CA1196805A - Alumina-forming nickel-based austenitic alloys - Google Patents
Alumina-forming nickel-based austenitic alloysInfo
- Publication number
- CA1196805A CA1196805A CA000410627A CA410627A CA1196805A CA 1196805 A CA1196805 A CA 1196805A CA 000410627 A CA000410627 A CA 000410627A CA 410627 A CA410627 A CA 410627A CA 1196805 A CA1196805 A CA 1196805A
- Authority
- CA
- Canada
- Prior art keywords
- alloy
- content
- alloys
- nickel
- alumina
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Production Of Liquid Hydrocarbon Mixture For Refining Petroleum (AREA)
- Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
Disclosed are heat resisting alumina-forming, nickel-based austenitic alloys having superior oxidation and carburization resistance, superior creep strength, good high temperature ductility, and good microstructural stability, which alloys consist essentially of (in % by weight):
Cr 20-25 %
Fe 10-15 %
Al 3-6 %
Hf 1-2 %
W 1.5-3.25 %
Nb 1-2 %
Y 0.01- %
C 0.2-0.3 %
Ni balance
Disclosed are heat resisting alumina-forming, nickel-based austenitic alloys having superior oxidation and carburization resistance, superior creep strength, good high temperature ductility, and good microstructural stability, which alloys consist essentially of (in % by weight):
Cr 20-25 %
Fe 10-15 %
Al 3-6 %
Hf 1-2 %
W 1.5-3.25 %
Nb 1-2 %
Y 0.01- %
C 0.2-0.3 %
Ni balance
Description
~9~ S
BACKGROUND OF THE INVENTI ON
BACKGROUND OF THE INVENTI ON
2 'rhis invention relates to alumina-forming
3 nickel-based austenitic alloys having superior oxidation
4 and carburization resistance, superior creep strength, goo~ high temperature ductility, and good microstructural 6 stability.
7 Various industrial processes, especially 8 chemical processes, create an insatiable demand for g alloys which can withstand higher and higher tempèra-tures and environments deleterious to the alloy. One such 11 deleterious environment is a carburizing environment, the 12 effects of which are known to significantly affect plant 13 performance and efficiency in many indus-trial processes.
14 These effects are evidenced in heat treatment equipment, ethylene pyrolysis tubing, carbon dioxide and helium-16 cooled nuclear reactors, coal processing plants, and 17 hydrocarbon reformers.
18 A variety of alloy steels exhibiting both 19 heat and carburization resistance have been developed for use in pyrolysis furnaces for the thermal decom-21 position of organic compounds, such as the steam cracking 22 of hydrocarbons. Generally, the pyrolysis furnace con-23 tains a series of heat-resistant alloy steel tubes in 24 which the reaction occurs. It will be noted that the term "tube" as used herein also includes fittings, pipes and 26 other parts used to contain carburizing materials.
27 It is well known that alloy steels containing 28 various amounts of nickel, chromium, and silicon, as 29 well as the addition of elements such as tungsten and/or niobium, are frequently used in high temperature applica-31 tions. ~owever, after extended use at high temperatures, 32 most, if not all, of these known alloys fail to accomplish 33 all of the above objectives.
3~ The major cause of failure, especially in pyrolysis tubes, is creep rupture, brought about by the 36 combined effect of thermal stress and carburization.
37 Carburization of such tubes, which is the diffusion of 38 carbon into the alloy steel causing the formation of :~9~ 35 1 additional carbides principally at the grain boundaries, 2 and the attendant depletion of the matrix in chromium, 3 brings about both a loss of creep strength and embrittle-4 nent of the grain boundaries. Once the steel has become embrittled, it is more susceptible to Eailure by creep 6 rupture at high temperatures, brittle fracture at low 7 temperatures, or both, because of ther~al stress.
