CA2592027A1 - A ni based alloy, a component, a gas turbine arrangement and use of pd in connection with such an alloy - Google Patents
A ni based alloy, a component, a gas turbine arrangement and use of pd in connection with such an alloy Download PDFInfo
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- CA2592027A1 CA2592027A1 CA002592027A CA2592027A CA2592027A1 CA 2592027 A1 CA2592027 A1 CA 2592027A1 CA 002592027 A CA002592027 A CA 002592027A CA 2592027 A CA2592027 A CA 2592027A CA 2592027 A1 CA2592027 A1 CA 2592027A1
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 120
- 239000000956 alloy Substances 0.000 title claims abstract description 120
- 239000007789 gas Substances 0.000 claims abstract description 25
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 25
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims abstract description 24
- 239000001257 hydrogen Substances 0.000 claims abstract description 24
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 229910052719 titanium Inorganic materials 0.000 claims description 7
- 229910052721 tungsten Inorganic materials 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 229910052702 rhenium Inorganic materials 0.000 claims description 6
- 229910052799 carbon Inorganic materials 0.000 claims description 5
- 229910052741 iridium Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052762 osmium Inorganic materials 0.000 claims description 5
- 229910052697 platinum Inorganic materials 0.000 claims description 5
- 229910052703 rhodium Inorganic materials 0.000 claims description 5
- 229910052707 ruthenium Inorganic materials 0.000 claims description 5
- 229910052715 tantalum Inorganic materials 0.000 claims description 5
- 229910052768 actinide Inorganic materials 0.000 claims description 4
- 150000001255 actinides Chemical class 0.000 claims description 4
- 229910052796 boron Inorganic materials 0.000 claims description 4
- 229910052747 lanthanoid Inorganic materials 0.000 claims description 4
- 150000002602 lanthanoids Chemical class 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 229910052706 scandium Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052746 lanthanum Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052727 yttrium Inorganic materials 0.000 claims description 3
- 241001367053 Autographa gamma Species 0.000 claims 1
- 238000005275 alloying Methods 0.000 abstract description 5
- KDLHZDBZIXYQEI-UHFFFAOYSA-N palladium Substances [Pd] KDLHZDBZIXYQEI-UHFFFAOYSA-N 0.000 description 52
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 30
- 239000011651 chromium Substances 0.000 description 20
- 239000010936 titanium Substances 0.000 description 15
- 230000000694 effects Effects 0.000 description 13
- 239000000463 material Substances 0.000 description 9
- 238000005192 partition Methods 0.000 description 8
- 229910000601 superalloy Inorganic materials 0.000 description 8
- 238000005260 corrosion Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 230000003647 oxidation Effects 0.000 description 6
- 238000007254 oxidation reaction Methods 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 239000010410 layer Substances 0.000 description 5
- 230000001681 protective effect Effects 0.000 description 5
- 229910001005 Ni3Al Inorganic materials 0.000 description 4
- 238000002485 combustion reaction Methods 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical class S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- 229910052763 palladium Inorganic materials 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 239000005864 Sulphur Substances 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- DWDWQJHDVOKTDZ-UHFFFAOYSA-N nickel dihydride Chemical class [NiH2] DWDWQJHDVOKTDZ-UHFFFAOYSA-N 0.000 description 1
- 229910000652 nickel hydride Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000011241 protective layer Substances 0.000 description 1
- WUAPFZMCVAUBPE-UHFFFAOYSA-N rhenium atom Chemical compound [Re] WUAPFZMCVAUBPE-UHFFFAOYSA-N 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000000638 solvent extraction Methods 0.000 description 1
- 238000005382 thermal cycling Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 230000003313 weakening effect Effects 0.000 description 1
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
-
- 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%
-
- 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
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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)
- Other Surface Treatments For Metallic Materials (AREA)
- Physical Vapour Deposition (AREA)
- Crystals, And After-Treatments Of Crystals (AREA)
Abstract
The invention concerns a Ni based alloy suitable for single 5 crystalline, directionally solidified or polycrystalline components to be used at high temperatures. The alloy is a '/ alloy and consists of different alloying elements within defined ranges. Among other defined ranges of elements, the alloy contains Pd in a significant amount sufficient to 10 provide the alloy with an improved resistance against hydrogen embrittlement. The invention also concerns a component (13, 15) designed for use as a component (13, 15) in a high temperature environment. Furthermore, the invention concerns a gas turbine arrangement. Moreover, the invention 15 concerns the use of Pd for providing an alloy with improved resistance against hydrogen embrittlement.
Description
A Ni based alloy, a component, a gas turbine arrangement and use of Pd in connection with such an alloy BACKGROUND OF THE INVENTION AND PRIOR ART
The present invention relates to the field of nickel based alloys with excellent properties for use at high temperatures. The alloys according to the invention may for example be used for components in gas turbines. The invention also relates to components made from an alloy according to the invention. Furthermore, the invention relates to a gas turbine arrangement. Moreover, the invention relates to the use of Pd in alloys.
Many different alloys for high temperature applications are known. A group of such alloys are called superalloys. The term "superalloy" is used to represent complex alloys based on e.g. nickel, iron, and cobalt, containing additional elements such as chromium, carbon, aluminium, tungsten, rhenium, titanium, silicon and molybdenum. The term "based"
as used herein means that that element is the largest weight fraction of the alloy, i.e. that there is no other element in the alloy that is present in a weight % that is the same as or higher than the weight % of the base element. The additives are normally used to impart high values of mechanical strength and creep resistance at elevated temperatures and improved oxidation and hot corrosion resistance. For nickel based superalloys, high hot strength is obtained partly by solid solution hardening using such elements as tungsten or molybdenum and partly by precipitation hardening. The precipitates are often produced by adding aluminium and titanium to form the intermetallic compound y' ("gamma prime"), based on Ni3(Ti,Al), within the host material (y).
The document US 6 177 046 B1 describes y/y' superalloys containing Pd. According to this document, Pd is added in order to provide improved weldability to the alloy. The document lists quite wide ranges for the contents of the alloying elements. Concerning Pd, the range 4-32 weight % is specified in the claims. According to the most preferable ranges of the alloying elements according to different examples in this document, the Pd content should be 5-40 weight o(Table 7), 5-45 weight o(Table 8) or 8-27 weight %
(the table in column 17). In the concrete examples in this document, the Pd content is quite high. It is proposed that up to approximately half of the Ni content in existing Ni based superalloys should be substituted by Pd (see column 9).
