NO141371B - MCRALY TYPE COATING ALLOY. - Google Patents
MCRALY TYPE COATING ALLOY. Download PDFInfo
- Publication number
- NO141371B NO141371B NO75752355A NO752355A NO141371B NO 141371 B NO141371 B NO 141371B NO 75752355 A NO75752355 A NO 75752355A NO 752355 A NO752355 A NO 752355A NO 141371 B NO141371 B NO 141371B
- Authority
- NO
- Norway
- Prior art keywords
- alloy
- coating
- platinum
- weight percent
- rhodium
- Prior art date
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- 229910045601 alloy Inorganic materials 0.000 title claims description 36
- 239000000956 alloy Substances 0.000 title claims description 36
- 238000000576 coating method Methods 0.000 title claims description 29
- 239000011248 coating agent Substances 0.000 title claims description 18
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 claims description 30
- 238000005260 corrosion Methods 0.000 claims description 16
- 230000007797 corrosion Effects 0.000 claims description 16
- 229910052697 platinum Inorganic materials 0.000 claims description 12
- 229910052703 rhodium Inorganic materials 0.000 claims description 11
- 239000010948 rhodium Substances 0.000 claims description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 10
- MHOVAHRLVXNVSD-UHFFFAOYSA-N rhodium atom Chemical compound [Rh] MHOVAHRLVXNVSD-UHFFFAOYSA-N 0.000 claims description 10
- 229910052751 metal Inorganic materials 0.000 claims description 9
- 239000002184 metal Substances 0.000 claims description 9
- 229910052727 yttrium Inorganic materials 0.000 claims description 7
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 5
- 229910052776 Thorium Inorganic materials 0.000 claims description 4
- 239000010970 precious metal Substances 0.000 claims description 4
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 4
- 150000002910 rare earth metals Chemical class 0.000 claims description 4
- 229910052706 scandium Inorganic materials 0.000 claims description 4
- ZSLUVFAKFWKJRC-IGMARMGPSA-N 232Th Chemical compound [232Th] ZSLUVFAKFWKJRC-IGMARMGPSA-N 0.000 claims description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- QXZUUHYBWMWJHK-UHFFFAOYSA-N [Co].[Ni] Chemical compound [Co].[Ni] QXZUUHYBWMWJHK-UHFFFAOYSA-N 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 239000011651 chromium Substances 0.000 claims description 3
- 229910017052 cobalt Inorganic materials 0.000 claims description 3
- 239000010941 cobalt Substances 0.000 claims description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 claims description 3
- 229910000531 Co alloy Inorganic materials 0.000 claims description 2
- 229910000990 Ni alloy Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 239000000203 mixture Substances 0.000 description 15
- 238000000034 method Methods 0.000 description 7
- 229910000951 Aluminide Inorganic materials 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 230000003647 oxidation Effects 0.000 description 5
- 238000007254 oxidation reaction Methods 0.000 description 5
- 238000007792 addition Methods 0.000 description 4
- 230000004888 barrier function Effects 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 230000003628 erosive effect Effects 0.000 description 3
- 229910000510 noble metal Inorganic materials 0.000 description 3
- 239000011734 sodium Substances 0.000 description 3
- 229910000601 superalloy Inorganic materials 0.000 description 3
- 239000007832 Na2SO4 Substances 0.000 description 2
- PMZURENOXWZQFD-UHFFFAOYSA-L Sodium Sulfate Chemical compound [Na+].[Na+].[O-]S([O-])(=O)=O PMZURENOXWZQFD-UHFFFAOYSA-L 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 239000008199 coating composition Substances 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 125000004122 cyclic group Chemical group 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 229910052746 lanthanum Inorganic materials 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 235000002639 sodium chloride Nutrition 0.000 description 2
- 229910052938 sodium sulfate Inorganic materials 0.000 description 2
- 235000011152 sodium sulphate Nutrition 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 229910002543 FeCrAlY Inorganic materials 0.000 description 1
- 229910001260 Pt alloy Inorganic materials 0.000 description 1
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 229910052708 sodium Inorganic materials 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000009718 spray deposition Methods 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- 238000005406 washing Methods 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
