Classifications

• • 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
  • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
  • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
  • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
  • C23C8/10—Oxidising
• • 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
  • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
  • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
  • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
  • C22C32/0026—Matrix based on Ni, Co, Cr or alloys thereof

Definitions

• This invention relates to nickel base alloys and, more particularly, to a solid solution type nickel base alloy of improved dynamic oxidation resistance.
• the alloy of the copending application provides an unexpected improvement in oxidation resistance over similar known alloys. This improvement is now seen to be significant when used in a relatively static application such as in a furnace. However, it has been recognized that such an alloy requires further improvement for use under dynamic oxidation conditions.
• One example of a use under dynamic conditions is as a combustor material in a gas turbine engine where there is a rapid flow of combustion gases including excess oxygen.
• a principal object of the present invention is to provide an alloy of the type described in the above identified c0- pending application but having improved oxidation resistance under dynamic oxidation conditions as well as under static oxidation conditions.
• Another object is to provide such an alloy which, under dynamic oxidation conditions, will form an improved surface as a thermal reaction product in an oxidizing atmosphere to resist further oxidation of the alloy and to act as a barrier to internal oxidation.
• Still another object is to provide an article including such an alloy and having an oxidation resistant surface.
• the present invention provides an improved nickel base alloy of the solution strengthened type from which an improved article can be produced, the alloy consisting essentially of, by weight, 20-23% Cr; 8-10% Mo; 17-20% Fe; up to 0.15% C; up to 2% W; 0.05 to less than 0.3% La; 0.56% of the spinel forming elements selected from the group Co and Mn, the Co when selected being in the range of 13% and the Mn when selected 3,383,206 Patented May 14, 1968 being in the range of 0.53% with the balance nickel and incidental impurities.
• the alloy of the present invention includes O.1-0.2% La along with 1.5-2.5 Co and 0.5- 1.5% Mn.
• the spinel formers manganese and cobalt were identified as impurities in the composition of the alloy of the copending application and of the alloy of the Spendelow et al. patent. They were not specifically included nor were their amounts controlled. In the Spendelow et a1. patent, cobalt is included as an impurity generally at less than 1% and in no event greater than about 2.5%; manganese is listed as an impurity permissible up to about 1% along with silicon and the like.
• Example 1 in Table II The 1% Mn variation shown as Example 1 in Table II was successfully reduced to sheet and subjected to extensive oxidation evaluation and some mechanical testing.
• Example B has signii'icantly improved oxidation resistance under static conditions over the known alloy, represented by Example A.
• Table III gives a comparison of Examples A and B with each other and with the preferred form of the alloy of the present invention, represented by Example 1, under static oxidation resistance.
• Example B has oxidation resistance under static conditions better than does Example 1
• the alloy of the present invention shown as Example 1 in Table III has static oxidation resistance at least equal to that of Example A.
• Example A experienced a lower weight gain at 2000 F. after 400 and 1000 hours static exposure, nevertheless, the reaction product surface of Example A spalled upon cooling. The surface of Examples B and 1 did not.
• the effectiveness of the reaction product surface to prevent internal oxidation is significantly greater in Alloys B and 1.
• the alloy of the present invention has good oxidation resistance under static conditions, in general better than that of Example A.
• Example 1 TABLE V.DYNA. ⁇ 1IC OXIDATION TESTING IN FLAME TU N'EL [Average after 1,000 hours] 10 Avg. Depth Internal Oxi- Avg. width Example Temp, F. dation (mils/side) loss (m)i1s/ side Front Rear
