WO2006067189A1 - 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 PDF

Info

Publication number
WO2006067189A1
WO2006067189A1 PCT/EP2005/057043 EP2005057043W WO2006067189A1 WO 2006067189 A1 WO2006067189 A1 WO 2006067189A1 EP 2005057043 W EP2005057043 W EP 2005057043W WO 2006067189 A1 WO2006067189 A1 WO 2006067189A1
Authority
WO
WIPO (PCT)
Prior art keywords
content
alloy
alloy according
component
elements
Prior art date
Application number
PCT/EP2005/057043
Other languages
French (fr)
Inventor
Douglas James Arrell
Magnus Hasselqvist
Original Assignee
Siemens Aktiengesellschaft
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Siemens Aktiengesellschaft filed Critical Siemens Aktiengesellschaft
Priority to US11/794,071 priority Critical patent/US20080101981A1/en
Priority to JP2007547519A priority patent/JP2008525634A/en
Priority to EP05825328A priority patent/EP1825012A1/en
Priority to CA002592027A priority patent/CA2592027A1/en
Priority to BRPI0519432-6A priority patent/BRPI0519432A2/en
Publication of WO2006067189A1 publication Critical patent/WO2006067189A1/en
Priority to US11/788,295 priority patent/US20070202003A1/en
Priority to US11/788,299 priority patent/US20070199629A1/en
Priority to US11/788,238 priority patent/US20070202002A1/en

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
    • 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%

Definitions

  • 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 .
  • the invention relates to a gas turbine arrangement .
  • the invention relates to the use of Pd in alloys .
  • superalloys are 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.
  • 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 .
  • 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 ⁇ ' ( "gamma prime" ) , based on Ni 3 (Ti, Al) , within the host material ( ⁇ ) .
  • the document US 6 177 046 Bl describes ⁇ / ⁇ ' superalloys containing Pd .
  • Pd is added in order to provide improved weldability to the alloy .
  • the Pd content should be 5-40 weight % (Table 7 ) , 5-45 weight % (Table 8 ) or 8-27 weight % (the table in column 17 ) .
  • 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 ⁇ / ⁇ ' 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 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 .
  • 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 ⁇ / ⁇ ' alloys are known to have excellent properties for use at high temperatures , such as for components in gas turbines .
  • HE has been reported also for these alloys , see the paper by Nazmy et al mentioned above .
  • Ni based ⁇ / ⁇ ' alloys are quite complex alloys . These alloys have a matrix of the ⁇ phase, which is Ni with other elements like Cr, Co, Fe, W, Mo and Re in solution . Furthermore, such alloys contain particles of the ⁇ ' phase, which normally is Ni 3 Al 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 ⁇ and ⁇ ' 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 .
  • Al tends to partition favourably to the ⁇ ' phase .
  • Pd tends to partition favourably to the ⁇ ' phase .
  • the partition of an element between the ⁇ and ⁇ ' 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 ⁇ phase .
  • Components of Ni based ⁇ / ⁇ ' alloys usually have a protective oxide layer that will prevent hydrogen embrittlement .
  • 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 .
  • 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 ⁇ / ⁇ ' 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 .
  • the risk of hydrogen embrittlement should be reduced when components made from the alloy are subjected to thermal cycling with humid conditions under at least parts of the cycle .
  • 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 ⁇ / ⁇ ' 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 ⁇ / ⁇ ' alloy and consisting, in weight %, of :
  • the alloy contains Pd in a significant amount sufficient to provide the alloy with an improved resistance against hydrogen embrittlement .
  • 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 ⁇ ' phase by Pd . As is mentioned above, Pd partitions favourably to the ⁇ ' 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
  • 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 .
  • 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 .
  • the content of Cr > 3.0, preferably > 6.0. With a fairly large amount of Cr an excellent corrosion and oxidation resistance is obtained.
  • the content of Cr ⁇ 3.0. 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.
  • the content of Co can for example be > 6.0.
  • 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.
  • the content of W can, according to a preferred embodiment , be > content of Mo .
  • (the content of Re + the content of Rh) can be ⁇ 1.0. With a sufficient amount of for example W, the strength of the alloy is increased . Furthermore, the creep resistance is improved .
  • the content of Al > 1.0.
  • the content of Al can for example be > 3.0 but ⁇ 10.0.
  • 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 ⁇ ' phase .
  • Al can increase the oxidation and hot corrosion resistance .
  • the content of one or more elements selected from the group consisting of Ru, Os , Ir and Pt > 0.01 but ⁇ 5.0. The addition of elements from this group can be used to control the partition of other elements between the two phases ⁇ and ⁇ ' .
  • the content of Hf can, according to an embodiment , be > 0.05.
  • 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 .
  • the alloy thus preferably contains a quite large amount of the base element Ni .
  • a quite high fraction of ⁇ ' is advantageous for providing a high hot strength .
  • a component designed for use as a component in a high temperature environment 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 .
  • the component can be used at high temperatures and still have a good resistance against hydrogen embrittlement .
  • 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 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 .
  • Fig 1 shows very schematically a turbine arrangement according to the invention with a plurality of components according to the invention .
  • the alloys 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 .
  • all the alloys are Ni based ⁇ / ⁇ ' alloys .
  • the ratio ⁇ ' / ⁇ can for example be 0.4 ( 40%) or > 0.6 ( 60%) . This ratio can for example be 0.5 ( 50%) .
  • 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 .
  • 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 ⁇ / ⁇ ' superalloys of the prior art .
  • the alloys can be used for producing single crystal, directionally solidified or polycrystalline components in a 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 a typical gas turbine arrangement according to the invention .
  • the gas turbine arrangement has an annular combustion chamber 11.
  • 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 .
  • 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 .
  • 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 .

