United States of America As Represented by the Secretary of the Air Force

Dennis M Dimiduk

Young-Won Kim

Madan G Mendiratta

P R Subramanian

Triplicane A Parthasarathy

Sheldon L Semiatin

Madan Mendiratta

Michael D Uchic

David S Lee

Paul A McQuay

A dual function indenter for use in a nanoindentation system is disclosed. The indenter of the present invention includes an indentation tip having a machined flat at its distal end forming a compression platen. A sharp imaging probe tip adjacent the machined flat extends parallel to the centerline axis of the indentation tip. The sharp imaging probe tip extends beyond the surface of the machined flat for in situ scanning/imaging of the sample surface.

Dual function indenter

A method for enhancing the oxidation resistance of substrates fabricated from metallic molybdenum and alloys containing at least 50% molybdenum which comprises depositing silicon on the surface of the substrate under conditions which cause the formation of an outer layer of MoSi . Also disclosed is a method for enhancing the oxidation resistance of other substrates, such as carbon-carbon and metals and alloys which show minimal reaction with molybdenum under the coating conditions, which comprises depositing a layer of molybdenum on the surface, then depositing silicon on the molybdenum layer under conditions which cause the formation of an outer layer of MoSi .

Oxidation protective coating for Mo-Si-B alloys

Methods are presented to produce duplex (DP) microstructures, nearly lamellar (NL) microstructures, and fully TMT lamellar (TMTL) microstructures in gamma titanium aluminide alloy articles. The key step for obtaining a specific type of microstructure is the post-hot work annealing treatment at a temperature in a specific range for the desired microstructure. The annealing temperatures range from T &plus;100&deg; C. to T&agr;&minus;25&deg; C. for duplex (DP) microstructures, from T&agr;&minus;25&deg; C. to T&agr;&minus;5&deg; C. for nearly lamellar (NL) microstructures, and from T&agr; to T&agr;&plus;60&deg; C. for fully TMT lamellar (TMTL) microstructures, where T is the titanium-aluminum eutectoid temperature of the alloy and T&agr; is the alpha transus temperature of the alloy. The times required for producing specific microstructures range from 2 min to 15 hours depending on microstructural type, alloy composition, annealing temperature selected, material section size, and desired grain-size. The heating rate to the post-hot work annealing treatment is critical and must be fast enough to avoid compositional segregation (in the two-phase field) and uneven grain growth. Cooling schemes and rates after the annealing treatments are determined according to the microstructural features of interest, and their stability.

Method to produce gamma titanium aluminide articles having improved properties

Gamma titanium aluminide alloys having the composition Ti-(45.5-47.5)Al-(0-3.0)X-(1-5)Y-(0.05-1.0)W, where X is Cr, Mn or any combination thereof, and Y is Nb, Ta or any combination thereof (at %), are treated to provide specific microstructures. To obtain duplex microstructures, the annealing temperature (T.sub.a) range is the eutectoid temperature (T.sub.e)+100.degree. C. to the alpha transus temperature (T.sub..alpha.)-30.degree. C.; to obtain nearly lamellar microstructures, the annealing temperature range is T.sub..alpha. -20.degree. C. to T.sub..alpha. -1.degree. C.; to obtain fully lamellar microstructures, the annealing temperature range is T.sub..alpha. to T.sub..alpha. +50.degree. C. The times required for producing these microstructures range from 0.25 to 15 hours, depending on the desired microstructure, alloy composition, annealing temperature selected, material section size and grain size desired. The cooling schemes and rates after annealing depend mainly on the microstructure type and stability; for duplex and nearly lamellar microstructures, the initial cooling rate is 5.degree. to 1000.degree. C./min, while for fully lamellar microstructure, the the initial cooling rate is 5.degree. to 100.degree. C./min. The article can be cooled at the initial rate directly to the aging temperature; alternatively, the article can be cooled at the initial rate down to a temperature between room temperature and the annealing temperature, then cooled to room temperature at a cooling rate between the initial rate and water quenching, after which the article is aged. Following annealing, the article is aged at a temperature in the range of 700.degree. C. to 1050.degree. C. for about 4 to 150 hours.

Method to produce gamma titanium aluminide articles having improved

High temperature melting niobium-titanium-chromium-aluminum-silicon alloys having a wide range of desirable microstructures, excellent microstructural and morphological properties, superior oxidation resistance at temperatures from 1000.degree. C. to 1500.degree. C., and good low temperature toughness and good high temperature strength and creep resistance are described which comprise generally two- or three-or four-phase alloys systems having compositions (31-41)Nb-(26-34)Ti-(8-10)Cr-(6-12)Al-(9-18)Si. Two-phase beta+Nb.sub.5 Si.sub.3 -base alloys can be obtained by increasing the Nb/Ti ratio, while three-phase beta+Nb.sub.5 Si.sub.3 -base+Ti.sub.5 Si.sub.3 -base alloys or four-phase beta+Nb.sub.5 Si.sub.3 -base+Ti.sub.5 Si.sub.3 -base +Ti.sub.3 Si-base alloys can be obtained by decreasing the Nb/Ti ratio.