The document US 6 007 645 describes y/y' Ni based superalloys. The document describes alloys said to have good hot corrosion resistance, a high creep-rupture strength and good microstructural stability. The document stresses that the Cr content should be low. The document suggests several different alloy compositions. The Cr content is never above 2.9 weight %. The document mentions that the alloy, among other alloying elements, can contain 0-10 weight % of one or more of the elements selected from the group consisting of Ru, Rh, Pd, Os, Ir and Pt. It is mentioned that such elements are effective in increasing the creep-rupture strength and oxidation and corrosion resistance. The document does not seem to mention any concrete example where Pd is present in the alloy.
The article "Effect of palladium on the hydrogen embrittlement of B-doped Ni3Al" by Liu Yang and Rex B.
McLellan in the Journal of Materials Research, vol. 11, no.
4, April 1996, pp. 862-864 discusses that hydrogen embrittlement in B-doped Ni3Al can be reduced by the addition of Pd.
It is known that hydrogen may diffuse into alloys and thereby be the cause of disadvantageous properties of the alloy. For example, the hydrogen may reduce the ductility of the material, may be the cause of the occurrence of cracks and may make the material hard but brittle. The most important mechanism for these effects is associated with the weakening of grain and particle boundaries. There may also be a possible disadvantageous synergy effect between H and S such that hydrogen sulphides are formed at the grain and particle boundaries. It is also known that S may tend to segregate preferentially to grain boundaries. Even very low contents of S may be sufficient to form hydrogen sulphide layers at these boundaries. Such problems can also occur by the formation of nickel hydrides in the absence of sulphur. Problems of the described kinds can be referred to as hydrogen embrittlement (HE).
HE can be caused by the presence of hydrogen gas but may also occur under humid conditions. Alloy elements such as Al may oxidise in water such that free hydrogen is formed, see the paper mentioned earlier by Yang&McLellan on gamma prime alloys and the paper "Environmental effects on tensile and low cycle fatigue behaviour of single crystal nickel base superalloys" by Nazmy et al. In Scripta Materialia 48 (2003).
This hydrogen can diffuse into the alloy and cause HE.
Ni based y/y' alloys are known to have excellent properties for use at high temperatures, such as for components in gas turbines. However, HE has been reported also for these alloys, see the paper by Nazmy et al mentioned above.
Ni based y/y' alloys are quite complex alloys. These alloys have a matrix of the y phase, which is Ni with other elements like Cr, Co, Fe, W, Mo and Re in solution. Furthermore, such alloys contain particles of the y' phase, which normally is Ni3Al with other elements like Ti, Ta and Nb in solution.
Furthermore, such alloys may contain other elements, for example in order to strengthen grain boundaries and/or to stabilise a protective oxide layer. It can also be noted that different alloying elements tend to be present in different concentrations in the y and y' phases, i.e. a certain element may tend to be drawn to a certain one of these phases such that a concentration of the element is higher in this phase than in the other phase. It has for example been reported that Al tends to partition favourably to the y' phase. It has also been reported that Pd tends to partition favourably to the y' phase. Furthermore, the partition of an element between the y and y' phases may change in the presence of further elements. It has been noted that the addition of Pd can have as an effect that Al tends to partition more favourably to the y phase.
SUMMARY OF THE INVENTION
Components of Ni based y/y' alloys usually have a protective oxide layer that will prevent hydrogen embrittlement.
However, the inventors of the present invention have noticed that in particular in components that are subject to a variation in temperature, for example between ambient temperature and a high service temperature, and in particular if these components are also exposed to humidity, the microstructure of the oxide scale will change with time such that the protective oxide layer can loose at least part of its protective effect or fail mechanically exposing the parent material. The inventors have found that for such components, hydrogen embrittlement is likely to occur. Since normal air contains a certain amount of humidity, humidity can be a problem in many cases. Furthermore, the inventors have found that hydrogen embrittlement may be a problem in for example gas turbines using "wet process" such as fogging and steam cooling. The hydrogen embrittlement can shorten the time during which such components can be used. Since for example gas turbines are expensive devices, it is important that components in such devices can function during a long time.
An object of the invention is to provide an improved Ni based y/y' alloy suitable to be used for components exposed to high temperatures. A particular object it thereby that the alloy should have improved robustness and be resistant to hydrogen embrittlement. In particular the risk of hydrogen embrittlement should be reduced when components made from the alloy are subjected to thermal cycling with humid conditions 5 under at least parts of the cycle. An object it thereby to provide alloys for such components which can function without failing during a long time. A further object of the invention is to provide a component with advantageous properties, in particular a component that will resist hydrogen embrittlement. Still an object is to provide a gas turbine arrangement including one or more components that have advantageous properties when used at high temperatures.
Another object of the invention is to use Pd in Ni based y/y' alloys in order to achieve an advantageous technical effect.
The first objects above are achieved by a Ni based alloy suitable for single crystalline, directionally solidified or polycrystalline components to be used at high temperatures, the alloy being a y/y' alloy and consisting, in weight %, of:
0.5-25 Cr 0-25 of one or more elements selected from the group consisting of Co, Fe and Mn 1-25 of one or more elements selected from the group consisting of Mo, W, Re and Rh 3-25 of one or more elements selected from the group consisting of Al, Ti, Ta, Nb, and V
0-10 of one or more elements selected from the group consisting of Ru, Os, Ir and Pt < 4.0 Pd 0-3 Hf 0-2 Si 0-2 of one or more elements selected from the group consisting of B, C, N and Zr 0-1 of one or more elements selected from the group consisting of Y, La, Sc, the actinides and Ce and the other lanthanides 0-2 of one or more additional elements selected from the group consisting of all elements except for Ni and except for those referred to above in this table balance Ni wherein the alloy contains Pd in a significant amount sufficient to provide the alloy with an improved resistance against hydrogen embrittlement.
It should be noted that when in this document a content of a group of elements is specified (for example: "of one or more elements selected from the group consisting of...") the content means the total content of all the elements from the group that are present in the alloy. Consequently, in case the alloy contains only one element from the group in question, the specified content is the content of this element.
It should also be noted that in this document, if nothing else is said, the contents of different elements or groups of elements always concern weight %.
It can also be noted that when a range of contents begins with 0, this means that the presence of the element or elements in question is optional.
The inventors of the present invention have thus found that an improved alloy is obtained by selecting the different elements as defined above. It has thereby been found that in particular an improved resistance against hydrogen embrittlement is obtained. It has been found that this improved resistance can be obtained also with very low concentrations of Pd. Since Pd is an expensive material, it is an advantageous aspect of the invention that only small amounts of Pd are needed. The improved resistance against HE
is probably due to the fact that H present at the grain or particle boundaries is drawn into the y' phase by Pd. As is mentioned above, Pd partitions favourably to the y' phase.