- 230000004584 weight gain Effects 0.000 description 1
- 235000019786 weight gain Nutrition 0.000 description 1
Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
- F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
- F01D5/12—Blades
- F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
- F01D5/288—Protective coatings for blades
-
- 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
-
- 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
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
- Y02T50/00—Aeronautics or air transport
- Y02T50/60—Efficient propulsion technologies, e.g. for aircraft
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12778—Alternative base metals from diverse categories
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12875—Platinum group metal-base component
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12944—Ni-base component
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Engineering & Computer Science (AREA)
- Coating By Spraying Or Casting (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Physical Vapour Deposition (AREA)
- Turbine Rotor Nozzle Sealing (AREA)
Description
Den foreliggende oppfinnelse vedrører en belegglegering The present invention relates to a coating alloy
av MCrAlY-typen med økt varmkorrosjonsbestandighet for belegging av gjenstander av nikkel- og koboltlegeringer, inneholdende 8-30 vektprosent krom, 5-15 vektprosent aluminium, 0-1 vektprosent reaktivt metall i form av yttrium, scandium, thorium eller et annet sjeldent jordmetall og resten, bortsatt fra forurensninger, nikkel, kobolt eller nikkel-kobolt. of the MCrAlY type with increased hot corrosion resistance for coating objects made of nickel and cobalt alloys, containing 8-30 weight percent chromium, 5-15 weight percent aluminum, 0-1 weight percent reactive metal in the form of yttrium, scandium, thorium or another rare earth metal and the rest, excluding impurities, nickel, cobalt or nickel-cobalt.
Det er kjent at superlegeringer i moderne jetmotorer er utsatt for oksydasjonserosjon og varmkorrosjon ved meget høye temperaturer og at det er vanlig praksis å overtrekke super-legeringene med et belegg som er forskjellig fra og som har større oksydasjonserosjons- og korrosjonsbestandighet enn den underliggende legering. It is known that superalloys in modern jet engines are subject to oxidation erosion and hot corrosion at very high temperatures and that it is common practice to coat the superalloys with a coating that is different from and has greater oxidation erosion and corrosion resistance than the underlying alloy.
Generelt er det to hovedtyper belegg: 1) aluminidbelegg, såsom de som er beskrevet i et av US-patentskriftene 3.102.044, 3.677.789 og 3.692.554, hvor det dannes aluminider ved reaksjon med eller diffusjon av et belegg på den underliggende flate, og 2) belegg såsom de av MCrAlY-typen, f.eks. NiCrAlY beskrevet i US-patentskrift 3.754.903, CoCrAlY beskrevet i US-patentskrift 3.676.085, NiCoCrAlY beskrevet i US-patentskrift 3.928.026 samt FeCrAlY beskrevet i US-patentskrift 3.542.530. Særlig anvendbare MCrAlY-overtrekk er de som hovedsakelig består av ca. 8-3 0 vektprosent krom, 5-15 vektprosent aluminium, opptil 1 vektprosent reaktivt metall i form av yttrium, scandium, thorium eller lanthan eller et annet sjeldent jordmetall, mens resten består av nikkel, kobolt eller nikkel-kobolt, fortrinnsvis på-ført i en tykkelse på ca. 0,012-0,015 cm. In general, there are two main types of coatings: 1) aluminide coatings, such as those described in one of US patents 3,102,044, 3,677,789 and 3,692,554, where aluminides are formed by reaction with or diffusion of a coating onto the underlying surface , and 2) coatings such as those of the MCrAlY type, e.g. NiCrAlY described in US patent 3,754,903, CoCrAlY described in US patent 3,676,085, NiCoCrAlY described in US patent 3,928,026 and FeCrAlY described in US patent 3,542,530. Particularly applicable MCrAlY coatings are those which mainly consist of approx. 8-30% by weight chromium, 5-15% by weight aluminium, up to 1% by weight reactive metal in the form of yttrium, scandium, thorium or lanthanum or another rare earth metal, while the rest consists of nickel, cobalt or nickel-cobalt, preferably applied in a thickness of approx. 0.012-0.015 cm.