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)
  • Crystals, And After-Treatments Of Crystals (AREA)
  • Physical Vapour Deposition (AREA)
  • Other Surface Treatments For Metallic Materials (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 connect ion 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 γ' ( "gamma prime" ) , based on Ni3 (Ti, Al) , within the host material (γ) .
The document US 6 177 046 Bl describes γ/γ' 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 % (Table 7 ) , 5-45 weight % (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 γ/γ' 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 γ/γ' 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 γ/γ' alloys are quite complex alloys . These alloys have a matrix of the γ phase, which is Ni with other elements like Cr, Co, Fe, W, Mo and Re in solution . Furthermore, such alloys contain particles of the γ' 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 γ and γ' 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 γ' phase . It has also been reported that Pd tends to partition favourably to the γ' phase . Furthermore, the partition of an element between the γ and γ' 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 γ phase .
SUMMARY OF THE INVENTION
Components of Ni based γ/γ' 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 γ/γ' 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 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 γ/γ' 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 γ/γ' alloy and consisting, in weight %, of :
Figure imgf000007_0001
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 γ' phase by Pd . As is mentioned above, Pd partitions favourably to the γ' 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 γ' 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 γ/γ' alloys such that slightly more Al partitions to the γ phase . This means , for a given γ' 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 > 6.0. 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 < 3.0. 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 > 3.0. The content of Co can for example be > 6.0. 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 > 3.0. 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 < 1.0. 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 > 1.0. The content of Al can for example be > 3.0 but < 10.0. 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 γ' 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 < 5.0. The addition of elements from this group can be used to control the partition of other elements between the two phases γ and γ' .
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 γ' /γ > 0.4 ( 40%) or even > 0.6 ( 60%) . A quite high fraction of γ' 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 .
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 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 γ/γ' alloys . The ratio γ' /γ can for example be 0.4 ( 40%) or > 0.6 ( 60%) . This ratio can for example be 0.5 ( 50%) .
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 W
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
3-5 W
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
3-5 W
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
9-11 W
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
1-3 W
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
1-3 W
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
7-9 W
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
0.005-0.0 15 C
0.005-0.0 15 B
Example 9
6-7 Cr
9-11 Co
0.4-0.8 Mo
5-7 W
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
0.005-0.0 15 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 S i
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 γ/γ' superalloys of the prior art . The alloys can be used for producing single crystal, directionally solidified or polycrystalline components in a 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 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

Cl aims
1. A Ni based alloy suitable for single crystalline, directionally solidified or polycrystalline components to be used at high temperatures , the alloy being a γ/γ' alloy and consisting, in weight %, of :
Figure imgf000019_0001
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 < 1.0.
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 < 2.0.
6. The alloy according to claim 5 , wherein the content of Pd < 1.0.
7. The alloy according to any of the preceding claims , wherein the content of Cr > 3.0.
8. The alloy according to claim 7 , wherein the content of Cr > 6.0.
9. The alloy according to any of the claims 1-6 , wherein the content of Cr < 3.0.
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 > 3.0.
11. The alloy according to claim 10 , wherein the content of Co > 6.0.
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 > 3.0.
14. The alloy according claim 13 , wherein the content of W > content of Mo .
15. The alloy according to claim 13 or 14 , wherein (the content of Re + the content of Rh) < 1.0.
16. The alloy according to any of the preceding claims , wherein the content of Al > 1.0.
17. The alloy according to claim 16 , wherein the content of Al > 3.0 but < 10.0.
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 < 5.0.
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 γ' /γ > 0.4 ( 40%) .
27. The alloy according to any of claim 26 , wherein the volume ratio γ' /γ > 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 .
PCT/EP2005/057043 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 WO2006067189A1 (en)