8 Although progress has been rnade in the develop-9 ment of alloy steels capable of withstanding the rigors of high ternperature hydrocarbon environments, there still 11 exists a need in the art for the further development of 12 alloy steels having high temperature properties superior 13 to those known in the art 14 SU~MARY OE` THE INVENTION
I~ accordance with the present invention 16 there is provided alumina-forming nickel~based austenitic 17 alloys having improved oxidation and carburization 18 resistance, improved creep rupture properties, good high 19 temperature ductility, and good microstructural stability.
These alloys can be characterized by the following 21 composition (~ by weight):
22 Cr 20-25 23 Fe 10~15 24 Al 3-6 Hf 1-2 26 W 1.5-3.25 27 Nb 1-2 28 Y n.01-1 29 C 0.2-0.3 Ni balance 31 BRIEF DESCRIPTIO~_OF THE FIGURES
32 Figure 1 is a graph showing the superior creep 33 strellgth and ductility of the alloys of the present 34 invention compared with alloys commercially available for hic~h temperature service.
36 Figure 2 is a graph which again shows the 37 superior creep and ductility properties of the alloys of 3~ the present invention over those conventionally employed.
~.~.96~3C15 1 The alloys represented on this ~raph were first aged at 2 1000C for 3,000 to 5,000 hours before testing.
3 DETAIL~D DESCRIPTION OF TIIE INVENTION
4 Tl~e alloys accordin~ to the present invention are particularly adapted to constitute metallic parts to 6 be used on the inside or outside of reforming and steam 7 cracking furnaces wherein there exists an oxidizing and ~ carburizing atmosphere and operating temyeratures in the 9 range of about 900C to about 1100C.
The alloys of the present invention simulta-11 neously possess the following properties:
12 (a) superior oxidation an~ carburization 13 resistance;
14 (b) good creep stren~th;
(c) good high temperature ductility; and 16 (d) good microstructural stability.
17 The composition of the alloys of the present 18 invention, b~ weight percent based on the total weight of 19 the alloy, can be characterized as follows:
20 Cr 20-25 preferably24-25 21 Fe 10-15 preferably12-1 22 Al 3-6 preferably~-5 23 ~f 1-2 preferably1.5-2 2~ W 1.5-3.25 preferably2.75-3.25 25 Nb 1-2 preferably1.25-1.75 26 Y 0.01-1 preferably0.5-1 27 C 0.2-0.3 preferably0.3 28 The rest being nickel with the usual minimum impurities.
29 In the composition o~ the alloys of the present invention:
31 Chromium (Cr) and aluminum (Al) are jointly 32 responsible for hi~h temperature oxidation and car-33 burization resistance of the alloys. Aluminum in the 34 ran~e oE about 3 to 6 wt.~, preferably from about ~ to
7 Various industrial processes, especially 8 chemical processes, create an insatiable demand for g alloys which can withstand higher and higher tempèra-tures and environments deleterious to the alloy. One such 11 deleterious environment is a carburizing environment, the 12 effects of which are known to significantly affect plant 13 performance and efficiency in many indus-trial processes.
14 These effects are evidenced in heat treatment equipment, ethylene pyrolysis tubing, carbon dioxide and helium-16 cooled nuclear reactors, coal processing plants, and 17 hydrocarbon reformers.
18 A variety of alloy steels exhibiting both 19 heat and carburization resistance have been developed for use in pyrolysis furnaces for the thermal decom-21 position of organic compounds, such as the steam cracking 22 of hydrocarbons. Generally, the pyrolysis furnace con-23 tains a series of heat-resistant alloy steel tubes in 24 which the reaction occurs. It will be noted that the term "tube" as used herein also includes fittings, pipes and 26 other parts used to contain carburizing materials.
27 It is well known that alloy steels containing 28 various amounts of nickel, chromium, and silicon, as 29 well as the addition of elements such as tungsten and/or niobium, are frequently used in high temperature applica-31 tions. ~owever, after extended use at high temperatures, 32 most, if not all, of these known alloys fail to accomplish 33 all of the above objectives.
3~ The major cause of failure, especially in pyrolysis tubes, is creep rupture, brought about by the 36 combined effect of thermal stress and carburization.