I motsetning til overtrekkene frembringes aluminidbeleggene typisk ved å la aluminium reagere med den deoksyderte overflate av gjenstanden som skal beskyttes. Aluminidlaget dannes som en barrieresone med varierende bestanddelskonsentrasjon avhengig av forbruket av bestanddelene i underlaget. Dette aluminidlaget på sin side oksyderes til dannelse av det inerte barriereoksyd. Ifølge US-patentskrifter 3.677.789 og 3.692.554 påføres det et separat lag av metall tilhørende platinagruppen før aluminium-diffusjonsbehandlingen. Men som følge av den komplekse natur til de fleste kjente legeringer og idet beleggsammensetningen på disse delvis kommer fra bestanddelene i de underliggende legeringer er det vanskelig å regulere beleggets sammensetning slik at det dannes et egnet barriereoksyd. I tillegg ligger det i diffusjonsteknikken at det dannete belegg er uhomogent, og når det gjelder innhold av f.eks. metaller tilhørende platinagruppen, fremkommer det en høy konsentrasjon av metallet tilhørende platinagruppen på overflaten. En slik gradient er selvfølgelig ufordelaktig idet beleggets effektivitet avtar under bruk når dets sammensetning forandres. In contrast to the coatings, the aluminide coatings are typically produced by allowing aluminum to react with the deoxidized surface of the object to be protected. The aluminide layer is formed as a barrier zone with varying component concentration depending on the consumption of the components in the substrate. This aluminide layer, in turn, is oxidized to form the inert barrier oxide. According to US patents 3,677,789 and 3,692,554, a separate layer of metal belonging to the platinum group is applied before the aluminum diffusion treatment. However, due to the complex nature of most known alloys and as the coating composition on these partly comes from the constituents of the underlying alloys, it is difficult to regulate the composition of the coating so that a suitable barrier oxide is formed. In addition, it is inherent in the diffusion technique that the coating formed is inhomogeneous, and when it comes to content of e.g. metals belonging to the platinum group, a high concentration of the metal belonging to the platinum group appears on the surface. Such a gradient is of course disadvantageous as the coating's effectiveness decreases during use when its composition changes.
Selv om noen kjente beleggsammensetninger har representert forbedringer i forhold til tidligere legeringssammensetninger har det fortsatt vært behov for ytterligere forbedringer, særlig f.eks. når det gjelder varmkorrosjonsbestandighet. Although some known coating compositions have represented improvements in relation to previous alloy compositions, there has still been a need for further improvements, especially e.g. in terms of hot corrosion resistance.
Legeringen ifølge oppfinnelsen er kjennetegnet ved at den for økning av varmkorrosjonsbestandigheten er tilsatt 3-12 vektprosent av et edelt metall i form av platina eller rhodium som legeririgsbestanddel. The alloy according to the invention is characterized by the fact that, to increase the hot corrosion resistance, 3-12 percent by weight of a precious metal in the form of platinum or rhodium has been added as an alloy component.
Anvendelsen av det edle metall som en legeringsbestanddel resulterer i en stort sett jevn dispergering av dette i legeringen og homogeniteten som er kjennetegnene for overtrekks-beleggene av MCrAlY-typen bibeholdes således. The use of the noble metal as an alloy component results in a largely uniform dispersion of this in the alloy and the homogeneity which is the characteristic of the MCrAlY-type coating is thus maintained.
Ifølge en foretrukket sammensetning er det reaktive metall yttrium og det edle metall 5-10 vektprosent platina. I en annen sammensetning er det reaktive metall yttrium og det edle metall 5 vektprosent rhodium. According to a preferred composition, the reactive metal is yttrium and the noble metal is 5-10 weight percent platinum. In another composition, the reactive metal is yttrium and the noble metal is 5% by weight rhodium.