Priority Applications (8)

Application Number Priority Date Filing Date Title
US11/794,071 US20080101981A1 (en) 2004-12-23 2005-12-21 Ni Based Alloy, a Component, a Gas Turbine Arrangement and Use of Pd in Connection With Such an Alloy
JP2007547519A JP2008525634A (en) 2004-12-23 2005-12-21 Ni-based alloys, components, gas turbine equipment and use of Pd in connection with the alloys
EP05825328A EP1825012A1 (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
CA002592027A 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
BRPI0519432-6A BRPI0519432A2 (en) 2004-12-23 2005-12-21 ni-based alloy arrangement, one component and one gas turbine and use of pd in connection with such an alloy
US11/788,295 US20070202003A1 (en) 2004-12-23 2007-04-19 Rare earth modified high strength oxidation resistant superalloy with enhanced coating compatibility
US11/788,299 US20070199629A1 (en) 2004-12-23 2007-04-19 Corrosion resistant superalloy with improved oxidation resistance
US11/788,238 US20070202002A1 (en) 2004-12-23 2007-04-19 Rare earth modified corrosion resistant superalloy with enhanced oxidation resistance and coating compatibility

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
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
SE0403162-1 2004-12-23

Related Child Applications (3)

Application Number Title Priority Date Filing Date
US11/788,238 Continuation-In-Part US20070202002A1 (en) 2004-12-23 2007-04-19 Rare earth modified corrosion resistant superalloy with enhanced oxidation resistance and coating compatibility
US11/788,299 Continuation-In-Part US20070199629A1 (en) 2004-12-23 2007-04-19 Corrosion resistant superalloy with improved oxidation resistance
US11/788,295 Continuation-In-Part US20070202003A1 (en) 2004-12-23 2007-04-19 Rare earth modified high strength oxidation resistant superalloy with enhanced coating compatibility

Publications (1)

Publication Number Publication Date
WO2006067189A1 true WO2006067189A1 (en) 2006-06-29

Family

ID=34102111

Family Applications (1)

Application Number Title Priority Date Filing Date
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

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)

Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1953253A1 (en) * 2007-01-09 2008-08-06 General Electric Company Metal alloy compositions and articles comprising the same
EP2039789A1 (en) * 2007-09-14 2009-03-25 Kabushiki Kaisha Toshiba Nickel-based alloy for turbine rotor of steam turbine and turbine rotor of steam turbine
EP2145968A1 (en) * 2008-07-14 2010-01-20 Siemens Aktiengesellschaft Nickel base gamma prime strengthened superalloy
CH699716A1 (en) * 2008-10-13 2010-04-15 Alstom Technology Ltd Component for high temperature steam turbine and high temperature steam turbine.
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
ITCO20090027A1 (en) * 2009-07-29 2011-01-30 Nuovo Pignone Spa NICKEL-BASED SUPERLEGA, MECHANICAL COMPONENT MADE WITH SUCH A SUPERLEGA, TURBOMACCHINA INCLUDING SUCH COMPONENT AND RELATIVE METHODS
EP2292807A1 (en) * 2009-09-04 2011-03-09 Hitachi, Ltd. Ni based casting alloy and turbine casing
CN102828070A (en) * 2012-08-24 2012-12-19 朱小英 Protective coating material for boiler pipeline
EP2465957A4 (en) * 2009-08-10 2015-03-04 Ihi Corp Ni-BASED MONOCRYSTALLINE SUPERALLOY AND TURBINE BLADE
EP2868427A3 (en) * 2013-11-04 2016-01-06 Siemens Energy, Inc. Braze alloy compositions and brazing methods for superalloys
WO2016146560A1 (en) * 2015-03-16 2016-09-22 Siemens Aktiengesellschaft Ni-Mn-Cr-Al-Ti-ALLOY, POWDER, METHOD AND COMPONENT
EP3287535A1 (en) * 2016-08-22 2018-02-28 Siemens Aktiengesellschaft Sx nickel alloy with improved tmf properties, raw material and component