37 Carburization of such tubes, which is the diffusion of 38 carbon into the alloy steel causing the formation of :~9~ 35 1 additional carbides principally at the grain boundaries, 2 and the attendant depletion of the matrix in chromium, 3 brings about both a loss of creep strength and embrittle-4 nent of the grain boundaries. Once the steel has become embrittled, it is more susceptible to Eailure by creep 6 rupture at high temperatures, brittle fracture at low 7 temperatures, or both, because of ther~al stress.
8 Although progress has been rnade in the develop-9 ment of alloy steels capable of withstanding the rigors of high ternperature hydrocarbon environments, there still 11 exists a need in the art for the further development of 12 alloy steels having high temperature properties superior 13 to those known in the art 14 SU~MARY OE` THE INVENTION
I~ accordance with the present invention 16 there is provided alumina-forming nickel~based austenitic 17 alloys having improved oxidation and carburization 18 resistance, improved creep rupture properties, good high 19 temperature ductility, and good microstructural stability.
These alloys can be characterized by the following 21 composition (~ by weight):
22 Cr 20-25 23 Fe 10~15 24 Al 3-6 Hf 1-2 26 W 1.5-3.25 27 Nb 1-2 28 Y n.01-1 29 C 0.2-0.3 Ni balance 31 BRIEF DESCRIPTIO~_OF THE FIGURES
32 Figure 1 is a graph showing the superior creep 33 strellgth and ductility of the alloys of the present 34 invention compared with alloys commercially available for hic~h temperature service.
36 Figure 2 is a graph which again shows the 37 superior creep and ductility properties of the alloys of 3~ the present invention over those conventionally employed.
~.~.96~3C15 1 The alloys represented on this ~raph were first aged at 2 1000C for 3,000 to 5,000 hours before testing.
3 DETAIL~D DESCRIPTION OF TIIE INVENTION
4 Tl~e alloys accordin~ to the present invention are particularly adapted to constitute metallic parts to 6 be used on the inside or outside of reforming and steam 7 cracking furnaces wherein there exists an oxidizing and ~ carburizing atmosphere and operating temyeratures in the 9 range of about 900C to about 1100C.
The alloys of the present invention simulta-11 neously possess the following properties:
12 (a) superior oxidation an~ carburization 13 resistance;
14 (b) good creep stren~th;
(c) good high temperature ductility; and 16 (d) good microstructural stability.
17 The composition of the alloys of the present 18 invention, b~ weight percent based on the total weight of 19 the alloy, can be characterized as follows:
20 Cr 20-25 preferably24-25 21 Fe 10-15 preferably12-1 22 Al 3-6 preferably~-5 23 ~f 1-2 preferably1.5-2 2~ W 1.5-3.25 preferably2.75-3.25 25 Nb 1-2 preferably1.25-1.75 26 Y 0.01-1 preferably0.5-1 27 C 0.2-0.3 preferably0.3 28 The rest being nickel with the usual minimum impurities.
29 In the composition o~ the alloys of the present invention:
31 Chromium (Cr) and aluminum (Al) are jointly 32 responsible for hi~h temperature oxidation and car-33 burization resistance of the alloys. Aluminum in the 34 ran~e oE about 3 to 6 wt.~, preferably from about ~ to
5 wt.~, leads to the development of protective A12O3 36 scales on the alloy surface, provided the chromium level 37 is in excess of 20 wt.%. At lower levels of chromium, 38 aluminwn will have a tendency to oxidize internally and a :~3~ `5 protective A12O3 scale will not develop on the alloy 2 surface. Chromium levels in excess of 25 wt. ~ will lead 3 to the precipitation of alpha chromium and sigma phases 4 which lead to microstructural instability. A12O3 scales 5 have been found to be more stable than Cr2O3 scales
6 (which forms in Al free alloys) at temperatures in
7 excess of about 1050C.
8 Chromium also provides strength by virtue of its g presence in solid solution and the formation of chromium 10 carbide particles.