Oppfinnelsen vil bli nærmere beskrevet i den etterfølgende detaljerte beskrivelse under henvisning til de medfølgende teg-ninger, hvori: Fig. 1 er et diagram som viser sulfidiseringsegenskapene for ulike NiCrAl-legeringer ved 1000°C. Fig. 2 og 3 er diagrammer som viser oksydasjonsegenskapene for ulike NiCrAl-legeringer ved henholdsvis 1100 og 1200°C i luft. Fig. 4 er et diagram som viser varmkorrosjonsegenskapene for ulike CoCrAlY- og NiCrAlY-legeringer ved 955°C og 2,0 mg.cm<-2 >Na2S04. Fig. 5 er et diagram som viser varmkorrosjonsegenskapene for NiCrAlY-legeringer ved 955°C og 0,5 mg.cm <2>Na^O^. The invention will be described in more detail in the following detailed description with reference to the accompanying drawings, in which: Fig. 1 is a diagram showing the sulphidation properties of various NiCrAl alloys at 1000°C. Figs 2 and 3 are diagrams showing the oxidation properties of various NiCrAl alloys at 1100 and 1200°C respectively in air. Fig. 4 is a diagram showing the hot corrosion properties of various CoCrAlY and NiCrAlY alloys at 955°C and 2.0 mg.cm<-2 >Na2SO4. Fig. 5 is a diagram showing the hot corrosion properties of NiCrAlY alloys at 955°C and 0.5 mg.cm <2>Na^O^.
Legeringene ifølge oppfinnelsen oppviser særlig god varmkorrosjonsbestandighet og anses for å være særlig anvendbare som belegg på moderne superlegeringer. Legeringene ifølge oppfinnelsen er korrosjonsbestandige i seg selv, og deres beskyttende virkning er ikke avhengig av en reaksjon med det underliggende materiale. I tillegg er disse legeringer homogene helt igjennom og vil således utøve deres beskyttende virkning mer kontinuerlig og jevnt enn aluminidbeleggene gjør. The alloys according to the invention show particularly good hot corrosion resistance and are considered to be particularly useful as coatings on modern superalloys. The alloys according to the invention are corrosion resistant in themselves, and their protective effect does not depend on a reaction with the underlying material. In addition, these alloys are homogeneous throughout and will thus exert their protective effect more continuously and evenly than the aluminide coatings do.
I en foretrukket legering anvendes det 0,5 vektprosent yttrium og 5-10 vektprosent platina. In a preferred alloy, 0.5% by weight of yttrium and 5-10% by weight of platinum are used.
Det var overraskende å finne at tilsetning som legerings-bestanddeler av nærmere angitte mengder platina eller rhodium til beleggene av MCrAlY-typen ikke bare ville øke sterkt sul-fidiseringsbestandigheten, men også selv uten nærvær av de reaktive metaller (Y, Sc, Th, La eller de andre sjeldne jordmetaller) som vanligvis frembringer oksydadhesjon til underlaget, ville frembringe ytterligere oksydadhesjon. It was surprising to find that the addition as alloying constituents of specified amounts of platinum or rhodium to the MCrAlY-type coatings would not only greatly increase the sulphidation resistance, but also even without the presence of the reactive metals (Y, Sc, Th, La or the other rare earth metals) that normally produce oxide adhesion to the substrate would produce additional oxide adhesion.
Når det gjelder fremgangsmåtene hvorved legeringen kan på-føres som et belegg på overflaten som skal beskyttes utelukker nærværet av platina eller rhodium i belegglegeringen som følge av platinas eller rhodiums lave damptrykk generelt bruken av dampbeleggingsteknikk. Andre teknikker er imidlertid effektive for å oppnå det riktige sammensatte belegg. Det er f.eks. iakttatt at beleggene kan avsettes ved hjelp av en teknikk som om-fatter samtidig dampavsetning av MCrAlY og spruteavsetning av platina eller rhodium. Som et alternativ kan beleggene frembringes ved hjelp av plasmasprøyte-teknikk. As regards the methods by which the alloy can be applied as a coating to the surface to be protected, the presence of platinum or rhodium in the coating alloy, as a result of platinum's or rhodium's low vapor pressure, generally precludes the use of vapor coating techniques. However, other techniques are effective in achieving the correct composite coating. It is e.g. observed that the coatings can be deposited using a technique which includes simultaneous vapor deposition of MCrAlY and spray deposition of platinum or rhodium. As an alternative, the coatings can be produced using the plasma spray technique.