Families Citing this family (54)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
US8029596B2 (en) 2008-08-19 2011-10-04 Siemens Energy, Inc. Method of making rare-earth strengthened components
US8192850B2 (en) * 2008-08-20 2012-06-05 Siemens Energy, Inc. Combustion turbine component having bond coating and associated methods
JP5408768B2 (en) * 2008-12-04 2014-02-05 三菱マテリアル株式会社 Ni-base heat-resistant alloy ingot having high-temperature strength and dendritic structure and gas turbine blade casting comprising the same
WO2010128147A1 (en) * 2009-05-08 2010-11-11 Sulzer Metco Ag Method for coating a substrate and substrate with a coating
FR2949234B1 (en) * 2009-08-20 2011-09-09 Aubert & Duval Sa SUPERALLIAGE NICKEL BASE AND PIECES REALIZED IN THIS SUPALLIATION
US8449262B2 (en) * 2009-12-08 2013-05-28 Honeywell International Inc. Nickel-based superalloys, turbine blades, and methods of improving or repairing turbine engine components
US9138963B2 (en) * 2009-12-14 2015-09-22 United Technologies Corporation Low sulfur nickel base substrate alloy and overlay coating system
JP5427642B2 (en) * 2010-02-24 2014-02-26 株式会社日立製作所 Nickel-based alloy and land gas turbine parts using the same
US20110256421A1 (en) * 2010-04-16 2011-10-20 United Technologies Corporation Metallic coating for single crystal alloys
CA2810504C (en) * 2010-11-10 2016-01-05 Honda Motor Co., Ltd. Nickel alloy
KR20120105693A (en) * 2011-03-16 2012-09-26 한국기계연구원 Ni base single crystal superalloy with enhanced creep property
RU2484167C1 (en) * 2012-03-27 2013-06-10 Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") Ni3Al INTERMETALLIDE-BASED ALLOY AND ARTICLES MADE THEREOF
US9339398B2 (en) * 2012-04-26 2016-05-17 Medtronic Vascular, Inc. Radiopaque enhanced nickel alloy for stents
CN102808112B (en) * 2012-08-24 2015-05-06 朱育盼 Nickel-based superalloy for exhaust valve
CN102808111B (en) * 2012-08-24 2014-08-20 朱育盼 Preparation method for nickel-based superalloy for exhaust valve
CN102808110B (en) * 2012-08-24 2015-05-06 朱育盼 Nickel-based alloy wire material used for coating layer of sealing surface of stainless steel valve
JP5721189B2 (en) * 2013-03-12 2015-05-20 株式会社 東北テクノアーチ Heat-resistant Ni-based alloy and method for producing the same
GB201400352D0 (en) 2014-01-09 2014-02-26 Rolls Royce Plc A nickel based alloy composition
JP2015189999A (en) * 2014-03-28 2015-11-02 田中貴金属工業株式会社 NiIr-BASED HEAT-RESISTANT ALLOY AND PRODUCTION METHOD THEREOF
CN104404309A (en) * 2014-12-02 2015-03-11 常熟市良益金属材料有限公司 High-temperature resistant nickel alloy
EP3042973B1 (en) 2015-01-07 2017-08-16 Rolls-Royce plc A nickel alloy
JPWO2016142962A1 (en) * 2015-03-06 2017-12-21 株式会社東芝 Ni-base alloy for casting and casting parts for turbine
CN106191529B (en) * 2015-04-20 2018-01-02 中南大学 Nickel-base alloy and the article formed by alloy
CN104878249A (en) * 2015-05-15 2015-09-02 新奥科技发展有限公司 Nickel-based alloy and preparation method and application thereof
CN106282668B (en) * 2015-06-12 2018-09-14 中南大学 A kind of nickel base superalloy and preparation method thereof
GB2539957B (en) 2015-07-03 2017-12-27 Rolls Royce Plc A nickel-base superalloy
CN105088018A (en) * 2015-09-10 2015-11-25 钢铁研究总院 High-strength oxidation-resisting cobalt-based super alloy