The present invention relates to the field of nickel based alloys with excellent properties for use at high temperatures. The alloys according to the invention may for example be used for components in gas turbines. The invention also relates to components made from an alloy according to the invention. Furthermore, the invention relates to a gas turbine arrangement. Moreover, the invention relates to the use of Pd in alloys.
Many different alloys for high temperature applications are known. A group of such alloys are called superalloys. The term "superalloy" is used to represent complex alloys based on e.g. nickel, iron, and cobalt, containing additional elements such as chromium, carbon, aluminium, tungsten, rhenium, titanium, silicon and molybdenum. The term "based"
as used herein means that that element is the largest weight fraction of the alloy, i.e. that there is no other element in the alloy that is present in a weight % that is the same as or higher than the weight % of the base element. The additives are normally used to impart high values of mechanical strength and creep resistance at elevated temperatures and improved oxidation and hot corrosion resistance. For nickel based superalloys, high hot strength is obtained partly by solid solution hardening using such elements as tungsten or molybdenum and partly by precipitation hardening. The precipitates are often produced by adding aluminium and titanium to form the intermetallic compound y' ("gamma prime"), based on Ni3(Ti,Al), within the host material (y).
The document US 6 177 046 B1 describes y/y' superalloys containing Pd. According to this document, Pd is added in order to provide improved weldability to the alloy. The document lists quite wide ranges for the contents of the alloying elements. Concerning Pd, the range 4-32 weight % is specified in the claims. According to the most preferable ranges of the alloying elements according to different examples in this document, the Pd content should be 5-40 weight o(Table 7), 5-45 weight o(Table 8) or 8-27 weight %
(the table in column 17). In the concrete examples in this document, the Pd content is quite high. It is proposed that up to approximately half of the Ni content in existing Ni based superalloys should be substituted by Pd (see column 9).
The document US 6 007 645 describes y/y' Ni based superalloys. The document describes alloys said to have good hot corrosion resistance, a high creep-rupture strength and good microstructural stability. The document stresses that the Cr content should be low. The document suggests several different alloy compositions. The Cr content is never above 2.9 weight %. The document mentions that the alloy, among other alloying elements, can contain 0-10 weight % of one or more of the elements selected from the group consisting of Ru, Rh, Pd, Os, Ir and Pt. It is mentioned that such elements are effective in increasing the creep-rupture strength and oxidation and corrosion resistance. The document does not seem to mention any concrete example where Pd is present in the alloy.
The article "Effect of palladium on the hydrogen embrittlement of B-doped Ni3Al" by Liu Yang and Rex B.
McLellan in the Journal of Materials Research, vol. 11, no.
4, April 1996, pp. 862-864 discusses that hydrogen embrittlement in B-doped Ni3Al can be reduced by the addition of Pd.
It is known that hydrogen may diffuse into alloys and thereby be the cause of disadvantageous properties of the alloy. For example, the hydrogen may reduce the ductility of the material, may be the cause of the occurrence of cracks and may make the material hard but brittle. The most important mechanism for these effects is associated with the weakening of grain and particle boundaries. There may also be a possible disadvantageous synergy effect between H and S such that hydrogen sulphides are formed at the grain and particle boundaries. It is also known that S may tend to segregate preferentially to grain boundaries. Even very low contents of S may be sufficient to form hydrogen sulphide layers at these boundaries. Such problems can also occur by the formation of nickel hydrides in the absence of sulphur. Problems of the described kinds can be referred to as hydrogen embrittlement (HE).
HE can be caused by the presence of hydrogen gas but may also occur under humid conditions. Alloy elements such as Al may oxidise in water such that free hydrogen is formed, see the paper mentioned earlier by Yang&McLellan on gamma prime alloys and the paper "Environmental effects on tensile and low cycle fatigue behaviour of single crystal nickel base superalloys" by Nazmy et al. In Scripta Materialia 48 (2003).
This hydrogen can diffuse into the alloy and cause HE.
Ni based y/y' alloys are known to have excellent properties for use at high temperatures, such as for components in gas turbines. However, HE has been reported also for these alloys, see the paper by Nazmy et al mentioned above.
Ni based y/y' alloys are quite complex alloys. These alloys have a matrix of the y phase, which is Ni with other elements like Cr, Co, Fe, W, Mo and Re in solution. Furthermore, such alloys contain particles of the y' phase, which normally is Ni3Al with other elements like Ti, Ta and Nb in solution.
Furthermore, such alloys may contain other elements, for example in order to strengthen grain boundaries and/or to stabilise a protective oxide layer. It can also be noted that different alloying elements tend to be present in different concentrations in the y and y' phases, i.e. a certain element may tend to be drawn to a certain one of these phases such that a concentration of the element is higher in this phase than in the other phase. It has for example been reported that Al tends to partition favourably to the y' phase. It has also been reported that Pd tends to partition favourably to the y' phase. Furthermore, the partition of an element between the y and y' phases may change in the presence of further elements. It has been noted that the addition of Pd can have as an effect that Al tends to partition more favourably to the y phase.
SUMMARY OF THE INVENTION
Components of Ni based y/y' alloys usually have a protective oxide layer that will prevent hydrogen embrittlement.
However, the inventors of the present invention have noticed that in particular in components that are subject to a variation in temperature, for example between ambient temperature and a high service temperature, and in particular if these components are also exposed to humidity, the microstructure of the oxide scale will change with time such that the protective oxide layer can loose at least part of its protective effect or fail mechanically exposing the parent material. The inventors have found that for such components, hydrogen embrittlement is likely to occur. Since normal air contains a certain amount of humidity, humidity can be a problem in many cases. Furthermore, the inventors have found that hydrogen embrittlement may be a problem in for example gas turbines using "wet process" such as fogging and steam cooling. The hydrogen embrittlement can shorten the time during which such components can be used. Since for example gas turbines are expensive devices, it is important that components in such devices can function during a long time.
An object of the invention is to provide an improved Ni based y/y' alloy suitable to be used for components exposed to high temperatures. A particular object it thereby that the alloy should have improved robustness and be resistant to hydrogen embrittlement. In particular the risk of hydrogen embrittlement should be reduced when components made from the alloy are subjected to thermal cycling with humid conditions 5 under at least parts of the cycle. An object it thereby to provide alloys for such components which can function without failing during a long time. A further object of the invention is to provide a component with advantageous properties, in particular a component that will resist hydrogen embrittlement. Still an object is to provide a gas turbine arrangement including one or more components that have advantageous properties when used at high temperatures.
Another object of the invention is to use Pd in Ni based y/y' alloys in order to achieve an advantageous technical effect.