Oppfinnelsen vil bli nærmere forklart ved hjelp av følgende eksempler: The invention will be explained in more detail using the following examples:
Eksempel 1 Example 1
Legeringer av Ni-8Cr-6Al med legeringstilsetninger av platina og rhodium ble fremstilt ved konvensjonell dråpestøpings-teknikk ved hjelp av lysbuesmelting. Prøvestykker med de sammensetninger som er angitt i diagrammet i fig. 1 hadde dimensjoner på 1 cm x 1 cm x 0,2 cm og ble underkastet varmkorrosjonsforsøk på følgende måte: Prøvestykkene av legeringene ble sprøytet med en vandig løsning av Na2SO^, tørket og veiet. Etter at det var oppnådd et belegg på 0,5 mg.cm Na2S04 ble de oksydert i 20 timer ved 1000°C i en 02 atmosfære i termisk balanse. Prøvestykkets vekt ble registrert kontinuerlig som en funksjon av tiden, og vektforandringene ble omdannet til vektøkning pr. overflate-arealenhet og er vist i fig. 1. Alloys of Ni-8Cr-6Al with alloying additions of platinum and rhodium were produced by conventional drop casting technique using arc melting. Test pieces with the compositions indicated in the diagram in fig. 1 had dimensions of 1 cm x 1 cm x 0.2 cm and was subjected to hot corrosion tests in the following manner: The specimens of the alloys were sprayed with an aqueous solution of Na 2 SO 4 , dried and weighed. After a coating of 0.5 mg.cm Na2SO4 had been obtained, they were oxidized for 20 hours at 1000°C in an O2 atmosphere in thermal balance. The weight of the sample was recorded continuously as a function of time, and the weight changes were converted into weight gain per unit surface area and is shown in fig. 1.
Det fremgår at tilsetningen av 2,5 vektprosent Pt ikke bed-ret egenskapene til Ni-8Cr-6Al-legeringen i dette forsøk. Men en vesentlig forbedring ble oppnådd når det blir tilsatt 5 eller 10 vektprosent Pt. Prøvestykker av Ni-8Cr-6Al-5Rh-legeringen tilsvarte omtrent 10 Pt-legeringen. It appears that the addition of 2.5% by weight of Pt did not improve the properties of the Ni-8Cr-6Al alloy in this experiment. But a significant improvement was achieved when 5 or 10 percent by weight Pt is added. Specimens of the Ni-8Cr-6Al-5Rh alloy were approximately equivalent to the 10 Pt alloy.
Eksempel 2 Example 2
Prøvestykker ble fremstilt som ifølge eksempel 1 med de sammensetninger som er vist i fig. 2 og 3. Prøvestykkene ble utsatt for cykliske oksydasjonsforsøk ved høy temperatur, og overraskende viste det seg at de som inneholdt platina eller rhodium hadde bedre oksydadhesjon for aluminiumoksydet som ble dannet på legeringene. Det fremgår at legeringene med 5 eller 10 vektprosent Pt er bedre enn legeringen med 2,5 vektprosent Pt som på sin side er betydelig bedre enn den umodifiserte legering. Oksydadhesjon på en Ni-8Cr-6Al-5Rh-legering ved 1200°C ble funnet å være like god som for Ni-8Cr-6Al-10Pt-legeringen ved samme temperatur. Test pieces were prepared as according to example 1 with the compositions shown in fig. 2 and 3. The test pieces were exposed to cyclic oxidation tests at high temperature, and surprisingly it turned out that those containing platinum or rhodium had better oxide adhesion for the aluminum oxide that was formed on the alloys. It appears that the alloys with 5 or 10 weight percent Pt are better than the alloy with 2.5 weight percent Pt, which in turn is significantly better than the unmodified alloy. Oxide adhesion on a Ni-8Cr-6Al-5Rh alloy at 1200°C was found to be as good as that of the Ni-8Cr-6Al-10Pt alloy at the same temperature.