RU2626118C2 (en) * 2015-09-17 2017-07-21 Открытое акционерное общество "Научно-производственное объединение "Сатурн" Casting heat resistant nickel-based alloy
CN106807794B (en) * 2015-12-08 2019-03-08 中南大学 The determination method of nickel base superalloy Hot Extrusion Parameters and the hot extrusion technique of nickel base superalloy
CN105543568B (en) * 2015-12-21 2017-10-13 谷月恒 A kind of platiniferous non-rhenium nickel base single crystal superalloy and its preparation method and application
ITUA20161551A1 (en) * 2016-03-10 2017-09-10 Nuovo Pignone Tecnologie Srl LEAGUE HAVING HIGH RESISTANCE TO OXIDATION AND APPLICATIONS OF GAS TURBINES THAT USE IT
GB201615496D0 (en) 2016-09-13 2016-10-26 Rolls Royce Plc Nickel-based superalloy and use thereof
TWI663263B (en) * 2016-11-25 2019-06-21 國家中山科學研究院 High creep-resistant equiaxed grain nickel-based superalloy
CN106756252B (en) * 2016-12-29 2019-03-22 沈阳大陆激光工程技术有限公司 A kind of Co-based alloy powder for heavy combustion engine wheel hub tenon tooth reparation
CN106636760B (en) * 2017-01-16 2019-01-08 宁国市华成金研科技有限公司 A kind of nickel base superalloy and its manufacturing method
CN106676366B (en) * 2017-01-16 2018-12-28 宁国市华成金研科技有限公司 The preparation method of high-temperature alloy
CN107805807B (en) * 2017-10-23 2019-06-25 武汉理工大学 A kind of steam turbine sliding block and preparation method thereof based on laser melting deposition
CN108004433B (en) * 2017-10-25 2019-04-23 广西贵三钜科技有限公司 A kind of engine nozzle fuel-economizing strainer and preparation method thereof
KR101866833B1 (en) * 2017-11-24 2018-06-14 한국기계연구원 Nickel-based heat-resistant material improved cyclic oxidation property and method of preparing the same
CN108486418B (en) * 2018-04-25 2020-08-11 常州市潞城慧热电子厂 Alloy wire for thermoelectric generator and preparation process thereof
CN108588605B (en) * 2018-05-03 2020-05-05 西安科技大学 Heat treatment process of boron-containing nickel-based single crystal superalloy
DE102018251722A1 (en) 2018-12-27 2020-07-02 Siemens Aktiengesellschaft Nickel based alloy for additive manufacturing and processes
CA3129143A1 (en) * 2019-03-07 2020-09-10 Oerlikon Metco (Us) Inc. Advanced bond coat materials for tbc with improved thermal cyclic fatigue and sulfidation resistance
CN110802345A (en) * 2019-11-21 2020-02-18 天津铸金科技开发股份有限公司 High-temperature-resistant plasma spray welding powder
CN112410616B (en) * 2020-11-03 2022-07-12 中国航发北京航空材料研究院 Low-cost and low-macrosegregation-tendency high-temperature alloy for large isothermal forging die
US11426822B2 (en) * 2020-12-03 2022-08-30 General Electric Company Braze composition and process of using
CN112501476B (en) * 2021-01-29 2021-06-25 北京科技大学 Ultrahigh-strength-toughness high-density alloy and preparation method and application thereof
CN112981184B (en) * 2021-02-03 2022-04-01 中国人民解放军陆军装甲兵学院 High-plasticity high-temperature-resistant nickel-based alloy powder
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
CN114686731B (en) * 2022-04-12 2022-11-22 北航（四川）西部国际创新港科技有限公司 Single crystal high temperature alloy and preparation method and application thereof
CN115449669B (en) * 2022-09-13 2023-08-08 中国联合重型燃气轮机技术有限公司 Creep-resistant and oxidation-resistant nickel-based superalloy, and preparation method and application thereof

