GB2417729A - Nickel-chromium-cobalt based alloy - Google Patents
Nickel-chromium-cobalt based alloy Download PDFInfo
- Publication number
- GB2417729A GB2417729A GB0517657A GB0517657A GB2417729A GB 2417729 A GB2417729 A GB 2417729A GB 0517657 A GB0517657 A GB 0517657A GB 0517657 A GB0517657 A GB 0517657A GB 2417729 A GB2417729 A GB 2417729A
- Authority
- GB
- United Kingdom
- Prior art keywords
- alloy
- nickel
- chromium
- based alloy
- cobalt based
- 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.)
- Granted
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
-
- 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%
-
- 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
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
- Powder Metallurgy (AREA)
- Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
- Hydrogen, Water And Hydrids (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Coating By Spraying Or Casting (AREA)
- Catalysts (AREA)
Abstract
A nickel-chromium-cobalt based alloy has a composition comprising (by weight): 17-22 % chromium, 8-15 % cobalt, 4.0-9.5 % molybdenum, 1.28-1.65 % aluminium, 1.50-2.30% titanium, 0.01-0.2 % carbon, up to 7.0 % tungsten, up to 0.80 % niobium, up to 0.015 % boron, up to 3 % iron, up to 1.5 tantalum, up to 1.5 % manganese, up to 0.5 % silicon, up to 0.5 % copper, up to 0.5 % each of magnesium, calcium, hafnium, zirconium, yttrium, cerium and lanthanum, with the balance being nickel and impurities. The sum of A1 + 0.56Ti + 0.29Nb lies between 2.2-2.9 and the sum of Mo + 0.52W lies between 6.5-9.5. The alloy may be used in wrought, cast, spray-formed of powder form and used to make components for gas turbine engines.
Description
24 1 7729
TITLE
Ni-Cr-Co ALLOY FOR ADVANCED GAS TURBINE ENGINES
FIELD OF THE INVENTION
This invention relates to wroughtable high strength alloys for use at elevated temperatures. In particular, it is related to alloys which possess sufficient creep strength, thermal stability, and resistance to strain age cracking to allow for fabrication and service in gas turbine transition ducts and other gas turbine components.
BACKGROUND OF THE INVENTION
To meet the demand for increased operating efficiency, gas turbine engine designers would like to employ higher and higher operating temperatures. However, the ability to increase operating temperatures is often limited by material properties. One application with such a limitation is gas turbine transition ducts. Transition ducts are often welded components made of sheet or thin plate material and thus need to be weldable as well as wroughtable. Often gamma- prime strengthened alloys are used in transition ducts due to their high- strength at elevated temperatures. However, current commercially available wrought gamma-prime strengthened alloys either do not have the strength or stability to be used at the very high temperatures demanded by advanced gas turbine design concepts, or can present difficulties during fabrication. Ln particular, one such fabrication difficulty is the susceptibility of many wrought gamma-prime strengthened alloys to strain age cracking. The problem of strain age cracking will be described in more detail later in this document.
Wrought gamma-prime strengthened alloys are often based on the nickelchromium- cobalt system, although other base systems are also used. These alloys will typically have aluminum and titanium additions which are responsible for the formation of the gamma-prime phase, Ni3(Al,Ti). Other gamma-prime forming elements, such as niobium and/or tantalum, can also be employed. An age-hardening heat treatment is used to develop the gamma-prime phase into the alloy microstructure. This heat treatment is normally given to the alloy when it is in the annealed condition. The presence of gamma- prime phase leads to a considerable strengthening of the alloy over a broad temperature range. Other elemental additions may include molybdenum or tungsten for solid solution strengthening, carbon for carbide formation, and boron for improved high temperature ductility.
Strain age cracking is a problem which limits the weldability of many gamma-prime strengthened alloys. This phenomenon typically occurs when a welded part is subjected to a high temperature for the first time after the welding operation. Often this is during the post-weld annealing treatment given to most welded gamma-prime alloy fabrications. The cracking occurs as a result of the formation of the gamma-prime phase during the heat up to the annealing temperature. The formation of the strengthening gamma-prime phase in conjunction with the low ductility many of these alloys possess at intermediate temperatures, as well as the mechanical restraint typically imposed by the welding operation will often lead to cracking. The problem of strain age cracking can limit alloys to be used up to only a certain thickness since greater material thickness leads to greater mechanical restraint.
Several types of tests to evaluate the susceptibility of an alloy to strain age cracking have been developed. These include the circular patch test, the restrained plate test, and various dynamic thermal-mechanical tests. One test which can be used to evaluate the susceptibility of an alloy to strain age cracking is the controlled heating rate tensile (CHRT) test developed in the 1 960's. Recent testing at Haynes International has found the CHRT test to successfully rank the susceptibility of several commercial alloys in an order consistent with field experience. In the CHRT test, a sheet tensile sample is heated from a low temperature up to the test temperature at a constant rate (a rate of 25 F to 30 F per minute was used in the tests run at Haynes International). Once reaching the test temperature the sample is pulled to fracture at a constant engineering strain rate. The test sample starts in me annealed (not age-hardened) condition, so that the gamma-prime phase is precipitating during the heatup stage as would be the case in a welded component being subjected to a post-weld heat treatment. The percent elongation to fracture in the test sample is taken as a measure of susceptibility to strain age cracking (lower elongation values suggesting greater susceptibility to strain age cracking). The elongation in the CHRT is a function of test temperature and normally will exhibit a minimum at a particular temperature. The temperature at which this occurs is around 1500 F for many wrought garnmaprime strengthened alloys.
Good strength and thermal stability at the high temperatures demanded by advanced gas turbine concepts are two properties lacking in many current commercially available wrought gamma-prime strengthened alloys. High temperature strength has long been evaluated with the use of creeprupture tests, where samples are isothermally subjected to a constant load until the sample fractures. The time to fracture, or rupture life, is then used as a measure of the alloy strength at that temperature. Thermal stability is a measure of whether the alloy microstructure remains relatively unaffected during a thermal exposure. Many high- temperature alloys can form brittle intermetallic or carbide phases during thermal exposure. The presence of these phases can dramatically reduce the room-temperature ductility of the material. This loss of ductility can be effectively measured using a standard tensile test.
Many wrought gamma-prime strengthened alloys are available in sheet form today in today's marketplace. The Rene-41 or R-41 alloy (U.S. Patent No. 2,945,758) was developed by General Electric in the 1950's for use in turbine engines. It has excellent creep strength, but is limited by poor thermal stability and resistance to strain age cracking. A similar General Electric alloy, M-252 alloy (U.S. Patent No. 2,747,993), was also developed in the 1950's. Although currently available only in bar form, the composition would easily lend itself to sheet manufacture. The M-252 alloy has good creep strength and resistance to strain age cracking, but like R-41 alloy is limited by poor thermal stability. The Pratt & Whitney developed alloy known commercially as WASPALOY alloy (apparently having no U.S. patent coverage) is another gamma-prime strengthened alloy intended for use in turbine engines and available in sheet form.