The first objects above are achieved by a Ni based alloy suitable for single crystalline, directionally solidified or polycrystalline components to be used at high temperatures, the alloy being a y/y' alloy and consisting, in weight %, of:
0.5-25 Cr 0-25 of one or more elements selected from the group consisting of Co, Fe and Mn 1-25 of one or more elements selected from the group consisting of Mo, W, Re and Rh 3-25 of one or more elements selected from the group consisting of Al, Ti, Ta, Nb, and V
0-10 of one or more elements selected from the group consisting of Ru, Os, Ir and Pt < 4.0 Pd 0-3 Hf 0-2 Si 0-2 of one or more elements selected from the group consisting of B, C, N and Zr 0-1 of one or more elements selected from the group consisting of Y, La, Sc, the actinides and Ce and the other lanthanides 0-2 of one or more additional elements selected from the group consisting of all elements except for Ni and except for those referred to above in this table balance Ni wherein the alloy contains Pd in a significant amount sufficient to provide the alloy with an improved resistance against hydrogen embrittlement.
It should be noted that when in this document a content of a group of elements is specified (for example: "of one or more elements selected from the group consisting of...") the content means the total content of all the elements from the group that are present in the alloy. Consequently, in case the alloy contains only one element from the group in question, the specified content is the content of this element.
It should also be noted that in this document, if nothing else is said, the contents of different elements or groups of elements always concern weight %.
It can also be noted that when a range of contents begins with 0, this means that the presence of the element or elements in question is optional.
The inventors of the present invention have thus found that an improved alloy is obtained by selecting the different elements as defined above. It has thereby been found that in particular an improved resistance against hydrogen embrittlement is obtained. It has been found that this improved resistance can be obtained also with very low concentrations of Pd. Since Pd is an expensive material, it is an advantageous aspect of the invention that only small amounts of Pd are needed. The improved resistance against HE
is probably due to the fact that H present at the grain or particle boundaries is drawn into the y' phase by Pd. As is mentioned above, Pd partitions favourably to the y' phase.
Furthermore, the addition of Pd may have further advantageous effects. It has for example been reported that Pd may be advantageous in preventing the formation of TCP
(topologically close packed) areas. Furthermore, since Pd is very similar to Ni, its solubility in Ni is very high.
Moreover, since Pd preferentially partitions to the y' phase, also the solubility in Ni3Al is excellent. As indicated above, it has also been reported that the addition of Pd may change the partitioning factors of Ni based y/y' alloys such that slightly more Al partitions to the y phase. This means, for a given y' content, that it is possible to add slightly more Al to the alloy. This would seem to increase the resistance to oxidation and hot corrosion. Moreover, since it is sufficient to use a small amount of Pd in order to obtain the advantageous effects, no significant negative effect of the addition of Pd has been noted (it has been reported that Pd potentially could cause problems with heat treatment procedures and a reduction in creep strength at high temperatures).
According to an embodiment of the alloy according to the invention, the content of said additional elements < 1.0, or even only at the level of impurities that are normally accepted in alloys for components to be used at high temperatures, such as components used in gas turbines. The properties of the alloy are easier to control if the alloy only contains a small amount (or no amount) of such additional elements.
According to a further embodiment, the content of Pd > 0.05.
The content of Pd can be < 2.0, preferably < 1.0 and even <
0.5. It is an advantageous aspect of the present invention that the effects aimed at can be achieved also with small amounts of Pd. This is particularly important since Pd is an expensive material and since large amounts of Pd possibly could have some negative effects.
(topologically close packed) areas. Furthermore, since Pd is very similar to Ni, its solubility in Ni is very high.
Moreover, since Pd preferentially partitions to the y' phase, also the solubility in Ni3Al is excellent. As indicated above, it has also been reported that the addition of Pd may change the partitioning factors of Ni based y/y' alloys such that slightly more Al partitions to the y phase. This means, for a given y' content, that it is possible to add slightly more Al to the alloy. This would seem to increase the resistance to oxidation and hot corrosion. Moreover, since it is sufficient to use a small amount of Pd in order to obtain the advantageous effects, no significant negative effect of the addition of Pd has been noted (it has been reported that Pd potentially could cause problems with heat treatment procedures and a reduction in creep strength at high temperatures).
According to an embodiment of the alloy according to the invention, the content of said additional elements < 1.0, or even only at the level of impurities that are normally accepted in alloys for components to be used at high temperatures, such as components used in gas turbines. The properties of the alloy are easier to control if the alloy only contains a small amount (or no amount) of such additional elements.
According to a further embodiment, the content of Pd > 0.05.
The content of Pd can be < 2.0, preferably < 1.0 and even <
0.5. It is an advantageous aspect of the present invention that the effects aimed at can be achieved also with small amounts of Pd. This is particularly important since Pd is an expensive material and since large amounts of Pd possibly could have some negative effects.
According to a further embodiment, the content of Cr > 3.0, preferably > 6Ø With a fairly large amount of Cr an excellent corrosion and oxidation resistance is obtained.
However, according to an alternative embodiment, the content of Cr <_ 3Ø According to this alternative embodiment, a low amount of Cr is thus used. This may increase the creep-rupture strength of the alloy. By a careful selection of the other elements, a sufficient corrosion and oxidation resistance can be obtained even if the Cr content is low.
According to an embodiment, the content of one or more elements selected from the group consisting of Co, Fe and Mn > 3Ø The content of Co can for example be > 6Ø Furthermore, the content of Co can be > (the content of Fe + the content of Mn). Co is a material that is known to provide an alloy of this kind with advantageous properties, in particular a sufficient hardness at higher temperatures.
According to still another embodiment, the content of one or more elements selected from the group consisting of Mo, W, Re and Rh > 3Ø The content of W can, according to a preferred embodiment, be > content of Mo. Moreover, (the content of Re + the content of Rh) can be < 1Ø With a sufficient amount of for example W, the strength of the alloy is increased.
Furthermore, the creep resistance is improved.
According to a further embodiment, the content of Al > 1Ø
The content of Al can for example be > 3.0 but < 10Ø The molar fraction of Al in the alloy is preferably larger than the molar fraction of any of the other elements selected from the group consisting of Al, Ti, Ta, Nb, and V. Al, in particular, is an advantageous material for the formation of the y' phase. Furthermore, Al can increase the oxidation and hot corrosion resistance.
However, according to an alternative embodiment, the content of Cr <_ 3Ø According to this alternative embodiment, a low amount of Cr is thus used. This may increase the creep-rupture strength of the alloy. By a careful selection of the other elements, a sufficient corrosion and oxidation resistance can be obtained even if the Cr content is low.
According to an embodiment, the content of one or more elements selected from the group consisting of Co, Fe and Mn > 3Ø The content of Co can for example be > 6Ø Furthermore, the content of Co can be > (the content of Fe + the content of Mn). Co is a material that is known to provide an alloy of this kind with advantageous properties, in particular a sufficient hardness at higher temperatures.