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1997038144A1 (en) * 1996-04-10 1997-10-16 The Penn State Research Foundation Improved superalloys with improved oxidation resistance and weldability
EP0848071A1 (en) * 1996-12-11 1998-06-17 United Technologies Corporation Superalloy compositions
WO2001064964A1 (en) * 2000-02-29 2001-09-07 General Electric Company Nickel base superalloys and turbine components fabricated therefrom
US20030041930A1 (en) * 2001-08-30 2003-03-06 Deluca Daniel P. Modified advanced high strength single crystal superalloy composition

Family Cites Families (29)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA967403A (en) * 1971-02-23 1975-05-13 International Nickel Company Of Canada Nickel alloy with good stress rupture strength
US4039330A (en) * 1971-04-07 1977-08-02 The International Nickel Company, Inc. Nickel-chromium-cobalt alloys
BE794144A (en) * 1972-01-17 1973-07-17 Int Nickel Ltd NICKEL-CHROME ALLOYS
GB1520630A (en) * 1974-07-08 1978-08-09 Johnson Matthey Co Ltd Platinum group metal-containing alloys
US4261742A (en) * 1978-09-25 1981-04-14 Johnson, Matthey & Co., Limited Platinum group metal-containing alloys
SE428937B (en) * 1979-01-11 1983-08-01 Cabot Stellite Europ NICKEL-BASED, HARD ALLOY OR ADDITIVE MATERIAL PROVIDED FOR WASTE WASTE OR WELDING
DE3272247D1 (en) * 1981-04-08 1986-09-04 Johnson Matthey Plc Nickel alloys containing large amounts of chromium
US4519979A (en) * 1983-06-06 1985-05-28 Inco Europe Limited Nickel-chromium-cobalt base alloys and castings thereof
US4885216A (en) * 1987-04-03 1989-12-05 Avco Corporation High strength nickel base single crystal alloys
US5077141A (en) * 1984-12-06 1991-12-31 Avco Corporation High strength nickel base single crystal alloys having enhanced solid solution strength and methods for making same
US4719080A (en) * 1985-06-10 1988-01-12 United Technologies Corporation Advanced high strength single crystal superalloy compositions
US4692305A (en) * 1985-11-05 1987-09-08 Perkin-Elmer Corporation Corrosion and wear resistant alloy
EP0433072B1 (en) * 1989-12-15 1994-11-09 Inco Alloys International, Inc. Oxidation resistant low expansion superalloys
US5077006A (en) * 1990-07-23 1991-12-31 Carondelet Foundry Company Heat resistant alloys
US5346563A (en) * 1991-11-25 1994-09-13 United Technologies Corporation Method for removing sulfur from superalloy articles to improve their oxidation resistance
US5366695A (en) * 1992-06-29 1994-11-22 Cannon-Muskegon Corporation Single crystal nickel-based superalloy
JP2625612B2 (en) * 1992-07-20 1997-07-02 インターナショナル・ビジネス・マシーンズ・コーポレイション Image processing method and image processing apparatus
EP0648850B1 (en) * 1993-09-20 1997-08-13 Mitsubishi Materials Corporation Nickel-based alloy
GB9903988D0 (en) * 1999-02-22 1999-10-20 Rolls Royce Plc A nickel based superalloy
EP1184473B1 (en) * 2000-08-30 2005-01-05 Kabushiki Kaisha Toshiba Nickel-base single-crystal superalloys, method of manufacturing same and gas turbine high temperature parts made thereof
US20020164263A1 (en) * 2001-03-01 2002-11-07 Kenneth Harris Superalloy for single crystal turbine vanes
US7011721B2 (en) * 2001-03-01 2006-03-14 Cannon-Muskegon Corporation Superalloy for single crystal turbine vanes
CA2479774C (en) * 2002-03-27 2012-09-04 National Institute For Materials Science Ni-base directionally solidified and single-crystal superalloy
CH695497A5 (en) * 2002-04-30 2006-06-15 Alstom Technology Ltd Nickel-base superalloy.
US20040042927A1 (en) * 2002-08-27 2004-03-04 O'hara Kevin Swayne Reduced-tantalum superalloy composition of matter and article made therefrom, and method for selecting a reduced-tantalum superalloy
US6905559B2 (en) * 2002-12-06 2005-06-14 General Electric Company Nickel-base superalloy composition and its use in single-crystal articles
JP4036091B2 (en) * 2002-12-17 2008-01-23 株式会社日立製作所 Nickel-base heat-resistant alloy and gas turbine blade
JP4449337B2 (en) * 2003-05-09 2010-04-14 株式会社日立製作所 High oxidation resistance Ni-base superalloy castings and gas turbine parts
US20060051234A1 (en) * 2004-09-03 2006-03-09 Pike Lee M Jr Ni-Cr-Co alloy for advanced gas turbine engines

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1997038144A1 (en) * 1996-04-10 1997-10-16 The Penn State Research Foundation Improved superalloys with improved oxidation resistance and weldability
EP0848071A1 (en) * 1996-12-11 1998-06-17 United Technologies Corporation Superalloy compositions
US6007645A (en) * 1996-12-11 1999-12-28 United Technologies Corporation Advanced high strength, highly oxidation resistant single crystal superalloy compositions having low chromium content
WO2001064964A1 (en) * 2000-02-29 2001-09-07 General Electric Company Nickel base superalloys and turbine components fabricated therefrom
US20030041930A1 (en) * 2001-08-30 2003-03-06 Deluca Daniel P. Modified advanced high strength single crystal superalloy composition