However, this alloy has marginal creep strength above 1500 F, marginal thermal stability, and has fairly poor resistance to strain age cracking. The alloy commercially known as 263 alloy (U.S. Patent 3,222,165) was developed in the late 1950's and introduced in 1960 by Rolls-Royce Limited. This alloy has excellent thermal stability and resistance to strain age cracking, but has very poor creep strength at temperatures greater than 1500 F. The PK-33 alloy (U.S. Patent No. 3,248,213) was developed by the International Nickel Company and introduced in 1961. This alloy has good thermal stability and creep strength, but is limited by a poor resistance to strain age cracking. As suggested by these examples, no currently commercially available alloys are available which possess the unique combination of three key properties: good creep strength and good themmal stability in the l 600 to 1 700 F temperature range as well as good resistance to strain age cracking.
SUMMARY OF THE INVENTION
The principal objective of this invention is to provide new wrought agehardenable nickel-chromium-cobalt based alloys which are suitable for use in high temperature gas turbine transition ducts and other gas turbine components possessing a combination of three specific key properties, namely resistance to strain age cracking, good thermal stability, and good creep- rupture strength.
It has been found that this objective can be reached with an alloy containing a certain range of chromium and cobalt, a certain range of molybdenum and possibly tungsten, and a certain range of aluminum, titanium and possibly niobium, with a balance of nickel and various minor elements and impurities.
Specifically, the preferred ranges are 17 to 22 wt.% chromium, 8 to 15 wt. % cobalt, 4.0 to 9.5 wt.% molybdenum, up to 7.0 wt.% tungsten, 1.28 to 1. 65 wt.% aluminum, 1.50 to 2.30 wt.% titanium, up to 0.80 wt.% niobium, up to 3 wt.% iron, 0.01 to 0.2 wt.% carbon, and up to 0.015 wt.% boron, with a balance of nickel and impurities. s
DESCRIPTION OF THE FIGURES
Figure 1 is a graph of the ductility of the studied wrought agehardenable nickel- chromium-cobalt based alloys in a controlled heating rate tensile test at 1 500 F.
Figure 2 is a graph of the ductility of the studied wrought agehardenable nickel- chromium-cobalt based alloys in a standard tensile test at room temperature.
DESCRIPTION OF THE PREFERRED EMBODIMENT
The wrought age-hardenable nickel-chromium-cobalt based alloys described here have sufficient creep strength, thermal stability, and resistance to strain age cracking to allow for service in sheet or plate form in gas turbine transition ducts as well as in other product forms and other demanding gas turbine applications. This combination of critical properties is achieved through control of several critical elements each with certain functions. The presence of gamma- prime forming elements such as aluminum, titanium, and niobium contribute significantly to the high creep-rupture strength through the formation of the gamma-prime phase during the age- hardening process. However, the combined amount of aluminum, titanium, and niobium must be carefully controlled to allow for good resistance to strain age cracking. Molybdenum and possibly tungsten are added to provide additional creep-rupture strength through solid solution strengthening. Again, however, the total combined molybdenum and tungsten concentration must be carefully controlled, in this case to ensure sufficient thermal stability of the alloy.
Based on the projected requirements for the next generation of gas turbine transition ducts, gamma-prime strengthened alloys have significant potential. Three of the more critical properties are creep strength, weldability (i.e. strain age cracking resistance), and thermal stability. However, producing a gamma-prime strengthened alloy which excels in all three of these properties is not straightforward and no commercially available alloy was found which possessed all three properties to a sufficient degree.
I tested 26 experimental and 5 commercial alloys whose compositions are set forth in Table 1. The experimental alloys have been labeled A through Z. The commercial alloys were HAYNES R-41 alloy, HAYNES WASPALOY alloy, HAYNES 263 alloy, M-252 alloy, and NIMONIC PK-33 alloy. The alloys (including both the experimental and the commercial alloys) had a Cr content which ranged from 17.5 to 21.3 wt.%, as well as a cobalt content ranging from 8.3 to 19.6 wt.%. The aluminum content ranged from 0.49 to 1.89 wt.%, the titanium content from 1.53 to 3.12 wt.%, and the niobium content ranged from nil to 0.79 wt.%. The molybdenum content ranged from 3.2 to 10.5 wt. % and the tungsten ranged from nil up to 8.3 wt.%. Intentional minor element additions carbon and boron ranged from 0.034 to 0.163 wt.% and from nil to 0.008 wt.%, respectively. Iron ranged from nil to 3.6 wt.%.
All testing of the alloys was performed on sheet material of 0.047" to 0. 065" thickness.
The experimental alloys were vacuum induction melted, and then electroslag remelted, at a heat size of 50 lb. The ingots so produced were soaked at 2150 F and then forged and rolled with starting temperatures of 2150 F. The sheet thickness after hot rolling was 0.085". The sheets were annealed at 2150 F for 15 minutes and water quenched. The sheets were then cold rolled to 0.060" thickness. The cold rolled sheets were annealed at temperatures between 2050 and 2175 F as necessary to produce a fully recrystallized, equiaxed grain structure with an ASTM grain size between 4 and 5. Finally, the sheet material was given an age-hardening heat treatment of 1475 F for 8 hours to produce the gamma-prime phase. The commercial alloys HAYNES R-41 alloy, HAYNES WASPALOY alloy, HAYNES 263 alloy, and NIMONIC PK- 33 alloy were obtained in sheet form in the mill annealed condition. Since no commercially available M-252 alloy sheet could be found, a 50 lb. heat was produced for evaluation using the same method as described above for the experimental alloys. All five of the commercial alloys were given post-anneal age-hardening heat treatments according accepted standards. These heat treatments are reported in Table 2.
To evaluate the three properties identified above as important (strain age cracking resistance, thermal stability, and creep strength) three different tests were employed on each of the alloys. The first test was the controlled heating rate tensile test (CHRT). The results of the CHRT testing are given in Table 3. The critical property in this test is the tensile ductility, as measured by a measurement of the elongation to failure. Alloys with a greater ductility in this test are expected to have greater resistance to strain age cracking. The objective of the present study was to have a ductility of 4.5% or greater. Of the experimental alloys, only alloy W failed to meet this requirement. For the commercial alloys, M-252 alloy and 263 alloy met the requirement, while PK-33 alloy, WASPALOY alloy, and R-41 alloy did not. It was found that the performance of a given alloy in the CHRT test could be correlated to the amount of the gamma-prime forming elements in the alloy using the following equation (where the elemental compositions are in wt. %): Al + 0.56Ti + 0.29Nb < 2.9 (1) The values of the left hand side of Eq. ( I) for all of the alloys in this study are given in Table 1. All ofthe alloys which passed the CHRT test were found to obey Eq. (1). Furthermore, all of the alloys which did not obey Eq. (1) did not pass the CHRT test requirement, that is, they were found to have a 1 500 F CHRT ductility less than 4.5%. This relationship is shown more clearly in Fig. 1, where the 1 500 F CHRT ductility is plotted against the value of the left hand side of Eq. (1) for all of the alloys in the study. All testing was performed on samples in the annealed condition. The tensile ductility (measured as the percent elongation to failure) is plotted as a function of the compositional variable Al + 0.56Ti + 0.29Nb (where the elemental compositions are in wt.%). A line is drawn on the figure corresponding to a tensile ductility of 4.5%. All alloys plotted above this line (symbol: filled circles) were considered to have passed the controlled heating rate tensile test, while alloys plotted below the line (symbol: x-marks) were considered to have failed. A dashed vertical line is drawn at a value of 2.9 wt.% for the compositional variable, Al + 0.56Ti + 0.29Nb. All alloys with a value greater than 2.9 were found to fail the controlled heating rate tensile test.