According to still another embodiment, the content of one or more elements selected from the group consisting of Mo, W, Re and Rh > 3Ø The content of W can, according to a preferred embodiment, be > content of Mo. Moreover, (the content of Re + the content of Rh) can be < 1Ø With a sufficient amount of for example W, the strength of the alloy is increased.
Furthermore, the creep resistance is improved.
According to a further embodiment, the content of Al > 1Ø
The content of Al can for example be > 3.0 but < 10Ø The molar fraction of Al in the alloy is preferably larger than the molar fraction of any of the other elements selected from the group consisting of Al, Ti, Ta, Nb, and V. Al, in particular, is an advantageous material for the formation of the y' phase. Furthermore, Al can increase the oxidation and hot corrosion resistance.
According to another embodiment, the content of one or more elements selected from the group consisting of Ru, Os, Ir and Pt > 0.01 but < 5Ø The addition of elements from this group can be used to control the partition of other elements between the two phases y and y'.
The content of Hf can, according to an embodiment, be > 0.05.
According to an embodiment, the content of Si is > 0.02. Hf and/or Si can be used for promoting the formation of a protective oxide layer.
The content of one or more elements selected from the group consisting of B. C, N and Zr can for example be > 0.05 but <
0.8. These elements may be used to increase the strength at the grain boundaries.
The alloy can, according to an embodiment, have a content of one or more elements selected from the group consisting of Y.
La, Sc, the actinides and Ce and the other lanthanides >
0.005. These elements can be used to bind S. which can have as an effect that the risk of the formation of unwanted hydrogen sulphides decreases.
Preferably, the content of Ni > 35, and, more preferred, >
50. The alloy thus preferably contains a quite large amount of the base element Ni.
According to a further embodiment, the volume ratio y'/y >
0 . 4 (40%) or even > 0. 6(60 0) . A quite high fraction of y' is advantageous for providing a high hot strength.
According to another object of the invention, a component designed for use as a component in a high temperature environment is provided in that the component is made from an alloy according to any of the preceding embodiments. Such a component thus has advantageous properties as described above in connection with the embodiments of the alloy. In particular, the component can be used at high temperatures and still have a good resistance against hydrogen embrittlement.
5 According to an embodiment, the component is a component for a gas turbine arrangement. The component can for example be a guide vane or part of a guide vane or a turbine rotor blade or part of a turbine rotor blade. It has been found to be particularly advantageous to use the alloy according to the 10 invention for such components. The components can be used for a very long time without risking being damaged by for example hydrogen embrittlement.
A gas turbine arrangement according to the invention comprises at least one component as defined above. Such a gas turbine arrangement will thus include components with advantageous properties as described above.
A use according to the invention is achieved by using Pd which forms part of the alloy according to any of the above embodiments for providing said alloy, according to any of the above embodiments, with improved resistance against hydrogen embrittlement. The inventors of the present invention have thus found a technical effect achieved by a careful use of Pd in alloys of the above described kind. In particular, it is advantageous that only a small amount of Pd is sufficient for achieving the advantageous effects described above.
BRIEF DESCRIPTION OF THE DRAWING
Fig 1 shows very schematically a turbine arrangement according to the invention with a plurality of components according to the invention.
The content of Hf can, according to an embodiment, be > 0.05.
According to an embodiment, the content of Si is > 0.02. Hf and/or Si can be used for promoting the formation of a protective oxide layer.
The content of one or more elements selected from the group consisting of B. C, N and Zr can for example be > 0.05 but <
0.8. These elements may be used to increase the strength at the grain boundaries.
The alloy can, according to an embodiment, have a content of one or more elements selected from the group consisting of Y.
La, Sc, the actinides and Ce and the other lanthanides >
0.005. These elements can be used to bind S. which can have as an effect that the risk of the formation of unwanted hydrogen sulphides decreases.
Preferably, the content of Ni > 35, and, more preferred, >
50. The alloy thus preferably contains a quite large amount of the base element Ni.
According to a further embodiment, the volume ratio y'/y >
0 . 4 (40%) or even > 0. 6(60 0) . A quite high fraction of y' is advantageous for providing a high hot strength.
According to another object of the invention, a component designed for use as a component in a high temperature environment is provided in that the component is made from an alloy according to any of the preceding embodiments. Such a component thus has advantageous properties as described above in connection with the embodiments of the alloy. In particular, the component can be used at high temperatures and still have a good resistance against hydrogen embrittlement.
5 According to an embodiment, the component is a component for a gas turbine arrangement. The component can for example be a guide vane or part of a guide vane or a turbine rotor blade or part of a turbine rotor blade. It has been found to be particularly advantageous to use the alloy according to the 10 invention for such components. The components can be used for a very long time without risking being damaged by for example hydrogen embrittlement.
A gas turbine arrangement according to the invention comprises at least one component as defined above. Such a gas turbine arrangement will thus include components with advantageous properties as described above.
A use according to the invention is achieved by using Pd which forms part of the alloy according to any of the above embodiments for providing said alloy, according to any of the above embodiments, with improved resistance against hydrogen embrittlement. The inventors of the present invention have thus found a technical effect achieved by a careful use of Pd in alloys of the above described kind. In particular, it is advantageous that only a small amount of Pd is sufficient for achieving the advantageous effects described above.
BRIEF DESCRIPTION OF THE DRAWING
Fig 1 shows very schematically a turbine arrangement according to the invention with a plurality of components according to the invention.
DESCRIPTION OF PREFERRED EMBODIMENTS
Below different examples of the composition of alloys according to the invention are given. The balance is Ni in all the below examples. In addition to Ni and to the elements specified in these examples, the alloys, according to these examples, may contain small amounts of impurities with a concentration which is normally accepted in alloys of these kinds for use for components which are intended for use at high temperatures, for example in gas turbines. Furthermore, all the alloys are Ni based y/y' alloys. The ratio y' /y can for example be 0.4 (40%) or > 0.6 (600). This ratio can for example be 0.5 (500).
The first example is one concrete example with specified amounts of the different elements. Each of the examples 2-10 defines small ranges for the different elements. The alloys according to examples 2-10 can be obtained by slightly changing the composition of known alloys, i.e. in particular by adding a small amount of Pd.
The alloys are suitable for the fabrication of single crystal or polycrystalline articles.