Eksempel 3 Example 3
Det ble fremstilt legeringsprøvestykker med dimensjoner Alloy test pieces with dimensions were produced
på 1 cm x 0,8 cm x 0,1-0,2 cm og sammensetninger Ni-17Cr-12Al-0,5Y, Ni-17Cr-12Al-5Rh-0,5Y, Ni-17Cr-12Al-10Pt-0,5Y, Co-17Cr-11A1-0,5Y, Co-17Cr-llAl-5Rh-0,5Y samt Co-17Cr-llAl-10Pt-0,5Y. Prøvestykkene ble målt og veiet og deretter belagt med 0,5- of 1 cm x 0.8 cm x 0.1-0.2 cm and compositions Ni-17Cr-12Al-0.5Y, Ni-17Cr-12Al-5Rh-0.5Y, Ni-17Cr-12Al-10Pt-0 ,5Y, Co-17Cr-11A1-0.5Y, Co-17Cr-11Al-5Rh-0.5Y and Co-17Cr-11Al-10Pt-0.5Y. The test pieces were measured and weighed and then coated with 0.5-
2,0 mg/cm 2 Na2S04. De ble deretter underkastet opptil 14 cykler som hver bestod i oksydasjon i luft i 20 timer ved 955°C, av-kjøling til romtemperatur, vasking og veiing igjen. Dette ble gjentatt til det oppstod svikt. Resultatene som ble oppnådd i ett sett forsøk ved 955°C under anvendelse av 2 mg/cm<2> salt er vist i fig. 4. Selv om CoCrAlY i grunnen er mer bestandig mot varmkorrosjon enn NiCrAlY, fremgår det at tilsetning av enten Pt eller Rh til enten CoCrAlY eller NiCrAlY sterkt bedrer deres varmkorrosjonsbestandighet. 2.0 mg/cm 2 Na 2 SO 4 . They were then subjected to up to 14 cycles each consisting of oxidation in air for 20 hours at 955°C, cooling to room temperature, washing and weighing again. This was repeated until failure occurred. The results obtained in one set of experiments at 955°C using 2 mg/cm<2> salt are shown in fig. 4. Although CoCrAlY is basically more resistant to hot corrosion than NiCrAlY, it appears that the addition of either Pt or Rh to either CoCrAlY or NiCrAlY greatly improves their hot corrosion resistance.
Eksempel 4 Example 4
Erosjonsstenger av Ni-17Cr-12Al-0,5Y, Ni-17Cr-12Al-5Rh-0,5Y, Ni-17Cr-12Al-5Pt-0,5Y samt Ni-17Cr-12Al-10Pt-0,5Y ble vurdert i en cyklisk varmkorrosjonsbrenner-rigg ved 955°C hvor det ble anvendt 35 ppm sjøsalt tilsatt til brennstoffet før forbrenningen. Alvorlige angrep på typen av både NiCrAlY-grunnsammensetningen og den rhodium-modifiserte sammensetning oppstod etter 110 timer. Varmsonesvikter ble iakttatt etter mellom 300 og 4 00 timer for begge disse stenger, idet det rhodium-modifiserte prøvestykke klarte seg litt lenger enn grunnsammensetningen. Selv om den rhodium-modifiserte sammensetning oppviste litt forbedring sammenliknet med grunnlegeringen i dette forsøk var typen av dens svikt uvanlig og gjorde disse resultater noe usikre og ikke overbevisende. Derimot viste de platina-modifiserte sammensetninger seg å være mye mer resistent overfor varmkorrosjon enn grunnsammensetningen. For disse sammensetninger var det intet tegn til svikt etter opptil 675 timer da forsøkene ble avsluttet. Erosion bars of Ni-17Cr-12Al-0.5Y, Ni-17Cr-12Al-5Rh-0.5Y, Ni-17Cr-12Al-5Pt-0.5Y and Ni-17Cr-12Al-10Pt-0.5Y were evaluated in a cyclic hot corrosion burner rig at 955°C where 35 ppm sea salt added to the fuel before combustion was used. Severe attack on the type of both the NiCrAlY base composition and the rhodium-modified composition occurred after 110 hours. Hot zone failures were observed after between 300 and 400 hours for both of these bars, with the rhodium-modified specimen surviving slightly longer than the basic composition. Although the rhodium-modified composition showed some improvement over the base alloy in this test, the nature of its failure was unusual and made these results somewhat uncertain and inconclusive. In contrast, the platinum-modified compositions proved to be much more resistant to hot corrosion than the base composition. For these compositions there was no sign of failure after up to 675 hours when the tests were terminated.