11 Carbon (C) provides strength at elevated tem-12 peratures in the presence of carbide forming elements 13 through the formation of finely dispersed alloy carbides 1~1 in the matrix and discontinuous blocky carbides in the grain boundaries. The latter inhibit grain boundary 16 sliding and thereby constrain rnatrix deformation at a 17 carbon level of 0.2-0.3. Higher levels of carbon promote 18 the formation of a continuous layer of carbide at grain 19 boundaries which serve as an easy path for crack propa-gation and thus impart poor ductility.
21 Hafnium (Hf) additions result in the formation 22 of highly stable hafnium carbides (HfC). These form in 23 preference to chromium carbides during solidification and 24 precipitate as discrete particles at grain boundaries.
This process removes carbon from solution and suppresses 26 the precipitation of chromium carbides and thereby pro-27 motes the formation of discrete particles of haEnium 28 carbides in preference to the continuous carbide boundary 29 film formed in the absence of hafnium.
Yttrium (Y) in levels less than about 1 wt.9~
31 have been shown to significantly improve the adherence of 32 '91203 scales; therefore, a Y content of about 0.01 to 33 1 wt.%, preferably about 0.5 to 1 wt.% is emyloyed for use 34 in the instant alloys.
Tungsten (W) contributes to solid solution 36 strengthening at high temperatures and 1.5 to 3.25 wt.%, 37 preEerably 2.75 to 3.25 wt.~ is employed in the alloys of 38 the present invention.
~g~ 5 Niobium (`l~b), when present in the alloys of 2 the present invention, will form fine niobium carbide 3 precipitates on dislocations in the alloy structure 4 and contributes to the strength of the alloy. Niobium levels of about 1 to 2 wt.% are suitable for use herein, 6 preferred is a niobium content of about 1.25 to 1.75 7 wt.%.
a Nickel constitutes the balance of the alloys
11 Carbon (C) provides strength at elevated tem-12 peratures in the presence of carbide forming elements 13 through the formation of finely dispersed alloy carbides 1~1 in the matrix and discontinuous blocky carbides in the grain boundaries. The latter inhibit grain boundary 16 sliding and thereby constrain rnatrix deformation at a 17 carbon level of 0.2-0.3. Higher levels of carbon promote 18 the formation of a continuous layer of carbide at grain 19 boundaries which serve as an easy path for crack propa-gation and thus impart poor ductility.
21 Hafnium (Hf) additions result in the formation 22 of highly stable hafnium carbides (HfC). These form in 23 preference to chromium carbides during solidification and 24 precipitate as discrete particles at grain boundaries.
This process removes carbon from solution and suppresses 26 the precipitation of chromium carbides and thereby pro-27 motes the formation of discrete particles of haEnium 28 carbides in preference to the continuous carbide boundary 29 film formed in the absence of hafnium.
Yttrium (Y) in levels less than about 1 wt.9~
31 have been shown to significantly improve the adherence of 32 '91203 scales; therefore, a Y content of about 0.01 to 33 1 wt.%, preferably about 0.5 to 1 wt.% is emyloyed for use 34 in the instant alloys.
Tungsten (W) contributes to solid solution 36 strengthening at high temperatures and 1.5 to 3.25 wt.%, 37 preEerably 2.75 to 3.25 wt.~ is employed in the alloys of 38 the present invention.
~g~ 5 Niobium (`l~b), when present in the alloys of 2 the present invention, will form fine niobium carbide 3 precipitates on dislocations in the alloy structure 4 and contributes to the strength of the alloy. Niobium levels of about 1 to 2 wt.% are suitable for use herein, 6 preferred is a niobium content of about 1.25 to 1.75 7 wt.%.
a Nickel constitutes the balance of the alloys
9 with residual impurities at as low a concentration as possible.
11 The following examples serve to describe, 12 more fully, the present invention. It is understood 13 that these examples in no way serve to limit the true 14 scope of this invention, but rather, are presented for illustrative purposes.