Example 1 12.0 Cr 8.0 Co 2.0 Mo 4.0 W
4.0 Al 2.0 Ti 1.5 Ta 1.5 Nb 0.4 Pd 0.1 Hf 0.1 Si 0.01 B
0.05 C
Example 2 15-17 Cr 8-9 Co 1.5-2.5 Mo 3-4 Al 3-4 Ti 1.5-2.5 Nb 0.1-0.5 Pd 0.05-0.2 C
0.005-0.015 B
0.05-0.015 Zr Example 3 12-14 Cr 8-10 Co 1.5-2.5 Mo 3-4 Al 3.5-5 Ti 3-5 Ta 1.5-2.5 Nb 0.1-0.5 Pd 0.1-0.3 C
0.015-0.025 B
0.005-0.015 Zr Example 4 12-14 Cr 8-10 Co 1.5-2.5 Mo 3-4 Al 3.5-4.5 Ti 3-5 Ta 0.1-0.5 Pd Example 5 7.5-9 Cr 8-11 Co 0.4-0.8 Mo 5-6 Al 0.5-1.5 Ti 2-4 Ta 0.1-0.5 Pd 0.05-0.2 C
0.01-0.02 B
0.005-0.05 Zr 1-2 Hf Example 6 21-25 Cr 18-20 Co 1.5-2.5 Al 3-4 Ti 1-2 Ta 0.5-1.5 Nb 0.1-0.5 Pd 0.1-0.2 C
0.005-0.015 B
0.05-0.15 Zr Example 7 21-25 Cr 18-20 Co 2-3 Al 3-4 Ti 1-2 Ta 0.5-1.5 Nb 0.1-0.5 Pd 0.1-0.2 C
0.005-0.015 B
Below different examples of the composition of alloys according to the invention are given. The balance is Ni in all the below examples. In addition to Ni and to the elements specified in these examples, the alloys, according to these examples, may contain small amounts of impurities with a concentration which is normally accepted in alloys of these kinds for use for components which are intended for use at high temperatures, for example in gas turbines. Furthermore, all the alloys are Ni based y/y' alloys. The ratio y' /y can for example be 0.4 (40%) or > 0.6 (600). This ratio can for example be 0.5 (500).
The first example is one concrete example with specified amounts of the different elements. Each of the examples 2-10 defines small ranges for the different elements. The alloys according to examples 2-10 can be obtained by slightly changing the composition of known alloys, i.e. in particular by adding a small amount of Pd.
The alloys are suitable for the fabrication of single crystal or polycrystalline articles.
Example 1 12.0 Cr 8.0 Co 2.0 Mo 4.0 W
4.0 Al 2.0 Ti 1.5 Ta 1.5 Nb 0.4 Pd 0.1 Hf 0.1 Si 0.01 B
0.05 C
Example 2 15-17 Cr 8-9 Co 1.5-2.5 Mo 3-4 Al 3-4 Ti 1.5-2.5 Nb 0.1-0.5 Pd 0.05-0.2 C
0.005-0.015 B
0.05-0.015 Zr Example 3 12-14 Cr 8-10 Co 1.5-2.5 Mo 3-4 Al 3.5-5 Ti 3-5 Ta 1.5-2.5 Nb 0.1-0.5 Pd 0.1-0.3 C
0.015-0.025 B
0.005-0.015 Zr Example 4 12-14 Cr 8-10 Co 1.5-2.5 Mo 3-4 Al 3.5-4.5 Ti 3-5 Ta 0.1-0.5 Pd Example 5 7.5-9 Cr 8-11 Co 0.4-0.8 Mo 5-6 Al 0.5-1.5 Ti 2-4 Ta 0.1-0.5 Pd 0.05-0.2 C
0.01-0.02 B
0.005-0.05 Zr 1-2 Hf Example 6 21-25 Cr 18-20 Co 1.5-2.5 Al 3-4 Ti 1-2 Ta 0.5-1.5 Nb 0.1-0.5 Pd 0.1-0.2 C
0.005-0.015 B
0.05-0.15 Zr Example 7 21-25 Cr 18-20 Co 2-3 Al 3-4 Ti 1-2 Ta 0.5-1.5 Nb 0.1-0.5 Pd 0.1-0.2 C
0.005-0.015 B
0.05-0.15 Zr 0.5-1.5 Hf Example 8 8-9 Cr 4-6 Co 1-3 Mo 4.5-5.5 Al 1-2 Ti 5-7 Ta 0.1-0.5 Pd 0.05-0.15 Hf 0.05-0.15 Si 0.005-0.015 C
0.005-0.015 B
Example 9 6-7 Cr 9-11 Co 0.4-0.8 Mo 2.5-3.5 Re 5-6 Al 0.5-1.5 Ti 5-7 Ta 0.1-0.5 Pd 0.05-0.15 Hf 0.005-0.015 Y
Example 10 2.2-2.8 Cr 10-14 Co 8-10 w 6-7 Re 1.5-2.5 Ru 5.5-6.5 Al 5-6 Ta 0.1-0.5 Pd 0.05-0.15 Hf 0.05-0.15 Si 5 The alloys according to the invention can be produced in a manner which is known to a person skilled in the art for producing Ni based y/y' superalloys of the prior art. The alloys can be used for producing single crystal, directionally solidified or polycrystalline components in a 10 manner known to the person skilled in the art. The alloy according to the invention can be used for any component, or part of a component, intended for use at high temperatures.
Fig 1 shows very schematically a sectional view of a part of 15 a typical gas turbine arrangement according to the invention.
In the embodiment shown in Fig 1, the gas turbine arrangement has an annular combustion chamber 11. In Fig 1 only a lower part of this combustion chamber 11 is shown. The annular combustion chamber can be arranged around a symmetry axis marked X-X in Fig 1. This symmetry axis X-X can also constitute the axis of rotation of a rotor that forms part of the gas turbine arrangement. The combustion chamber 11 is fixed relative to a stator part 14. The gas turbine arrangement comprises a number of guide vanes 13. In Fig 1, two guide vanes 13 are shown. The guide vanes 13 are fixed relative to the stator 14. The gas turbine arrangement also has a number of turbine rotor blades 15. Two such rotor blades 15 are shown in Fig 1. The rotor blades 15 form part of the rotor that rotates around the axis of rotation X-X.
The gas turbine arrangement can of course comprise other parts which are known to a person skilled in the art. The gas turbine arrangement can for example have one or more compressor stages and also additional turbine stages.
Different components in a gas turbine arrangement can be made from alloys according to the present invention. For example, the guide vanes 13 and/or the turbine rotor blades 15 can be made of alloys according to the present invention. The alloys according to the invention can also be used for parts of components, for example for a protective layer on a guide vane 13, turbine rotor blade 15 or other part of a gas turbine.
The invention also concerns the use of Pd. According to this use, Pd, for example in the amounts according to the above examples, is used in an alloy of the described kind for providing the alloy within improved resistance against hydrogen embrittlement.
The invention is not limited to the described embodiments but may be varied and modified within the scoop of the following claims.
