 760 ⁰ C and cooled in air, and then a tear strength test at 815.6 ⁰ C and under a tensile stress

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subjected to stress of 33.1 kp / mni. The results of this Tests are given in Table XIII below.

Table XIII

sample Tearing time,
(Hours.) -Strain,
(tf) Cross-sectional
he raind _; ~ ( p ) JT 58.9
59.7 26.4
21.8 25.6
21.4 O 53.0
46.3 28.3
16.8 33.8
36.6 P. 32.0
39.5 22.7
22.8 33.5
28, ο Q 30.2
26.4 28.1
25.5 46.7
33.9

The test results listed in Table XIII are shown graphically in FIGS. The diagram of Figure 7 shows how the addition of iron the high temperature. influences the strength of the alloys, while the diagram in FIG. 8 shows how the addition of iron influences the ductility of the alloys. In this connection, reference should be made to the increase in ductility, ie the higher cross-sectional reduction values which occur with an increase in the iron content of 0.10 to 0.25 ° and further up to 2.0 $.

Example 5

In order to show the superior combination of properties in terms of ductility and strength, those with nickel alloys according to the invention is achieved, several samples (R, S and T) are melted. The composition of these samples is from the following See Table XIY.

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Tabel XIY T element sample 0.09 (Wt .- '/) R. S. 17.1 C. 0.05 0.05 14.0 Cr 17.3 17.4 4.0 Co 13.8 14.0 > 0, l Mon 4.0 4.0 0.46 Pe > 0, l > 0, l 0.1 A / fJb 0.50 0.45 2.50 Y - 0.1 -1.53 Ti 2.50 2.50 0.008 Al 1.52 1.55 0.07 B. 0.008 0.008 Rest. Zr 0.06 0.06 Ni rest rest

The samples are treated as follows:

1) Sample R is thermoformed from a 101.6 mm thick ingot into a 12.7 mm thick iestilatte while the samples S and T each from rods with a diameter of 146.1 mm to rods with a square cross-section and an edge length of 57.2 mm can be thermoformed; '*

2) Samples R, S and T are each a three-stage heat treatment for 4 hours annealing at 1010 ⁰ C and quenching in oil, 4-hour calcination at 843.3 ° C and cooling in air and for 16 hours annealing at 760 C and subjected to cooling in air.

3) Schliesslieh the samples are R, S and T each at room temperature and at 537.8 ⁰ C to a tensile test in the longitudinal direction, ie in Yerforiaungs- BZV /. Rolling direction j a tear test at 815 C and with a tensile load of 30.4 kp / mm, as well as a tensile strength test at room temperature

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door in the transverse direction, ie in a direction perpendicular to the deformation or rolling direction. The test results obtained are shown in Tables XV to XVIiI below. In Table XV "the results of the tensile test at room temperature in the longitudinal direction, in Table XVI, the corresponding test results at 537.8 ⁰ C, in Table XVII, the tensile test and in Table XVIII, the results of tensile testing are listed in the transverse direction at room temperature.

Table XV

sample Tensile strength- €
speed ρ
(kp / mm) (kp / mm) strain
(/ *) Table XVII Cross section
reduction
(*> R. 136.2 98.1 29.7 strain 41.9 S. 128.8 84.8 32.5 36.8 57.1 T 130.9 87.2 31.7 32.4 41.2 Table XVI 34.0 sample Tensile strength
speed ρ
(kp / mm) ^ O 2 ~ ^ ^renze
ρ
(kp / mm) strain
(*) Cross section
reduction
(/ 0 R. 122.2 89.5 28.8 36.9 S. 111.9 74.2 27.9 37.7 T 114.8 74.9 31.0 39.8 sample Tearing time
(Hours.) Cross-sectional
reduction ($) R. 47.2 42.2 S. 7ö, 8 29.9 T 65.0 31.1

Tensile strength
ability 2
(kp / mm) Table XVIII Strain·,.
(Si) Cross-sectional
mind he ung
(*) sample 126.0
129.2 ^ _{n o} limit
2
(kp / mm) 24.4
24.6 27.0
25.9 S.
T 83.3
85.4

The above test results explain the superior combination of properties of nickel alloys according to the invention with regard to ductility and strength. For example, the tested nickel alloys according to the invention have an elongation at break of more than $ 24 and a cross-sectional reduction of $ 26 to $ 27 when tested in the transverse direction. These values are quite impressive when you compare them with those of known nickel alloys that are tested across the deformation or Rolling direction only had an elongation at break of 9 to 15 $ and a cross-section reduction of 11 to 16 ^c ß> .

It goes without saying that the person skilled in the art will find out from the foregoing Explanation of the new teaching of the invention on the basis of special exemplary embodiments, a number of further embodiments and possible applications of the teaching of the invention, which of course is accordingly not restricted to the special exemplary embodiments described above.

1 09837/11 «7

Claims (10)

P 4108-25 - ^ - 16β July 1971 Claims 1. Nickel alloy, consisting essentially of 10 to 15 j6 cobalt, 1.2 to 2.0 # aluminum, 2 to 3.5 # titanium, 0.1 to 2 £ iron, 0.0025 to 0.0125 $> boron , 0.05 to 0.2 ° / o zirconium, 15 to 19 fo chromium, 3 to 5 $ molybdenum, up to $ 0.15 carbon, up to 0.1 $ Ger, up to 0.5 $> vanadium, up to 0.02 ^c / o at least one metal from group HA of the Periodic Table of the Elements and 0.2 to 1.2 $> carbide formers, and, as esters, essentially nickel, with ITiobium, fc tantalum and / or as carbide formers Hafnium are present, of which niobium full, tantalum and hafnium count as carbide formers with only half of the actual content in percent by weight, as well as with the hatred that the sum of aluminum and titanium content is at least 3.6 ^ έ and the ratio of titanium to aluminum is less than 2.0. 2. Nickel alloy according to claim 1, characterized by a content of 0.2 to 1.2 ^ niobium as a carbide former. ^ 3. Nickel alloy according to claim 1 or 2, characterized by a niobium content of 0.4 to 0.8 ^. 4. Nickel alloy according to at least one of claims 1 to 3. characterized by a cobalt content of 12 to 14 ^c °. 5. Nickel alloy according to at least one of claims 1 to 4, characterized by an aluminum content of 1.3 to 1.8 fo. 6. Nickel alloy according to at least one of claims 1 to 5, characterized by a titanium content of 2.4 to 2.8 ^c / a. 109887/1197 7. Nickel alloy according to at least one of claims 1 to 6, characterized by a boron content of " $ 0.005 to $ 0.0100. 8. Nickel alloy according to at least one of claims 1 to 7, characterized by a zirconium content of 0.06 to 0.09 # » 9. Nickel alloy according to at least one of claims 1 to 8, characterized by a chromium content of $ 16 to $ 18. 10. Nickel alloy according to at least one of claims 1 to 9, characterized by a carbon content of 0.03 to 0.07 #. 11 · Nickel alloy according to at least one of Claims 1 to 10, characterized by a molybdenum content of 3.5 to 4.5 56. 109887/1197