TABLE 1
l Alloy Ni W 1 Mo I 1 i: Nb C | B Fe Mo+0.52W Al+0.56Ti+O.'GCb I I A BAL 19 1 7 0 5 5 1 1 1 < 0 05 1 0 079 0 003 <of -- I 2 60 1 I B BAL 195 109 54 43 1 207 1 151 1 002 1 0097 0006 <01 71 | 268 1 I C I BAL 19 2 - 6 3 1 5 1 1 2 20 | 1 60 1 < 0 05 1 0 095 | 0.006 <0 1 8 4 | 2. 84 1 I D BAL 19 0 iO7 5 9 6 3 1 1 1 0.63 j 0 090 1 0 005 <0 1 9.3 1 2 71 1 I E 1 BAL 192 6 8 1 5 3 1 1 59 1 1 0 79 1 0085 1 0.003 <0 1 8 8 1 2 63 1 F BAL 19 4 10 9 5 9 1 4 5 1 1 1 47 1 <0 05 1 0 086 | 0 005 <0 1 7 6 1 2 62 1 I G BAL 10 7 6 3 5 1 1 1 =;1 <0 05 1 1 0 002 <0 1 8 4 | 2 54 1 I H BAL 19 3 4.6 1 1 85 1 1 < 005 1 0088 1 0003 0 2 7 8 1 2 67 BAL 193 107 61 4: 189 1 129 1 <0.05 j 0075 | 0004 02 i -- I 235 1 I BAL 19 2 1 _ _ 4 6 1 1 1 <0 05 | 0.074 | 0 003 0 2 7 8 2 58 1 K BAL 192 107 62 51 207 1 1 0.080 1 0003 02 80 1 277 1 I L BAL 19 2 10 86 0 1 1 2 08 1 1 48 1 0.02 1 0 088 1 0 005 <0 1 7 9 1 2 65 1 I M BAL 19 3 10 76 1 4 6 1 1 1 <0 05 1 1 0.003 2 6 7 8 1 2 50 1 I N BAL - 6 0 1 1 1 <0 05 1 1 0 004 0.2 7.8 1 2 65 1 O BAL 17.5 142 61 1 1 1 147 1 <0. 05 0077 1 0004 0.2 79 1 266 1 I BAL 10 7 6 2 1 4 6 1 1 <0 05 1 0 034 1 0 006 0 2 7 8 | 2 64 I Q BAL 19 2 1 10 7 _ 1 1 <0 05 1 0 056 1 0.006 0 2 7 6 1 2 68 I R BAL 19 9 10 1 <0 1 7 2 1 2 05 1 1 50 | < 0 05 0 058 1 0 006 0.7 7 2 1 2 65 1 I 8 BAL 20 2 1 9 6 _ 2 12 1 1 <0 05 1 0 062 1 0 007 0 7 8 3 1 2 6i 1 1 T BAL 18 9 lOi <0.1 9 3 1 2 07 1 1 < 0 05 1 0 066 1 0 006 0 7 9 3 1 2 72 1 I U BAL 187 105 41 L80 1 <005 | 1 0002 0.1 106 1 244 1 i V BAL 1 10 9 0 1 9 91 2 21 | 1 33 1 0 65 1 0 094 j 0 004 1 <0 1 9 9 1 2 76 1 W BAL 10 9:1 3-3-<01 7 1 | 2 95 -1 X BAL 103 76 1 =1 1 1 072 0089 <0002 <0.1 99 246 - 1 BAL j 192 106 41 1 32 1 213 1 145 1 <005 1 0080 1 0004 1 02 1 53 1 265 1 I Z BAL 19 2 1 10 8 0 1 1 10 5 1 2 10 1 1 46 1 < 0 05 1 0 077 1 0 004 1 0 2 1 10 5 1 2 64 1 M- 252 BAL 1 189 97 <01 1 100 1 2.30 1 101 1 004 1 0163 1 0005 1 02 1 100 1 231 1 i PK-33 BAL 18 8 13 1 I 7 2 1 1 90 1 1 89 1 --- 1 0048 1 0 003 1 0 7 1 7 2 1 2 95 1 1 263 1 BAL I 20 5 1 19 6 <0I I 5 9 1 2 16 t 0 49 1 <005 1 0 060 1 0 002 1 04 1 5 9 1 1 61 1 i WASP BAL 19 1 13 3 < 01 1 4 3 1 2 92 1 1 45 1 0 05 1 0 080 1 0 008 1 1 0 1 4 3 1 2 97 1 I R-41 BAL]9 1 1 10 9 9 7 1 3 12 1 1 48 1 <0 05 1 0 090 1 0 008 1 3 6 1 9 7 1 3 10
TABLE 2
Alloy I Heat Treatments* l _ Experimental alloys A-Z I 1475 F/8hr./AC R-41 alloy I _ 2050 F/30min. /AC + 1650 F/4hr./AC l WASPALOY alloy 1 1825 F/2hr./AC + 1550 F/4hr./AC + 1400 F/16hr./AC 263 alloy l 1472 F/8hr./AC l M-252 alloy I 1400 F/15hr./AC _ PK-33 alloy I 1562 F/4hr./AC I * All heat treatments performed 1 after an annealing heat treatment.
AC = air cool
TABLE 3 =: 4 6.9
| T 5.0 1 W j 6.7 X I 6 9 Y 51 Z 9 3 R-41 alloy l 2.8 WASPALOY alloy I _ _ 3.5 263 alloy_ _ _ 22.9 1 M-252 alloy I 5.6 PK-33 alloy I 3.6 1 To evaluate the thermal stability of the alloys, their room temperature tensile ductility was determined after a long term thermal exposure. After performing the age-hardening heat treatments given in Table 2, samples from all of the experimental and commercial alloys were given a thermal exposure of 1600 F/1000 hrs. /AC. A room temperature tensile test was performed on the thermally exposed samples and the results are given in Table 4. Ductility greater than 20% was considered acceptable. Using this guideline, the experimental alloys U. V, X, and Z were found to fail along with the commercial alloys M-252 alloy, WASPALOY alloy, and R-41 alloy. It was found that control ofthe elements molybdenum and tungsten was critical to develop a thermally stable alloy. The following relationship was found (where the elemental compositions are in wt.%): Mo + 0.52W < 9.5 (2) The values of the left hand side of Eq. (2) for all of the alloys in this study are given in Table I. All of the alloys which did not obey Eq. (2) were found to not have sufficient thermal stability, that is, their room temperature tensile ductility after a 1000 hour thermal exposure at 1 600 F was found to be less than 20%. One alloy (WASPALOY alloy) was found to satisfy Eq.