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
WHITNEY, E., SIMKOVICH, G., FINK, J.: "High Temperature Oxidation of a Modified Alloy 625", SUPERALLOYS 718, 625, 706 AND VARIOUS DERIVATIVES, PROCEEDINGS OF THE INTERNATIONAL SYMPOSIUM, ED. BY E.A. LORIA, PUBLISHER: THE MINERALS, METALS & MATERIALS SOCIETY, 1997, Warrendale, Pa., USA, pages 695 - 704, XP009066278 *
YANG, L., MCLELLAN, R.B.: "Effect of palladium on the hydrogen embrittlement of B-doped Ni3Al", JOURNAL OF MATERIALS RESEARCH, vol. 11, no. 4, 1996, pages 862 - 864, XP002380624 *

Cited By (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7931759B2 (en) 2007-01-09 2011-04-26 General Electric Company Metal alloy compositions and articles comprising the same
EP1953253A1 (en) * 2007-01-09 2008-08-06 General Electric Company Metal alloy compositions and articles comprising the same
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
EP2039789A1 (en) * 2007-09-14 2009-03-25 Kabushiki Kaisha Toshiba Nickel-based alloy for turbine rotor of steam turbine and turbine rotor of steam turbine
EP2145968A1 (en) * 2008-07-14 2010-01-20 Siemens Aktiengesellschaft Nickel base gamma prime strengthened superalloy
US8431073B2 (en) 2008-07-14 2013-04-30 Siemens Aktiengesellschaft Nickel base gamma prime strengthened superalloy
WO2010006974A1 (en) * 2008-07-14 2010-01-21 Siemens Aktiengesellschaft Nickel base gamma prime strengthened superalloy
CH699716A1 (en) * 2008-10-13 2010-04-15 Alstom Technology Ltd Component for high temperature steam turbine and high temperature steam turbine.
EP2312001A1 (en) * 2009-07-29 2011-04-20 Nuovo Pignone S.p.A. Nickel-based superalloy, mechanical component made of it, piece of turbomachinery which includes the component and related methods
ITCO20090027A1 (en) * 2009-07-29 2011-01-30 Nuovo Pignone Spa NICKEL-BASED SUPERLEGA, MECHANICAL COMPONENT MADE WITH SUCH A SUPERLEGA, TURBOMACCHINA INCLUDING SUCH COMPONENT AND RELATIVE METHODS
US9359658B2 (en) 2009-07-29 2016-06-07 Nuovo Pignone S.P.A Nickel-based superalloy, mechanical component made of the above mentioned super alloy, piece of turbomachinery which includes the above mentioned component and related methods
EP2465957A4 (en) * 2009-08-10 2015-03-04 Ihi Corp Ni-BASED MONOCRYSTALLINE SUPERALLOY AND TURBINE BLADE
US9932657B2 (en) 2009-08-10 2018-04-03 Ihi Corporation Method of making a Ni—based single crystal superalloy and turbine blade incorporating same
EP2292807A1 (en) * 2009-09-04 2011-03-09 Hitachi, Ltd. Ni based casting alloy and turbine casing
CN102828070A (en) * 2012-08-24 2012-12-19 朱小英 Protective coating material for boiler pipeline
EP2868427A3 (en) * 2013-11-04 2016-01-06 Siemens Energy, Inc. Braze alloy compositions and brazing methods for superalloys
US9611741B2 (en) 2013-11-04 2017-04-04 Siemens Energy, Inc. Braze alloy compositions and brazing methods for superalloys
WO2016146560A1 (en) * 2015-03-16 2016-09-22 Siemens Aktiengesellschaft Ni-Mn-Cr-Al-Ti-ALLOY, POWDER, METHOD AND COMPONENT
EP3287535A1 (en) * 2016-08-22 2018-02-28 Siemens Aktiengesellschaft Sx nickel alloy with improved tmf properties, raw material and component
WO2018036797A1 (en) * 2016-08-22 2018-03-01 Siemens Aktiengesellschaft Sx-nickel alloy having improved tmf properties, raw material, and component