0.005-0.015 B
Example 9 6-7 Cr 9-11 Co 0.4-0.8 Mo 2.5-3.5 Re 5-6 Al 0.5-1.5 Ti 5-7 Ta 0.1-0.5 Pd 0.05-0.15 Hf 0.005-0.015 Y
Example 10 2.2-2.8 Cr 10-14 Co 8-10 w 6-7 Re 1.5-2.5 Ru 5.5-6.5 Al 5-6 Ta 0.1-0.5 Pd 0.05-0.15 Hf 0.05-0.15 Si 5 The alloys according to the invention can be produced in a manner which is known to a person skilled in the art for producing Ni based y/y' superalloys of the prior art. The alloys can be used for producing single crystal, directionally solidified or polycrystalline components in a 10 manner known to the person skilled in the art. The alloy according to the invention can be used for any component, or part of a component, intended for use at high temperatures.
Fig 1 shows very schematically a sectional view of a part of 15 a typical gas turbine arrangement according to the invention.
In the embodiment shown in Fig 1, the gas turbine arrangement has an annular combustion chamber 11. In Fig 1 only a lower part of this combustion chamber 11 is shown. The annular combustion chamber can be arranged around a symmetry axis marked X-X in Fig 1. This symmetry axis X-X can also constitute the axis of rotation of a rotor that forms part of the gas turbine arrangement. The combustion chamber 11 is fixed relative to a stator part 14. The gas turbine arrangement comprises a number of guide vanes 13. In Fig 1, two guide vanes 13 are shown. The guide vanes 13 are fixed relative to the stator 14. The gas turbine arrangement also has a number of turbine rotor blades 15. Two such rotor blades 15 are shown in Fig 1. The rotor blades 15 form part of the rotor that rotates around the axis of rotation X-X.
The gas turbine arrangement can of course comprise other parts which are known to a person skilled in the art. The gas turbine arrangement can for example have one or more compressor stages and also additional turbine stages.
Different components in a gas turbine arrangement can be made from alloys according to the present invention. For example, the guide vanes 13 and/or the turbine rotor blades 15 can be made of alloys according to the present invention. The alloys according to the invention can also be used for parts of components, for example for a protective layer on a guide vane 13, turbine rotor blade 15 or other part of a gas turbine.
The invention also concerns the use of Pd. According to this use, Pd, for example in the amounts according to the above examples, is used in an alloy of the described kind for providing the alloy within improved resistance against hydrogen embrittlement.
The invention is not limited to the described embodiments but may be varied and modified within the scoop of the following claims.
Claims (32)
1. A Ni based alloy suitable for single crystalline, directionally solidified or polycrystalline components to be used at high temperatures, the alloy being a .gamma./.gamma.' alloy and consisting, in weight %, of:
0.5-25 ~Cr 0-25 ~~of one or more elements selected from the group consisting of Co, Fe and Mn 1-25 ~~of one or more elements selected from the group consisting of Mo, W, Re and Rh 3-25 ~~of one or more elements selected from the group consisting of Al, Ti, Ta, Nb, and V
0-10 ~~of one or more elements selected from the group consisting of Ru, Os, Ir and Pt < 4.0 ~Pd 0-3 ~~Hf 0-2 ~~Si 0-2 ~~of one or more elements selected from the group consisting of B, C, N and Zr 0-1 ~~of one or more elements selected from the group consisting of Y, La, Sc, the actinides and Ce and the other lanthanides 0-2 ~~of one or more additional elements selected from the group consisting of all elements except for Ni and except for those referred to above in this table balance ~Ni wherein the alloy contains Pd in a significant amount sufficient to provide the alloy with an improved resistance against hydrogen embrittlement.
0.5-25 ~Cr 0-25 ~~of one or more elements selected from the group consisting of Co, Fe and Mn 1-25 ~~of one or more elements selected from the group consisting of Mo, W, Re and Rh 3-25 ~~of one or more elements selected from the group consisting of Al, Ti, Ta, Nb, and V
0-10 ~~of one or more elements selected from the group consisting of Ru, Os, Ir and Pt < 4.0 ~Pd 0-3 ~~Hf 0-2 ~~Si 0-2 ~~of one or more elements selected from the group consisting of B, C, N and Zr 0-1 ~~of one or more elements selected from the group consisting of Y, La, Sc, the actinides and Ce and the other lanthanides 0-2 ~~of one or more additional elements selected from the group consisting of all elements except for Ni and except for those referred to above in this table balance ~Ni wherein the alloy contains Pd in a significant amount sufficient to provide the alloy with an improved resistance against hydrogen embrittlement.
2. The alloy according to claim 1, wherein the content of said additional elements < 1Ø
3. The alloy according to claim 2, wherein the content of said additional elements is only at the level of impurities that are normally accepted in alloys for components to be used at high temperatures, such as components used in gas turbines.
4. The alloy according to any of the preceding claims, wherein the content of Pd > 0.05.
5. The alloy according to claim 4, wherein the content of Pd < 2Ø
6. The alloy according to claim 5, wherein the content of Pd < 1Ø
7. The alloy according to any of the preceding claims, wherein the content of Cr > 3Ø
8. The alloy according to claim 7, wherein the content of Cr > 6Ø
9. The alloy according to any of the claims 1-6, wherein the content of Cr <= 3Ø
10. The alloy according to any of the preceding claims, wherein the content of one or more elements selected from the group consisting of Co, Fe and Mn > 3Ø
11. The alloy according to claim 10, wherein the content of Co > 6Ø
12. The alloy according to claim 10 or 11, wherein the content of Co > (the content of Fe + the content of Mn).
13. The alloy according to any of the preceding claims, wherein the content of one or more elements selected from the group consisting of Mo, W, Re and Rh > 3Ø
14. The alloy according claim 13, wherein the content of W >
content of Mo.
content of Mo.
15. The alloy according to claim 13 or 14, wherein (the content of Re + the content of Rh) < 1Ø
16. The alloy according to any of the preceding claims, wherein the content of Al > 1Ø
17. The alloy according to claim 16, wherein the content of Al > 3.0 but < 10Ø
18. The alloy according to claim 16 or 17, wherein the molar fraction of Al in the alloy is larger than the molar fraction of any of the other elements selected from the group consisting of Al, Ti, Ta, Nb, and V.
19. The alloy according to any of the preceding claims, wherein the content of one or more elements selected from the group consisting of Ru, Os, Ir and Pt > 0.01 but < 5Ø
20. The alloy according to any of the preceding claims, wherein the content of Hf > 0.05.
21. The alloy according to any of the preceding claims, wherein the content of Si > 0.02.
22. The alloy according to any of the preceding claims, wherein the content of one or more elements selected from the group consisting of B, C, N and Zr > 0.05 but < 0.8.