(2), but to have poor thermal stability. However, this alloy did not satisfy Eq. (1) and therefore is not suitable for the target application. From this example, it is clear that to ensure thermal stability for this class of alloys, it is necessary to control the amount of aluminum, titanium, and niobium as well as the molybdenum and tungsten. The usefulness of Eq. (2) becomes quite clear when considering Fig. 2, \here the ductility of the thermally exposed samples is plotted against the value of the left hand side of Eq. (2) for all of the alloys in the study. Only alloys which satisfy the relationship Al + 0.56Ti + 0.29Nb < 2.9 (where the elemental compositions are in wt.%) are plotted in the graph. All testing was performed on samples given an age-hardening heat treatment followed by a thermal exposure of 1 600 F for l OOO hours. In the graph, the tensile ductility (measured as the percent elongation to failure) is plotted as a function of the compositional variable Mo + 0. 52W (where the elemental compositions are in wt.%). A line is drawn on the figure corresponding to a tensile ductility of 20%. All alloys plotted above this line (symbol: filled circles) were considered to have passed the thermal stability test, while alloys plotted below the line (symbol: x-marks) were considered to have failed. A dashed vertical line is drawn at a value of 9.5 wt.% for the compositional variable, Mo + 0. 52W. All alloys with a value greater than 9.5 were found to fail the thermal stability test.
TABLE 4
l Alloy Ductility after 1600 FtlOOO hrs./AC (% Elong.) C 28 8 D 22.2 1 | F _ 229.5 H 34.3 K 330.7 O 3323.
I-S - _ _ 33 6_ _ T 29.9 U 1 10.4 1 V 9.2 l W 27.3 1 X 19.0 Y 1 33.6 Z 18. 0 R-41 alloy 2.6 WASPALOY 12.8 263 alloy 40.9 M-252 alloy 10.1_ PK-33 alloy 26.2 1 The third key property for the target application is creep strength. The creep-rupture strength of the alloys was measured at 1700 F with a load of 7 ksi. A rupture life of greater than 300 hours was the established goal. The results for the experimental and commercial alloys are shown in Table 5. All of the experimental alloys were found to pass the goal, with the exception of alloys V, Y. and Z. The commercial alloys all passed with the exception of 263 alloy and WASPALOY alloy. Of the total of five alloys which failed the creep- rupture goal, three of them (alloys V and Z. as well as WASPALOY alloy) did not satisfy one or both of Eqs. (1) and (2) and were thermally unstable. Thermal instability can be a negative influence on creep strength.
The other two alloys which did not meet the creep strength goal (alloy Y and 263 alloy) both had a relatively low total content of the solid solution strengthening elements molybdenum and tungsten. Additionally, the 263 alloy had a low total content of the gamma-prime forming elements aluminum, titanium, and niobium. To ensure adequate levels of both the solid solution strengthening elements and the gamma-prime forming elements, the Eqs. (1) and (2) were modified respectfully as (where the elemental compositions are in wt.%): 2.2 < Al + 0.56Ti + 0.29Nb < 2.9 (3) and 6.5<Mo+0.52W<9.5 (4) Of the 31 total experimental and commercial alloys tested in this study, 20 were found to pass all three key property tests, i.e. the CHRT test, the thermal exposure test, and the creeprupture test. All 20 of the acceptable alloys (experimental alloys A through T) had compositions which satisfied both Eqs. (3) and (4). The 11 alloys which were deemed unacceptable (which included experimental alloys U through Z and all five of the commercial alloys) had compositions which failed to satisfy one or both of Eqs. (3) and (4). From Table I it can be seen that the acceptable alloys contained in weight percent 17.5 to 21.3 chromium, 8.3 to 14.2 cobalt, 4.3 to 9.3 molybdenum, up to 7.0 tungsten, 1.29 to 1.63 aluminum, 1.59 to 2.28 titanium, up to 0.79 niobium, 0.034 to 0.097 carbon, 0.002 to 0.007 boron and up to 2.6 iron. For the reasons explained below, alloys containing these elements within the following ranges and meeting Eqs.
(3) and (4) should provide the desired properties: 17 to 22 chromium, 8 to 15 cobalt, 4.0 to 9.5 molybdenum, up to 7.0 tungsten, 1.28 to 1.65 aluminum, 1.50 to 2.30 titanium, up to 0.80 niobium, 0.01 to 0.2 carbon and up to 0.015 boron with the balance being nickel plus impurities.
The alloy may also contain tantalum, up to 1.5 wt. %, manganese, up to 1. 5 wt. %, silicon, up to 0.5 wt. %, and one or more of magnesium, calcium, haLnium, zirconium, yttrium, cerium and lanthanum. Each of these seven elements may be present up to 0.05 wt. %. The acceptable alloys had a range of values for Al + 0.56 Ti + 0.29 Nb of from 2.35 to 2.84 and a range for Mo +0.52 Woffrom7.1to9.3.
TABLE 5
Alloy Rupture Life (hours) A 1 304 B 560
_
C 1 _ 481 l D 375 E 346 F 522 G 584 H 764 I 410 J 767 K 560 L 522 M 581 N 401 O 403 P 664 Q 419 R 328 S 641 T 506 _ U 384 V 284 W 463 X 339 Y 271 Z 283 R-41 alloy 618 WASPALOY 243 263 alloy 139 M-252 alloy 392 PK-33 alloy 412 The presence of chromium (Cr) in alloys used in high temperature environments provides for necessary oxidation and hot corrosion resistance. In general, the higher the Cr content the better the oxidation resistance, however, too much Cr can lead to thermal instability in the alloy.
For the alloys of this invention, it was found that the chromium level should be between about 17to22wl.%.
Cobalt (Co) is a common element in many wrought gamma-prime strengthened alloys.
Cobalt decreases the solubility of aluminum and titanium in nickel at lower temperatures allowing for a greater gamma-prime content for a given level of aluminum and titanium. It was found that Co levels of about 8 to 15 wt.% are acceptable for the alloys of this invention.
As mentioned previously, aluminum (Al), titanium (Ti), and niobium (Nb) contribute to the creep-strength of the alloys of this invention through the formation of the strengthening gamma-prime phase upon an agehardening heat treatment. The combined total of these elements is limited by Eq. (3) above. In terms of the individual elements, it was found that Al could range from 1.28 to 1.65 wt.%, Ti could range from 1.50 to 2.30 wt.%, and Nb could range from nil to 0.80 wt.%.
As mentioned previously, molybdenum (Mo) and tungsten (W) contribute to the creep- rupture strength of the alloys of this invention through solid solution strengthening. The combined total of these elements is limited by Eq. (4) above. In terms of the individual elements, it was found that Mo could range from about 4.0 to 9.5 wt.%, while W could range from ml to about 7. 0 wt.%.
Carbon (C) is a necessary component and contributes to creep-strength of the alloys of this invention through formation of carbides. Carbides are also necessary for proper grain size control. Carbon should be present in the amount of about 0.01 to 0.2 wt.%.
Iron (Fe) is not required, but typically will be present. The presence of Fe allows economic use of revert materials, most of which contain residual amounts of Fe. An acceptable, Fe-free alloy might be possible using new furnace linings and high purity charge materials. The presented data indicate that levels up to at least about 3 wt.% are acceptable.
Boron (B) is normally added to wrought gamma-prime strengthened alloys in small amounts to improve elevated temperature ductility. Too much boron may lead to weldability problems. The preferred range is up to about 0. 015 wt.%.
Tantalum (Ta) is a gamma-prime forming element in this class of alloys. It is expected that tantalum could be partially substituted for aluminum, titanium, or niobium at levels up to about 1.5 wt.%.
Manganese (Mn) is often added to nickel based alloys to help control problems arising from the presence of sulfur impurities. It is expected that Mn could be added to alloys of this invention to levels of at least 1.5 wt.%.