16 _omparative Example A
17 A coupon measur ing 2 cm x 1 cm x 5 mm was 18 taken from a cast tube comprised of 0.55 wt.96 C, 2.31 wt.%
19 5i, 1.21 wt.% Mn, 29.75 wt.% Cr, 28.70 wt.~ Ni, balance Fe. The coupon was pack carburized, that is, placed in a 21 carbon bed having access to air, at 1100C for 72 hours.
22 The coupon was then nickel-plated, cross-sectioned, 23 polished, and examined under a scanning electron micro-24 scope. It was observed that carburization occurred throughout the coupon.
26 Example 1 27 A coupon havin~ the same dimensions as that of 28 the above Comparative Example was taken from a cast tube 29 comprised of 23.û wt.% Cr, 12.2 wt.~ Fe, 4.8 wt.% Al, 1.23 wt.g Hf, 2.85 wt.~ W, 1.68 wt.% Nb, 0.48 wt.% Y, 31 0.2 wt.~6 C, and the balance Ni. The coupon was pack 32 carburized at ]100C for 72 hours. The coupon was then 33 prepared and analyzed as in the above Comparative Example 3~ and it was found that a protective A12o3 scale had formed which enabled the coupon to resist carburization.
36 Exan~
37 A COUpOIl of the alloy of Example 1 above was 38 oxidized in air at 1100C for 100 hours. The coupon was 3~i8~5 1 then analyzed and it was found that a protective layer of 2 A12O3 had formed on its surface, and that some internal 3 A12O3 stringes were also present. At the chromium and 4 aluminum levels claimed herein, the alloys of the present invention are selectively oxidized to form A12O3 scales 6 which resist further oxidation - thus evidencing the 7 oxidation resistance of the instantly claimed alloys.
8 Example 3 9 The microstructural stability of the alloy of Example 1 above was determined by studying samples of 11 the alloy after one sample was e~posed to air at 1100C
l2 for 1000 hours and another sample was exposed to air at 13 1175C for 100 hours. Both samples were found to be 14 structurally stable, that is, the grain structure and precipitates remained unchanged throughout the experimentO
16 Comparative Examples B and C and Example 4 17 Three alloy samples, shown in Table I below, 18 were prepared and tested for creep strength and ductility 19 at 1000C and 3000 psi for up to about 700 hours~ The results were recorded and are illustrated in Figure 1 21 herein which shows strain-inch~inch versus time in hours.
22 It is evidenced by this Figure 1 that the alloy of the 23 instant invention is superior to the other two alloys 24 which are representative of those alloys conventionally ernployed at elevated temperatures.
27 Comp. Ex. BComp. Ex. C Ex. 4 28 C - 0.11 0.43 0.2 29 Si - 0.88 1.1~ _ 30 Cr - 24.5 24.0 23.8 31 Ni - 38.7 41.8 balance 32 Fe - 33 30.7 12.2 33 Mn - 1.05 1.45 34 ~l 1.47 35 Nb - 1.49 1.68 36 W _ 2.85 37 Y 0.48 38 Hf 1.23 ___ 39 Al _ 4.8 l Samples of the above alloys were first aged 2 before being tested at 1000C and 3000 psi. The alloy 3 corresponding to Comparative B and C were aged at 1000C
4 for 5000 hours whereas the alloy corresyonding to E~ample 5 4 was aged at 1000C or 3000 hours. The results, as 6 illustrated in Figure 2, again demonstrate the superior 7 creep strengt}l and ductility of the instantly claimed 8 alloys.
11 The following examples serve to describe, 12 more fully, the present invention. It is understood 13 that these examples in no way serve to limit the true 14 scope of this invention, but rather, are presented for illustrative purposes.
16 _omparative Example A
17 A coupon measur ing 2 cm x 1 cm x 5 mm was 18 taken from a cast tube comprised of 0.55 wt.96 C, 2.31 wt.%
19 5i, 1.21 wt.% Mn, 29.75 wt.% Cr, 28.70 wt.~ Ni, balance Fe. The coupon was pack carburized, that is, placed in a 21 carbon bed having access to air, at 1100C for 72 hours.
22 The coupon was then nickel-plated, cross-sectioned, 23 polished, and examined under a scanning electron micro-24 scope. It was observed that carburization occurred throughout the coupon.