23. The alloy according to any of the preceding claims, wherein the content of one or more elements selected from the group consisting of Y, La, Sc, the actinides and Ce and the other lanthanides > 0.005.
24. The alloy according to any of the preceding claims, wherein the content of Ni > 35.
25. The alloy according to claim 24, wherein the content of Ni > 50.
26. The alloy according to any of the preceding claims, wherein the volume ratio .gamma.' / .gamma.>0.4 (40%) .
27. The alloy according to any of claim 26, wherein the volume ratio .gamma.' / .gamma. > 0.6 (60%).
28. A component (13, 15) designed for use as a component (13, 15) in a high temperature environment, wherein said component (13, 15) is made from an alloy according to any of the preceding claims.
29. A component (13, 15) according to claim 28, wherein said component (13, 15) is a component (13, 15) for a gas turbine arrangement.
30. A component (13, 15) according to claim 29, wherein said component (13, 15) is a guide vane (13) or part of a guide vane (13) or a turbine rotor blade (15) or part of a turbine rotor blade (15).
31. A gas turbine arrangement comprising at least one component (13, 15) according to claim 29 or 30.
32. Use of Pd which forms part of the alloy according to any of the claims 1-27 for providing said alloy, according to any of the claims 1-27, with improved resistance against hydrogen embrittlement.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE0403162-1 | 2004-12-23 | ||
| SE0403162A SE528807C2 (en) | 2004-12-23 | 2004-12-23 | Component of a superalloy containing palladium for use in a high temperature environment and use of palladium for resistance to hydrogen embrittlement |
| PCT/EP2005/057043 WO2006067189A1 (en) | 2004-12-23 | 2005-12-21 | A ni based alloy, a component, a gas turbine arrangement and use of pd in connection with such an alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2592027A1 true CA2592027A1 (en) | 2006-06-29 |
Family
ID=34102111
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002592027A Abandoned CA2592027A1 (en) | 2004-12-23 | 2005-12-21 | A ni based alloy, a component, a gas turbine arrangement and use of pd in connection with such an alloy |
Country Status (10)
| Country | Link |
|---|---|
| US (4) | US20080101981A1 (en) |
| EP (1) | EP1825012A1 (en) |
| JP (1) | JP2008525634A (en) |
| KR (1) | KR20070091350A (en) |
| CN (1) | CN100587093C (en) |
| BR (1) | BRPI0519432A2 (en) |
| CA (1) | CA2592027A1 (en) |
| RU (1) | RU2007127852A (en) |
| SE (1) | SE528807C2 (en) |
| WO (1) | WO2006067189A1 (en) |
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|---|---|---|---|---|
| RU2768946C1 (en) * | 2021-06-24 | 2022-03-25 | Публичное акционерное общество "ОДК-Уфимское моторостроительное производственное объединение" (ПАО "ОДК-УМПО") | Cast heat-resistant nickel alloy with monocrystalline structure |
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| US7727318B2 (en) | 2007-01-09 | 2010-06-01 | General Electric Company | Metal alloy compositions and articles comprising the same |
| US7846243B2 (en) | 2007-01-09 | 2010-12-07 | General Electric Company | Metal alloy compositions and articles comprising the same |
| US7931759B2 (en) | 2007-01-09 | 2011-04-26 | General Electric Company | Metal alloy compositions and articles comprising the same |
| JP2009084684A (en) * | 2007-09-14 | 2009-04-23 | Toshiba Corp | Nickel-based alloy for turbine rotor of steam turbine, and turbine rotor of steam turbine |
| JP4982324B2 (en) * | 2007-10-19 | 2012-07-25 | 株式会社日立製作所 | Ni-based forged alloy, forged parts for steam turbine plant, boiler tube for steam turbine plant, bolt for steam turbine plant, and steam turbine rotor |
| JP4982340B2 (en) * | 2007-11-30 | 2012-07-25 | 株式会社日立製作所 | Ni-based alloy, gas turbine stationary blade and gas turbine |
| EP2103700A1 (en) * | 2008-03-14 | 2009-09-23 | Siemens Aktiengesellschaft | Nickel base alloy and use of it, turbine blade or vane and gas turbine |
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2004
- 2004-12-23 SE SE0403162A patent/SE528807C2/en not_active IP Right Cessation
-
2005
- 2005-12-21 EP EP05825328A patent/EP1825012A1/en not_active Withdrawn
- 2005-12-21 WO PCT/EP2005/057043 patent/WO2006067189A1/en active Application Filing
- 2005-12-21 CN CN200580044306A patent/CN100587093C/en not_active Expired - Fee Related
- 2005-12-21 RU RU2007127852/02A patent/RU2007127852A/en not_active Application Discontinuation
- 2005-12-21 CA CA002592027A patent/CA2592027A1/en not_active Abandoned
- 2005-12-21 KR KR1020077016658A patent/KR20070091350A/en not_active Application Discontinuation
- 2005-12-21 BR BRPI0519432-6A patent/BRPI0519432A2/en not_active IP Right Cessation
- 2005-12-21 JP JP2007547519A patent/JP2008525634A/en not_active Abandoned
- 2005-12-21 US US11/794,071 patent/US20080101981A1/en not_active Abandoned
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2007
- 2007-04-19 US US11/788,238 patent/US20070202002A1/en not_active Abandoned
- 2007-04-19 US US11/788,295 patent/US20070202003A1/en not_active Abandoned
- 2007-04-19 US US11/788,299 patent/US20070199629A1/en not_active Abandoned
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| RU2768946C1 (en) * | 2021-06-24 | 2022-03-25 | Публичное акционерное общество "ОДК-Уфимское моторостроительное производственное объединение" (ПАО "ОДК-УМПО") | Cast heat-resistant nickel alloy with monocrystalline structure |
Also Published As
| Publication number | Publication date |
|---|---|
| US20080101981A1 (en) | 2008-05-01 |
| US20070199629A1 (en) | 2007-08-30 |
| RU2007127852A (en) | 2009-01-27 |
| CN101087894A (en) | 2007-12-12 |
| SE0403162D0 (en) | 2004-12-23 |
| KR20070091350A (en) | 2007-09-10 |
| SE528807C2 (en) | 2007-02-20 |
| CN100587093C (en) | 2010-02-03 |
| JP2008525634A (en) | 2008-07-17 |
| BRPI0519432A2 (en) | 2009-01-20 |
| SE0403162L (en) | 2006-06-24 |
| US20070202003A1 (en) | 2007-08-30 |
| US20070202002A1 (en) | 2007-08-30 |
| WO2006067189A1 (en) | 2006-06-29 |
| EP1825012A1 (en) | 2007-08-29 |
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