Silicon (Si) can be present as an impurity and is sometimes intentionally added for increased environmental resistance. It is expected that Si could be added to alloys of this invention to levels of at least 0.5 wt.%.
Copper (Cu) can be present as an impurity originating either from the use of revert materials or during the melting and processing of the alloy itself. It is expected that Cu could be present in amounts up to at least 0.5 wt.%.
The use of magnesium (Mg) and calcium (Ca) is often employed during primary melting of nickel base alloys. It is expected that levels of these elements up to about 0.05 wt.% could be present in alloys of this invention.
Often, small amounts of certain elements are added to nickel based alloys to provide increased environmental resistance. These elements include, but are not necessarily limited to lanthanum (La), cerium (Ce), yttrium (Y), zirconium (Zr), and hafnium (Hf). It is expected that amounts of each of these elements up to about 0.05 wt.% could be present in alloys of this invention. Even though the samples tested were limited to wrought sheet, the alloys
should exhibit comparable properties in other wrought forms (such as plates, bars, tubes, pipes, forgings, and wires) and in cast, sprayformed, or powder metallurgy forms, namely, powder, compacted powder and sintered compacted powder. Consequently, the present invention encompasses all forms of the alloy composition.
The combined properties of good thermal stability, resistance to strain age cracking and good creep rupture strength exhibited by this alloy make it particularly useful for fabrication into gas turbine engine components and particularly useful for transition ducts in these engines. Such components and engines containing these components can be operated at higher temperatures without failure and should have a longer service life than those components and engines currently available.
Although I have disclosed certain preferred embodiments of the alloy, it should be distinctly understood that the present invention is not limited thereto, but may be variously embodied within the scope of the following claims.
Claims (22)
- I claim: 1. A nickel-chromium-cobalt based alloy having a compositioncomprised in weight percent of: 17 to 22 chromium 8 to 15 cobalt 4.0 to 9.S molybdenum up to 7.0 tungsten 1.28 to 1.65 aluminum 1.50 to
- 2.30 titanium up to 0.80 niobium 0.01 to 0.2 carbon up to 0.015 boron with a balance of nickel and impurities, the alloy further satisfying the following compositional relationships defined with elemental quantities being in terms of weight percent: 2.2<AI+0.56Ti+0.29Nb<2.9 6.5 <Mo+0.52W<9.5 2. The nickel-chromium-cobalt based alloy of claim 1, also containing iron up to 3 weight percent.
- 3. The nickel-chromium-cobalt based alloy of claim 1, also containing in weight percent at least one of tantalum, up to 1.5%, manganese, up to 1. 5%, silicon, up to 0.5%, and copper, up to 0.5%.
- 4. The nickel-chromium-cobalt based alloy of claim 1, also containing at least one element selected from the group consisting of magnesium, calcium, hafnium, zirconium, yttrium, cerium, and lanthanum, wherein each said element present comprises up to 0.5 weight percent of the alloy.
- 5. The nickel-chromium-cobalt based alloy of claim 1, wherein the alloy is in wrought form selected from the group consisting of sheets, plates, bars, wires, tubes, pipes, and forgings.
- 6. The nickel-chromium-cobalt based alloy of claim 1, wherein the alloy is in cast form.
- 7. The nickel-chromium-cobalt based alloy of claim 1, wherein the alloy has been spray-formed.
- 8. The nickel-chromium-cobalt based alloy of claim I, wherein the alloy is in powder metallurgy form.
- 9. The nickel-chromium-cobalt based alloy of claim I wherein the alloy is formed as a component for a gas turbine engine.
- 10. A nickel-chromium-cobalt based alloy, suitable for use in gas turbine transition ducts, having a composition comprised in weight percent of: 17.5 to 21.3 chromium 8.3 to 14.2 cobalt 4.3 to 9.3 molybdenum up to 7.0 tungsten 1.29 to 1.63 aluminum 1.59 to 2.28 titanium up to 0.79 niobium 0.034 to 0.097 carbon 0.002 to 0.007 boron up to 2.6 iron with a balance of nickel and impurities, the alloy further satisfying the following compositional relationships defined with elemental quantities being in terms of weight percent: 2.35 < Al + 0.56Ti + 0.29Nb < 2.84 7.1 <Mo+0.52W<9.3
- 11. The nickel-chromium-cobalt based alloy of claim 10, also containing in weight percent at least one of tantalum, up to 1.5%, manganese, up to 1.5%, silicon, up to 0.5%, and copper, up to 0.5%.
- 12. The nickel-chromium-cobalt based alloy of claim 10, also containing up to at least one element selected from the group consisting of magnesium, calcium, hatnium, zirconium, yttrium, cerium, and lanthanum, wherein each said element present comprises up to 0.05 weight percent of the alloy.
- 13. The nickel-chromium-cobalt based alloy of claim 10, wherein the alloy is in wrought forms selected from the group consisting of sheets, plates, bars, wires, tubes, pipes, and forgings.
- 14. The nickel-chromium-cobalt based alloy of claim 10, wherein the alloy is in cast form.
- 15. The nickel-chromium-cobalt based alloy of claim 10, wherein the alloy has been spray-formed.
- 16. The nickel-chromium-cobalt based alloy of claim 10, wherein the alloy is in powder metallurgy form.
- 17. The nickel-chromium-cobalt based alloy of claim 10 wherein the alloy is formed as a component for a gas turbine engine.
- 18. An improved gas turbine engine of the type having a plurality of metal components wherein the improvement comprises at least one of the metal components consisting essentially of: 17 to 22 chromium 8 to 15 cobalt 4.0 to 9.5 molybdenum up to 7.0 tungsten 1.28 to 1.65 aluminum 1.50 to 2.30 titanium up to 0.80 niobium 0.01 to 0.2 carbon up to 0.015 boron with a balance of nickel and impurities, the alloy further satisfying the following compositional relationships defined with elemental quantities being in terms of weight percent: 2.2 < Al + 0.56Ti + 0.29Nb < 2.9 6.5 <Mo+0.52W<9.5
- 19. The improved gas turbine engine wherein the at least one of the metal components is a transition duct.
- 20. The improved gas turbine engine of claim 18 where the at least one of the metal components consists essentially of: 17.5 to
- 21.3 chromium 8.3 to 14.2 cobalt 4.3 to 9.3 molybdenum up to 7.0 tungsten 1.29 to 1.63 aluminium 1.59 to 2.28 titanium up to 0.79 niobium 0.034 to 0.097 carbon 0.002 to 0.007 boron up to 2.6 iron with a balance of nickel impurities, the alloy further satisfying the following compositional relationships defined with elemental quantities being in terms of weight percent: 2.35 < Al + 0.56Ti + 0.29Nb < 2.84 7.1 < Mo + 0.52W < 9.3 21. A nickel-chromium-cobalt based alloy substantially as described herein.