26 Example 1 27 A coupon havin~ the same dimensions as that of 28 the above Comparative Example was taken from a cast tube 29 comprised of 23.û wt.% Cr, 12.2 wt.~ Fe, 4.8 wt.% Al, 1.23 wt.g Hf, 2.85 wt.~ W, 1.68 wt.% Nb, 0.48 wt.% Y, 31 0.2 wt.~6 C, and the balance Ni. The coupon was pack 32 carburized at ]100C for 72 hours. The coupon was then 33 prepared and analyzed as in the above Comparative Example 3~ and it was found that a protective A12o3 scale had formed which enabled the coupon to resist carburization.
36 Exan~
37 A COUpOIl of the alloy of Example 1 above was 38 oxidized in air at 1100C for 100 hours. The coupon was 3~i8~5 1 then analyzed and it was found that a protective layer of 2 A12O3 had formed on its surface, and that some internal 3 A12O3 stringes were also present. At the chromium and 4 aluminum levels claimed herein, the alloys of the present invention are selectively oxidized to form A12O3 scales 6 which resist further oxidation - thus evidencing the 7 oxidation resistance of the instantly claimed alloys.
8 Example 3 9 The microstructural stability of the alloy of Example 1 above was determined by studying samples of 11 the alloy after one sample was e~posed to air at 1100C
l2 for 1000 hours and another sample was exposed to air at 13 1175C for 100 hours. Both samples were found to be 14 structurally stable, that is, the grain structure and precipitates remained unchanged throughout the experimentO
16 Comparative Examples B and C and Example 4 17 Three alloy samples, shown in Table I below, 18 were prepared and tested for creep strength and ductility 19 at 1000C and 3000 psi for up to about 700 hours~ The results were recorded and are illustrated in Figure 1 21 herein which shows strain-inch~inch versus time in hours.
22 It is evidenced by this Figure 1 that the alloy of the 23 instant invention is superior to the other two alloys 24 which are representative of those alloys conventionally ernployed at elevated temperatures.
27 Comp. Ex. BComp. Ex. C Ex. 4 28 C - 0.11 0.43 0.2 29 Si - 0.88 1.1~ _ 30 Cr - 24.5 24.0 23.8 31 Ni - 38.7 41.8 balance 32 Fe - 33 30.7 12.2 33 Mn - 1.05 1.45 34 ~l 1.47 35 Nb - 1.49 1.68 36 W _ 2.85 37 Y 0.48 38 Hf 1.23 ___ 39 Al _ 4.8 l Samples of the above alloys were first aged 2 before being tested at 1000C and 3000 psi. The alloy 3 corresponding to Comparative B and C were aged at 1000C
4 for 5000 hours whereas the alloy corresyonding to E~ample 5 4 was aged at 1000C or 3000 hours. The results, as 6 illustrated in Figure 2, again demonstrate the superior 7 creep strengt}l and ductility of the instantly claimed 8 alloys.
Claims (10)
PROPERTY OR PRIVILEGE IS CLAIMED ARE DEFINED AS FOLLOWS:
1. Heat resisting alumina-forming, nickel-based austenitic alloy having improved oxidation and carburization resistance, improved creep strength and good high temperature ductility and microstructural stability and consisting essentially of the following elements in the following by-weight proportion ranges:
Cr 20-25 %
Fe 10-15 %
Al 3-6 %
Hf 1-2 %
W 1.5-3.25 %
Nb 1-2 %
Y 0.01-1 %
C 0.2-0.3 %
Ni balance
Cr 20-25 %
Fe 10-15 %
Al 3-6 %
Hf 1-2 %
W 1.5-3.25 %
Nb 1-2 %
Y 0.01-1 %
C 0.2-0.3 %
Ni balance
2. The alloy of Claim 1 wherein the chromium content is about 24 to 25 wt. %.
3. The alloy of Claim 1 wherein the iron content is about 12 to 14 wt. %.
4. The alloy of Claim 1 wherein the aluminum content is about 4 to 5 wt. %.
5. The alloy of Claim 1 wherein the hafnium content is about 1.5 to 2 wt. %.
6. The alloy of Claim 1 wherein the tungsten content is about 2.75 to 3.25 wt. %.
7. The alloy of Claim 1 wherein the niobium content is about 1.25 to 1.75 wt. %.
8. The alloy of Claim 1 wherein the yttrium content is about 0.5 to 1 wt. %.
9. The alloy of Claim 1 wherein the carbon content is about 0.3 wt. %.
10. Heat resisting alumina-forming, nickel-based austenitic alloy having improved oxidation and carburi-zation resistance, improved creep strength,and good high temperature ductility and microstructural stability and consisting essentially of the following elements in the following by-weight proportion ranges:
Cr 24-25 %
Fe 12-14 %
Al 4-5 %
Hf 1.5-2 %
W 2.75-3.25 %
Nb 1.25-1,75 %
y 0.5-1 %
C 0.3 %
Ni balance
Cr 24-25 %
Fe 12-14 %
Al 4-5 %
Hf 1.5-2 %
W 2.75-3.25 %
Nb 1.25-1,75 %
y 0.5-1 %
C 0.3 %
Ni balance
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US29859181A | 1981-09-02 | 1981-09-02 | |
| US298,591 | 1989-01-17 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1196805A true CA1196805A (en) | 1985-11-19 |
Family
ID=23151177
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000410627A Expired CA1196805A (en) | 1981-09-02 | 1982-09-01 | Alumina-forming nickel-based austenitic alloys |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP0073685B1 (en) |
| JP (1) | JPS5873739A (en) |
| AU (1) | AU547863B2 (en) |
| CA (1) | CA1196805A (en) |
| DE (1) | DE3268674D1 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DK166219C (en) * | 1991-01-23 | 1993-08-16 | Man B & W Diesel Gmbh | VALVE WITH HAIR PILOT |
| DE102008051014A1 (en) * | 2008-10-13 | 2010-04-22 | Schmidt + Clemens Gmbh + Co. Kg | Nickel-chromium alloy |
| JP5920047B2 (en) * | 2012-06-20 | 2016-05-18 | 新日鐵住金株式会社 | Austenitic heat-resistant material |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE734745C (en) * | 1938-04-15 | 1943-04-29 | Heraeus Vacuumschmelze Ag | Use of nickel-chromium-iron alloys for objects with the highest heat resistance |
| FR1251688A (en) * | 1960-03-18 | 1961-01-20 | Thomson Houston Comp Francaise | Refractory alloys |
| GB1190047A (en) * | 1967-08-18 | 1970-04-29 | Int Nickel Ltd | Nickel-Chromium-Iron Alloys |
| GB1512984A (en) * | 1974-06-17 | 1978-06-01 | Cabot Corp | Oxidation resistant nickel alloys and method of making the same |
| US3976436A (en) * | 1975-02-13 | 1976-08-24 | General Electric Company | Metal of improved environmental resistance |
| US4077801A (en) * | 1977-05-04 | 1978-03-07 | Abex Corporation | Iron-chromium-nickel heat resistant castings |
-
1982
- 1982-09-01 AU AU87890/82A patent/AU547863B2/en not_active Expired
- 1982-09-01 CA CA000410627A patent/CA1196805A/en not_active Expired
- 1982-09-02 DE DE8282304610T patent/DE3268674D1/en not_active Expired
- 1982-09-02 EP EP19820304610 patent/EP0073685B1/en not_active Expired
- 1982-09-02 JP JP15335182A patent/JPS5873739A/en active Pending
Also Published As
| Publication number | Publication date |
|---|---|
| AU8789082A (en) | 1983-03-10 |
| EP0073685B1 (en) | 1986-01-22 |
| EP0073685A1 (en) | 1983-03-09 |
| JPS5873739A (en) | 1983-05-04 |
| DE3268674D1 (en) | 1986-03-06 |
| AU547863B2 (en) | 1985-11-07 |
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