Claims (3)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US487074A US3918139A (en) | 1974-07-10 | 1974-07-10 | MCrAlY type coating alloy |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| NO752355L NO752355L (en) | 1976-01-13 |
| NO141371B true NO141371B (en) | 1979-11-19 |
| NO141371C NO141371C (en) | 1980-02-27 |
Family
ID=23934299
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO75752355A NO141371C (en) | 1974-07-10 | 1975-06-30 | MCRALY TYPE COATING. |
Country Status (13)
| Country | Link |
|---|---|
| US (1) | US3918139A (en) |
| JP (1) | JPS5842255B2 (en) |
| BR (1) | BR7504327A (en) |
| CA (1) | CA1158075A (en) |
| CH (1) | CH606455A5 (en) |
| DE (1) | DE2530197C2 (en) |
| FR (1) | FR2277902A1 (en) |
| GB (1) | GB1500780A (en) |
| IL (1) | IL47407A (en) |
| IN (1) | IN144076B (en) |
| IT (1) | IT1039467B (en) |
| NO (1) | NO141371C (en) |
| SE (1) | SE410477B (en) |
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-
1974
- 1974-07-10 US US487074A patent/US3918139A/en not_active Expired - Lifetime
-
1975
- 1975-05-23 GB GB23056/75A patent/GB1500780A/en not_active Expired
- 1975-05-28 IN IN1079/CAL/1975A patent/IN144076B/en unknown
- 1975-06-03 IL IL47407A patent/IL47407A/en unknown
- 1975-06-04 CH CH721275A patent/CH606455A5/xx not_active IP Right Cessation
- 1975-06-19 SE SE7507095A patent/SE410477B/en unknown
- 1975-06-26 CA CA000230272A patent/CA1158075A/en not_active Expired
- 1975-06-27 IT IT24839/75A patent/IT1039467B/en active
- 1975-06-30 NO NO75752355A patent/NO141371C/en unknown
- 1975-07-03 FR FR7520876A patent/FR2277902A1/en active Granted
- 1975-07-05 DE DE2530197A patent/DE2530197C2/en not_active Expired
- 1975-07-09 JP JP50084341A patent/JPS5842255B2/en not_active Expired
- 1975-07-09 BR BR7504327*A patent/BR7504327A/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| US3918139A (en) | 1975-11-11 |
| CA1158075A (en) | 1983-12-06 |
| GB1500780A (en) | 1978-02-08 |
| SE410477B (en) | 1979-10-15 |
| FR2277902A1 (en) | 1976-02-06 |
| FR2277902B1 (en) | 1978-07-28 |
| DE2530197C2 (en) | 1983-02-03 |
| NO752355L (en) | 1976-01-13 |
| IN144076B (en) | 1978-03-18 |
| AU8156075A (en) | 1976-12-02 |
| IL47407A (en) | 1977-08-31 |
| NO141371C (en) | 1980-02-27 |
| SE7507095L (en) | 1976-01-12 |
| JPS5842255B2 (en) | 1983-09-19 |
| IT1039467B (en) | 1979-12-10 |
| BR7504327A (en) | 1976-07-06 |
| CH606455A5 (en) | 1978-10-31 |
| IL47407A0 (en) | 1975-08-31 |
| JPS5130530A (en) | 1976-03-15 |
| DE2530197A1 (en) | 1976-01-29 |
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