Also Published As

Publication number Publication date
CN101087894A (en) 2007-12-12
US20070199629A1 (en) 2007-08-30
US20070202003A1 (en) 2007-08-30
JP2008525634A (en) 2008-07-17
SE0403162D0 (en) 2004-12-23
EP1825012A1 (en) 2007-08-29
KR20070091350A (en) 2007-09-10
US20080101981A1 (en) 2008-05-01
SE0403162L (en) 2006-06-24
BRPI0519432A2 (en) 2009-01-20
SE528807C2 (en) 2007-02-20
CN100587093C (en) 2010-02-03
RU2007127852A (en) 2009-01-27
CA2592027A1 (en) 2006-06-29
US20070202002A1 (en) 2007-08-30

Similar Documents

Publication Publication Date Title
EP1825012A1 (en) A ni based alloy, a component, a gas turbine arrangement and use of pd in connection with such an alloy
JP5177559B2 (en) Ni-based single crystal superalloy
US7169241B2 (en) Ni-based superalloy having high oxidation resistance and gas turbine part
US20090087338A1 (en) Nickel base super alloy
US5516381A (en) Rotating blade or stationary vane of a gas turbine
US7666352B2 (en) Iridium-based alloy with high heat resistance and high strength and process for producing the same
CA2680650C (en) Ni-based single crystal superalloy and turbine blade incorporating the same
WO2009023090A2 (en) Corrosion resistant nickel alloy compositions with enhanced castability and mechanical properties
JP5226846B2 (en) High heat resistance, high strength Rh-based alloy and method for producing the same
JPWO2010119709A1 (en) Ni-based single crystal superalloy and turbine blade using the same
US6740292B2 (en) Nickel-base superalloy
CN111172430A (en) Nickel-based superalloy and article
US8048368B2 (en) High temperature and oxidation resistant material
JP4523264B2 (en) Nickel-base superalloy for manufacturing single crystal parts
EP1627930A1 (en) Stable, high-temperature nickel-base superalloy and single-crystal articles utilizing the superalloy
US6982059B2 (en) Rhodium, platinum, palladium alloy
JP4805803B2 (en) Ni-based alloy and turbine rotor
JPH09268337A (en) Forged high corrosion resistant superalloy alloy
AU2003255216B2 (en) Nickel-base superalloy
EP4211282A1 (en) Nickel based superalloy with high oxidation resistance, high corrosion resistance and good processability

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BW BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE EG ES FI GB GD GE GH GM HR HU ID IL IN IS JP KE KG KM KN KP KR KZ LC LK LR LS LT LU LV LY MA MD MG MK MN MW MX MZ NA NG NI NO NZ OM PG PH PL PT RO RU SC SD SE SG SK SL SM SY TJ TM TN TR TT TZ UA UG US UZ VC VN YU ZA ZM ZW

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): BW GH GM KE LS MW MZ NA SD SL SZ TZ UG ZM ZW AM AZ BY KG KZ MD RU TJ TM AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LT LU LV MC NL PL PT RO SE SI SK TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG

121 Ep: the epo has been informed by wipo that ep was designated in this application
WWE Wipo information: entry into national phase

Ref document number: 11788238

Country of ref document: US

Ref document number: 11788295

Country of ref document: US

Ref document number: 11788299

Country of ref document: US

WWE Wipo information: entry into national phase

Ref document number: 1830/KOLNP/2007

Country of ref document: IN

WWE Wipo information: entry into national phase

Ref document number: 2005825328

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: 2007547519

Country of ref document: JP

WWE Wipo information: entry into national phase

Ref document number: 2592027

Country of ref document: CA

WWE Wipo information: entry into national phase

Ref document number: 200580044306.6

Country of ref document: CN

NENP Non-entry into the national phase

Ref country code: DE

WWE Wipo information: entry into national phase

Ref document number: 1020077016658

Country of ref document: KR

WWE Wipo information: entry into national phase

Ref document number: 2007127852

Country of ref document: RU

WWP Wipo information: published in national office

Ref document number: 2005825328

Country of ref document: EP

WWP Wipo information: published in national office

Ref document number: 11788238

Country of ref document: US

Ref document number: 11788299

Country of ref document: US

Ref document number: 11788295

Country of ref document: US

WWE Wipo information: entry into national phase

Ref document number: 11794071

Country of ref document: US

WWP Wipo information: published in national office

Ref document number: 11794071

Country of ref document: US

ENP Entry into the national phase

Ref document number: PI0519432

Country of ref document: BR