- 22. An improved gas turbine engine of the type having a plurality of metal components substantially as described herein.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US10/934,920 US20060051234A1 (en) | 2004-09-03 | 2004-09-03 | Ni-Cr-Co alloy for advanced gas turbine engines |
Publications (3)
Publication Number | Publication Date |
---|---|
GB0517657D0 GB0517657D0 (en) | 2005-10-05 |
GB2417729A true GB2417729A (en) | 2006-03-08 |
GB2417729B GB2417729B (en) | 2008-01-16 |
Family
ID=35198601
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
GB0517657A Active GB2417729B (en) | 2004-09-03 | 2005-08-31 | Ni-Cr-Co alloy for advanced gas turbine engines |
Country Status (16)
Country | Link |
---|---|
US (1) | US20060051234A1 (en) |
EP (1) | EP1640465B1 (en) |
JP (1) | JP4861651B2 (en) |
KR (1) | KR100788527B1 (en) |
CN (2) | CN102586652B (en) |
AT (1) | ATE447048T1 (en) |
AU (1) | AU2005205736B2 (en) |
CA (1) | CA2517056A1 (en) |
DE (1) | DE602005017338D1 (en) |
DK (1) | DK1640465T3 (en) |
ES (1) | ES2335503T3 (en) |
GB (1) | GB2417729B (en) |
MX (1) | MXPA05009401A (en) |
PL (1) | PL1640465T3 (en) |
RU (1) | RU2377336C2 (en) |
TW (1) | TWI359870B (en) |
Families Citing this family (64)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE528807C2 (en) * | 2004-12-23 | 2007-02-20 | Siemens Ag | Component of a superalloy containing palladium for use in a high temperature environment and use of palladium for resistance to hydrogen embrittlement |
DE502005005347D1 (en) * | 2005-10-24 | 2008-10-23 | Siemens Ag | Filler metal, use of filler metal and method of welding |
EP1835040A1 (en) * | 2006-03-17 | 2007-09-19 | Siemens Aktiengesellschaft | Welding material, use of the welding material and method of welding a structural component |
JP5201708B2 (en) * | 2006-04-14 | 2013-06-05 | 三菱マテリアル株式会社 | Ni-based heat-resistant alloy welding wire |
JP5147037B2 (en) * | 2006-04-14 | 2013-02-20 | 三菱マテリアル株式会社 | Ni-base heat-resistant alloy for gas turbine combustor |
JP4805803B2 (en) * | 2006-12-19 | 2011-11-02 | 株式会社東芝 | Ni-based alloy and turbine rotor |
US8506883B2 (en) * | 2007-12-12 | 2013-08-13 | Haynes International, Inc. | Weldable oxidation resistant nickel-iron-chromium-aluminum alloy |
JP5232492B2 (en) * | 2008-02-13 | 2013-07-10 | 株式会社日本製鋼所 | Ni-base superalloy with excellent segregation |
EP2103700A1 (en) * | 2008-03-14 | 2009-09-23 | Siemens Aktiengesellschaft | Nickel base alloy and use of it, turbine blade or vane and gas turbine |
JP5254693B2 (en) * | 2008-07-30 | 2013-08-07 | 三菱重工業株式会社 | Welding material for Ni-base alloy |
WO2010038826A1 (en) * | 2008-10-02 | 2010-04-08 | 住友金属工業株式会社 | Ni‑BASED HEAT-RESISTANT ALLOY |
JP2010150585A (en) * | 2008-12-24 | 2010-07-08 | Toshiba Corp | Ni-based alloy for casting part of steam turbine excellent in high-temperature strength, castability and weldability, turbine casing of steam turbine, valve casing of steam turbine, nozzle box of steam turbine, and pipe of steam turbine |
JP5127749B2 (en) * | 2009-03-18 | 2013-01-23 | 株式会社東芝 | Ni-base alloy for turbine rotor of steam turbine and turbine rotor of steam turbine using the same |
JP2010249050A (en) * | 2009-04-16 | 2010-11-04 | Toshiba Corp | Steam turbine and steam turbine installation |
FR2949234B1 (en) * | 2009-08-20 | 2011-09-09 | Aubert & Duval Sa | SUPERALLIAGE NICKEL BASE AND PIECES REALIZED IN THIS SUPALLIATION |
JP5550298B2 (en) * | 2009-10-05 | 2014-07-16 | 株式会社東芝 | Ni-based alloy for forged parts of steam turbine, turbine rotor of steam turbine, moving blade of steam turbine, stationary blade of steam turbine, screwed member for steam turbine, and piping for steam turbine |
WO2011071054A1 (en) * | 2009-12-10 | 2011-06-16 | 住友金属工業株式会社 | Austenitic heat-resistant alloy |
JP5572842B2 (en) * | 2010-11-30 | 2014-08-20 | 独立行政法人日本原子力研究開発機構 | Precipitation strengthened Ni-base heat-resistant alloy and method for producing the same |
JP5792500B2 (en) * | 2011-04-11 | 2015-10-14 | 株式会社日本製鋼所 | Ni-base superalloy material and turbine rotor |
ITMI20110830A1 (en) * | 2011-05-12 | 2012-11-13 | Alstom Technology Ltd | VALVE FOR ONE STEAM TURBINE 700 C |
EP2546021A1 (en) * | 2011-07-12 | 2013-01-16 | Siemens Aktiengesellschaft | Nickel-based alloy, use and method |
CN103160709A (en) * | 2011-12-12 | 2013-06-19 | 北京有色金属研究总院 | High-performance alloy wire brush used for brush seal, and preparation method thereof |
JP5919980B2 (en) * | 2012-04-06 | 2016-05-18 | 新日鐵住金株式会社 | Ni-base heat-resistant alloy |
JP2014005528A (en) * | 2012-05-29 | 2014-01-16 | Toshiba Corp | Ni-BASED HEAT-RESISTANT ALLOY AND TURBINE COMPONENT |
JP5981251B2 (en) * | 2012-07-20 | 2016-08-31 | 株式会社東芝 | Ni-based alloy and forged parts for forging |
JP5743161B2 (en) * | 2012-09-24 | 2015-07-01 | 株式会社日本製鋼所 | Covering structure material with excellent Mg corrosion resistance |
KR101476145B1 (en) * | 2012-12-21 | 2014-12-24 | 한국기계연구원 | Ni-Cr-Co base alloys showing an excellent combination of bonding to porcelain and mechanical properties used as a porcelain-fused-to-metal |
JP6012454B2 (en) * | 2012-12-21 | 2016-10-25 | 三菱日立パワーシステムズ株式会社 | Forged member and steam turbine rotor, steam turbine rotor blade, boiler piping, boiler tube and steam turbine bolt using the same |
WO2014126086A1 (en) * | 2013-02-13 | 2014-08-21 | 日立金属株式会社 | Metal powder, tool for hot working and method for manufacturing tool for hot working |
TWI645049B (en) | 2013-03-15 | 2018-12-21 | 美商海尼斯國際公司 | FABRICABLE, HIGH STRENGTH, OXIDATION RESISTANT Ni-Cr-Co-Mo-Al ALLOYS |
US9346101B2 (en) | 2013-03-15 | 2016-05-24 | Kennametal Inc. | Cladded articles and methods of making the same |
US9862029B2 (en) | 2013-03-15 | 2018-01-09 | Kennametal Inc | Methods of making metal matrix composite and alloy articles |
CN104278175B (en) * | 2013-07-12 | 2018-10-02 | 大同特殊钢株式会社 | The Ni base superalloys for capableing of warm and hot forging of having excellent high-temperature strength |