• the alloy of the present invention particularly represented by Example 1 is characterized by a combination of good static oxidation resistance and significantly better dynamic oxidation resistance.
• the dynamic oxidation testing was conducted as thermal cyclic evaluations performed on 2.0" x 0.375" specimens.
• the surface of all specimens to be used for oxidation testing were prepared by mechanical abrasion up to and including 600 grit paper. Final surface preparation consisted of vapor blasting the surface of the specimen using 1250 grit abrasive.
• the specimens were supported in one end of a flame tunnel in a fire-brick with the majority of the specimen exposed to an uninterrupted gas/air flow of about 100 lbs./in. /hr.
• the tests were performed by cycling from 20 minutes at temperature followed by a 15 second blast of cooling air to reduce the specimen to a temperature of 1000 F. The entire cooling and heating cycle took approximately 30 seconds. Thus virtually the whole test period was spent at temperature. Weight and dimensional changes as shown in the above tables, as well as metallographic examination were used to determine the amount of oxidation.
• the following tensile properties of the alloy of the present invention particularly as represented by Example 1 were obtained on 60 mil sheet.
• Example The data of Table IV shows that the alloy of the present invention experiences a significantly lower weight loss than does either Examples A or B. More significantly in connection with its application as a useful article such as a combnstor in a gas turbine engine, the alloy of Example 1 has greatly improved resistance to internal oxidation compared with Examples A and B. This is too difiicult to reduce from an ingot.
• An improved nickel base alloy of the solution strengthened type consisting essentially of, by weight, 20-23% Cr; 8-10% Mo; 17-20% Fe; up to about 0.15% C; up to about 2% W; 0.05 to less than 0.3% La; 0.5-6% of the spinel forming elements selected from the group consisting of Co and Mn, the C0 when selected being in the range of 1-3% and the Mn when selected being in the range 0.5-3%; with the balance nickel and incidental impurities.
• An improved nickel base alloy of the solution strengthened type consisting essentially of, by weight, 20-23% Cr; 8-10% Mo; 17-20% Fe; up to about 0.15% C; up to about 2% W; 0.05 to less than 0.3% La; 1-3% Co; 0.05-3% Mn; up to about 1% Si; with the balance nickel and incidental impurities.
• An improved nickel base alloy of the solution strengthened type consisting essentially of, by weight, 20-23% Cr; 8-10% ⁇ Mo; 17-20% Fe; 0.05-0.15% C;
• An article including an alloy consisting essentially of, by weight, 20-23% Cr; 8-10% Mo; 17-20% Fe; up to about 0.15% C; up to about 2% W; 0.05 to less than 0.3% La; 0.5-6% of the spinel forming elements selected from the group consisting of Co and Mn, the Co when selected being in the range of 1-3% and the Mn when selected being in the range of 0.5-3%; with the balance nickel and incidental impurities; the alloy having a surface bonded with the alloy and comprising an integral combination of Cr and La oxides and a spinel of the Ni( Cr, Mn, Co) O type.
• a combustion means for a gas turbine engine including an alloy consisting essentially of, by weight, 20-23% Cr; 8-10% Mo; 17-20% Fe; up to about 0.15% C; up to about 2% W; 0.05 to less than 0.3% La; l-3% Co; 0.05-3% Mn; up to about 1% Si; with the balance nickel and incidental impurities; the alloy having a surface bonded with the alloy and comprising an integral combination of Cr and La oxides and a spinel of the Ni(Cr, Mn, Co) O type.

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• Chemical & Material Sciences (AREA)
• Engineering & Computer Science (AREA)
• Materials Engineering (AREA)
• Mechanical Engineering (AREA)
• Metallurgy (AREA)
• Organic Chemistry (AREA)
• Chemical Kinetics & Catalysis (AREA)
• Powder Metallurgy (AREA)
• Cell Electrode Carriers And Collectors (AREA)
• Inert Electrodes (AREA)

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Cited By (3)

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Citations (3)

• 1965
  • 1965-10-11 US US494966A patent/US3383206A/en not_active Expired - Lifetime
• 1966
  • 1966-06-29 GB GB29198/66A patent/GB1107669A/en not_active Expired
  • 1966-07-05 DE DE19661533258 patent/DE1533258A1/de active Pending
  • 1966-07-11 BE BE683945D patent/BE683945A/xx unknown

Patent Citations (3)

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