JP6223743B2 (en) * | 2013-08-07 | 2017-11-01 | 株式会社東芝 | Method for producing Ni-based alloy |
DE102014200121A1 (en) | 2014-01-08 | 2015-07-09 | Siemens Aktiengesellschaft | Manganese-containing high-temperature soldering alloy based on cobalt, powder, component and soldering process |
RU2542195C1 (en) * | 2014-02-19 | 2015-02-20 | Открытое акционерное общество Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения" ОАО НПО "ЦНИИТМАШ" | Refractory alloy on nickel base for casting of nozzle vanes with equiaxial structure of gas turbine plants |
RU2542194C1 (en) * | 2014-02-19 | 2015-02-20 | Открытое акционерное общество Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения" ОАО НПО "ЦНИИТМАШ" | Refractory nickel-based alloy for casting gas turbine working blades |
RU2538054C1 (en) * | 2014-02-19 | 2015-01-10 | Открытое акционерное общество Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения" ОАО НПО "ЦНИИТМАШ" | Heat-resistant alloy based on nickel for manufacture of blades of gas-turbine units |
CN103924126B (en) * | 2014-04-24 | 2016-07-13 | 四川六合锻造股份有限公司 | A kind of high-temperature alloy material and preparation method thereof |
RU2570130C1 (en) * | 2014-06-11 | 2015-12-10 | Открытое акционерное общество Научно-производственное объединение "Центральный научно-исследовательский институт технологии машиностроения" ОАО НПО "ЦНИИТМАШ" | Heat-resistant alloy based on nickel for casting of blades of gas-turbine units |
CN104087769B (en) * | 2014-06-25 | 2017-02-15 | 盐城市鑫洋电热材料有限公司 | Method for improving properties of nickel-base electrothermal alloy |
RU2564653C1 (en) * | 2014-08-08 | 2015-10-10 | Общество с ограниченной ответственностью "Научно-производственное объединение "Защитные покрытия" | Nickel-based heat resisting alloy for fabrication and repair of gas-turbine unit blades |
JP5995158B2 (en) * | 2014-09-29 | 2016-09-21 | 日立金属株式会社 | Ni-base superalloys |
CN104862533B (en) * | 2015-04-26 | 2016-08-17 | 北京金恒博远冶金技术发展有限公司 | engine turbine high-temperature alloy material and preparation method thereof |
JP6499546B2 (en) * | 2015-08-12 | 2019-04-10 | 山陽特殊製鋼株式会社 | Ni-based superalloy powder for additive manufacturing |
CN106676331B (en) * | 2016-12-22 | 2018-10-09 | 钢铁研究总院 | A kind of high-elastic nichrome band of high temperature resistant and preparation method thereof |
US11117208B2 (en) | 2017-03-21 | 2021-09-14 | Kennametal Inc. | Imparting wear resistance to superalloy articles |
BR112019021654A2 (en) * | 2017-04-21 | 2020-05-12 | Crs Holdings, Inc. | SUPERCALINATE BASED ON CLEAN-NICKEL HARDENING BY PRECIPITATION AND ITEM MANUFACTURED FROM THE SUPERLIGA ON COBALT-NICKEL BASED BY PRECIPITATION |
EP3707287A2 (en) * | 2017-11-10 | 2020-09-16 | Haynes International, Inc. | HEAT TREATMENTS FOR IMPROVED DUCTILITY OF Ni-Cr-Co-Mo-Ti-Al ALLOYS |
WO2019099719A1 (en) * | 2017-11-16 | 2019-05-23 | Arconic Inc. | Cobalt-chromium-aluminum alloys, and methods for producing the same |
KR102114253B1 (en) * | 2018-02-26 | 2020-05-22 | 한국기계연구원 | Ni based superalloy with high creep strength and manufacturing method thereof |
CN108330335A (en) * | 2018-03-15 | 2018-07-27 | 江苏理工学院 | A kind of high temperature heat-resisting and its manufacturing process |
CN108441705B (en) * | 2018-03-16 | 2020-06-09 | 中国航发北京航空材料研究院 | High-strength nickel-based wrought superalloy and preparation method thereof |
RU2674274C1 (en) * | 2018-03-22 | 2018-12-06 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Heat-resistant nickel-based cast alloy and an article made therefrom |
KR102139177B1 (en) * | 2018-03-28 | 2020-07-30 | 한국기계연구원 | Wrought nickel base superalloys for forging having excellent creep property and method for manufacturing the same |
DE102018208736A1 (en) * | 2018-06-04 | 2019-12-05 | Siemens Aktiengesellschaft | Y, Y 'hardened cobalt-nickel base alloy, powder, component and process |
CN110551920B (en) * | 2019-08-30 | 2020-11-17 | 北京北冶功能材料有限公司 | High-performance easy-processing nickel-based wrought superalloy and preparation method thereof |
CN111636013A (en) * | 2020-06-12 | 2020-09-08 | 江苏银环精密钢管有限公司 | Novel nickel-chromium-cobalt-molybdenum high-temperature alloy seamless tube for power station and manufacturing method |
CN114196854B (en) * | 2020-09-02 | 2022-07-15 | 宝武特种冶金有限公司 | High-strength and difficult-to-deform nickel-based high-temperature alloy and preparation method thereof |
CN112575228B (en) * | 2020-11-12 | 2021-09-03 | 中国联合重型燃气轮机技术有限公司 | Creep-resistant long-life nickel-based deformation superalloy and preparation method and application thereof |
CN113046600A (en) * | 2021-03-15 | 2021-06-29 | 瑞安市石化机械厂 | Incone625 alloy material and application thereof to high-strength slender shaft |
CN114032421B (en) * | 2022-01-07 | 2022-04-08 | 北京钢研高纳科技股份有限公司 | Nickel-based superalloy for additive manufacturing, nickel-based superalloy powder material and product |
CN115505788B (en) * | 2022-09-20 | 2023-06-27 | 北京北冶功能材料有限公司 | Nickel-based superalloy resistant to strain aging cracking and preparation method and application thereof |
CN116676510B (en) * | 2023-05-22 | 2024-04-19 | 烟台大学 | Nickel-cobalt-based casting polycrystalline superalloy material and preparation method thereof |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1029609A (en) * | 1965-04-07 | 1966-05-18 | Rolls Royce | Nickel-chromium-molybdenum-cobalt alloy |
JPH01129942A (en) * | 1987-11-13 | 1989-05-23 | Daido Steel Co Ltd | Ni-based alloy having excellent hot workability |
JPH06172900A (en) * | 1992-12-09 | 1994-06-21 | Hitachi Metals Ltd | Screw material for resin molding |
Family Cites Families (27)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2048167A (en) * | 1936-04-11 | 1936-07-21 | Int Nickel Co | Nickel-chromium-iron-titanium alloys |
US2515185A (en) * | 1943-02-25 | 1950-07-18 | Int Nickel Co | Age hardenable nickel alloy |
US2570193A (en) * | 1946-04-09 | 1951-10-09 | Int Nickel Co | High-temperature alloys and articles |
US2712498A (en) * | 1948-06-01 | 1955-07-05 | Rolls Royce | Nickel chromium alloys having high creep strength at high temperatures |
US2688536A (en) * | 1951-01-27 | 1954-09-07 | Gen Motors Corp | High-temperature creep resistant alloy |
US2747993A (en) * | 1951-12-26 | 1956-05-29 | Gen Electric | High temperature nickel-base alloy |
US2793950A (en) * | 1953-07-03 | 1957-05-28 | Union Carbide & Carbon Corp | Heat-resistant nickel-base sheet alloy |
US2805154A (en) * | 1953-11-02 | 1957-09-03 | Nat Res Corp | Nickel-base alloy |
US2809110A (en) * | 1954-08-05 | 1957-10-08 | Utica Drop Forge & Tool Corp | Alloy for high temperature applications |
US3047381A (en) * | 1958-02-03 | 1962-07-31 | Gen Motors Corp | High temperature heat and creep resistant alloy |
US2945758A (en) * | 1958-02-17 | 1960-07-19 | Gen Electric | Nickel base alloys |
GB880805A (en) * | 1958-11-26 | 1961-10-25 | Rolls Royce | Nickel-chromium-cobalt alloys |
US3065072A (en) * | 1959-04-02 | 1962-11-20 | Int Nickel Co | Alloys with a nickel-chromium base |
GB919709A (en) * | 1960-03-15 | 1963-02-27 | Mond Nickel Co Ltd | Improvements in nickel-chromium-cobalt alloys |
US3094414A (en) * | 1960-03-15 | 1963-06-18 | Int Nickel Co | Nickel-chromium alloy |
US3107167A (en) * | 1961-04-07 | 1963-10-15 | Special Metals Inc | Hot workable nickel base alloy |
DE1213618B (en) * | 1961-11-21 | 1966-03-31 | Int Nickel Ltd | Use of a nickel-chromium-cobalt alloy as a material for easily deformable and weldable sheets |
GB956405A (en) * | 1961-11-21 | 1964-04-29 | Mond Nickel Co Ltd | Improvements relating to nickel-chromium-cobalt alloys |
US3390023A (en) * | 1965-02-04 | 1968-06-25 | North American Rockwell | Method of heat treating age-hardenable alloys |
GB1070099A (en) * | 1965-06-25 | 1967-05-24 | Int Nickel Ltd | Welding high-temperature alloys |
GB1190047A (en) * | 1967-08-18 | 1970-04-29 | Int Nickel Ltd | Nickel-Chromium-Iron Alloys |
JP2778705B2 (en) * | 1988-09-30 | 1998-07-23 | 日立金属株式会社 | Ni-based super heat-resistant alloy and method for producing the same |
KR100336803B1 (en) * | 1994-06-20 | 2002-11-14 | 유나이티드 테크놀로지스 코포레이션 | Polycrystalline Nickel Superalloy with Excellent Oxidation Resistance |
DE69621460T2 (en) * | 1995-12-21 | 2003-02-13 | Teledyne Ind | NICKEL CHROME COBALT ALLOY WITH IMPROVED HIGH TEMPERATURE PROPERTIES |
JPH09268337A (en) * | 1996-04-03 | 1997-10-14 | Hitachi Metals Ltd | Forged high corrosion resistant superalloy alloy |
JP3371423B2 (en) * | 1999-01-28 | 2003-01-27 | 住友電気工業株式会社 | Heat resistant alloy wire |
JP2004190060A (en) * | 2002-12-09 | 2004-07-08 | Hitachi Metals Ltd | Heat-resistant alloy for engine valve |
-
2004
- 2004-09-03 US US10/934,920 patent/US20060051234A1/en not_active Abandoned
-
2005
- 2005-05-26 TW TW094117291A patent/TWI359870B/en active
- 2005-06-08 RU RU2005117714/02A patent/RU2377336C2/en active
- 2005-06-17 CN CN201210057737.8A patent/CN102586652B/en active Active
- 2005-06-17 CN CNA2005100781613A patent/CN1743483A/en active Pending
- 2005-07-15 JP JP2005206381A patent/JP4861651B2/en active Active
- 2005-08-24 CA CA002517056A patent/CA2517056A1/en not_active Abandoned
- 2005-08-30 ES ES05018830T patent/ES2335503T3/en active Active
- 2005-08-30 AT AT05018830T patent/ATE447048T1/en active
- 2005-08-30 PL PL05018830T patent/PL1640465T3/en unknown
- 2005-08-30 DK DK05018830.9T patent/DK1640465T3/en active
- 2005-08-30 EP EP05018830A patent/EP1640465B1/en active Active
- 2005-08-30 DE DE602005017338T patent/DE602005017338D1/en active Active
- 2005-08-31 AU AU2005205736A patent/AU2005205736B2/en active Active
- 2005-08-31 GB GB0517657A patent/GB2417729B/en active Active
- 2005-09-02 MX MXPA05009401A patent/MXPA05009401A/en active IP Right Grant
- 2005-09-02 KR KR1020050081625A patent/KR100788527B1/en active IP Right Grant
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1029609A (en) * | 1965-04-07 | 1966-05-18 | Rolls Royce | Nickel-chromium-molybdenum-cobalt alloy |
JPH01129942A (en) * | 1987-11-13 | 1989-05-23 | Daido Steel Co Ltd | Ni-based alloy having excellent hot workability |
JPH06172900A (en) * | 1992-12-09 | 1994-06-21 | Hitachi Metals Ltd | Screw material for resin molding |
Also Published As
Publication number | Publication date |
---|---|
AU2005205736B2 (en) | 2012-02-23 |
RU2005117714A (en) | 2006-12-20 |
CN102586652A (en) | 2012-07-18 |
CN102586652B (en) | 2016-05-11 |
RU2377336C2 (en) | 2009-12-27 |
KR20060050963A (en) | 2006-05-19 |
TWI359870B (en) | 2012-03-11 |
TW200609359A (en) | 2006-03-16 |
GB2417729B (en) | 2008-01-16 |
GB0517657D0 (en) | 2005-10-05 |
US20060051234A1 (en) | 2006-03-09 |
ES2335503T3 (en) | 2010-03-29 |
JP2006070360A (en) | 2006-03-16 |
CN1743483A (en) | 2006-03-08 |
MXPA05009401A (en) | 2006-03-07 |
AU2005205736A1 (en) | 2006-03-23 |
DK1640465T3 (en) | 2010-03-01 |
EP1640465A2 (en) | 2006-03-29 |
EP1640465B1 (en) | 2009-10-28 |
EP1640465A3 (en) | 2006-04-05 |
PL1640465T3 (en) | 2010-06-30 |
CA2517056A1 (en) | 2006-03-03 |
DE602005017338D1 (en) | 2009-12-10 |
KR100788527B1 (en) | 2007-12-24 |
ATE447048T1 (en) | 2009-11-15 |
JP4861651B2 (en) | 2012-01-25 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP1640465B1 (en) | Ni-Cr-Co-Mo alloy for advanced gas turbine engines | |
US8066938B2 (en) | Ni-Cr-Co alloy for advanced gas turbine engines | |
US10577680B2 (en) | Fabricable, high strength, oxidation resistant Ni—Cr—Co—Mo—Al alloys | |
Pike | Development of a fabricable gamma-prime (γ′) strengthened superalloy | |
US3046108A (en) | Age-hardenable nickel alloy | |
MXPA04010256A (en) | Nickel-base alloy. | |
EP2675931A1 (en) | HIGH TEMPERATURE LOW THERMAL EXPANSION Ni-Mo-Cr ALLOY | |
CA2560147C (en) | Ni-cr-co alloy for advanced gas turbine engines | |
US3005704A (en) | Nickel base alloy for service at high temperatures | |
US11814704B2 (en) | High strength thermally stable nickel-base alloys |