High temperature melting niobium-titanium-chromium-aluminum-silicon

High temperature melting molybdenum-chromium-silicon alloys having good high temperature strength and specific stiffness are described which comprise Mo--Cr--Si alloys in the Mo-rich (Mo, Cr)--(Mo, Cr).sub.3 Si two-phase field.

High temperature melting molybdenum-chromium-silicon alloys

A heat treatment method for producing moderate .alpha. grain size (50-250 .mu.m) fully lamellar, microstructures in thin cross section near-.gamma. titanium aluminide alloy products is described, wherein a wrought, fine y grain starting microstructure is heated at a temperature high in the two-phase .alpha.+.gamma. phase field and 30-60.degree. C. below the .alpha. transus temperature to produce a structure of small equiaxed .alpha. grains (about 25 .mu.m dim) and fine .gamma. phase grains, which is then briefly heated to a temperature in the single-phase .alpha. field in order to complete dissolution of remnant .gamma. grains and to minimize growth of .alpha. grains. The material is then cooled to transform the microstructure to fully lamellar .alpha..sub.2 +.gamma..

Method for heat treating titanium aluminide alloys

Gamma titanium aluminide alloys having the composition Ti--(45.5-47.5)Al--(0-3.0)X--(1-5)Y--(0.05-1.0)W, where X is Cr, Mn or any combination thereof, and Y is Nb, Ta or any combination thereof (at %), are treated to provide specific microstructures. To obtain duplex microstructures, the annealing temperature (T.sub.a) range is the eutectoid temperature (T.sub.e)+100.degree. C. to the alpha transus temperature (T.sub..alpha.)-30.degree. C.; to obtain nearly lamellar microstructures, the annealing temperature range is T.sub..alpha. -20.degree. C. to T.sub..alpha. -1.degree. C.; to obtain fully lamellar microstructures, the annealing temperature range is T.sub..alpha. to T.sub..alpha. +50.degree. C. The times required for producing these microstructures range from 0.25 to 15 hours, depending on the desired microstructure, alloy composition, annealing temperature selected, material section size and grain size desired. The cooling schemes and rates after annealing depend mainly on the microstructure type and stability; for duplex and nearly lamellar microstructures, the initial cooling rate is 5.degree. to 1000.degree. C./min, while for fully lamellar microstructure, the initial cooling rate is 5.degree. to 100.degree. C./min. The article can be cooled at the initial rate directly to the aging temperature; alternatively, the article can be cooled at the initial rate down to a temperature between room temperature and the annealing temperature, then cooled to room temperature at a cooling rate between the initial rate and water quenching, after which the article is aged. Following annealing, the article is aged at a temperature in the range of 700.degree. C. to 1050.degree. C. for about 4 to 150 hours.

Gamma titanium aluminide alloy articles having improved properties are produced by the following methods: The first of these methods comprises the steps of: (a) heat treating an alloy billet or preform at a temperature in the approximate range of T.sub..alpha. to T.sub..alpha. +100.degree. C. for about 0.5 to 8 hours, (b) shaping the billet at a temperature between T.sub..alpha. -30.degree. C. and T.sub..alpha. to produce a shaped article, and (c) aging the thus-shaped article at a temperature between about 750.degree. and 1050.degree. C. for about 2 to 24 hours. The second method comprises (a) rapidly preheating an alloy preform to a temperature in the approximate range of T.sub..alpha. to T.sub..alpha. +100.degree. C., (b) shaping the billet at a temperature between T.sub..alpha. and T.sub..alpha. +100.degree. C. to produce a shaped article, and (c) aging the thus-shaped article at a temperature between about 750.degree. and 1050.degree. C. for about 2 to 24 hours. The preform is held at the preheat temperature for 0.1 to 2 hours, just long enough to bring the preform uniformly to the shaping temperature. The third method comprises the steps of: (a) heat treating an alloy billet or preform at a temperature in the approximate range of T.sub..alpha. to T.sub..alpha. +100.degree. C. for about 0.5 to 8 hours, (b) rapidly heating the preform to shaping temperature, if the shaping temperature is greater than the heat treatment temperature, (c) shaping the preform at a temperature between T.sub..alpha. and T.sub..alpha. +100.degree. C. to produce a shaped article, and (d) aging the thus-shaped article at a temperature between about 750.degree. and 1050.degree. C. for about 2 to 24 hours. The fourth method comprises the steps of: (a) heat treating an alloy billet or preform at a temperature in the approximate range of T.sub..alpha. -40.degree. C. to T.sub..alpha. to for about 0.1 to 2 hours, (b) rapidly preheating the preform to shaping temperature, (c) shaping the preform at a temperature between T.sub..alpha. and T.sub..alpha. +100.degree. C. to produce an shaped article, and (d) aging the thus-shaped article at a temperature between about 750.degree. and 1050.degree. C. for about 2 to 24 hours.

A first method for producing articles of gamma titanium alumide alloy having improved properties comprises the steps of: (a) shaping the article at a temperature between the titanium-aluminum eutectoid temperature of the alloy and the alpha-transus temperature of the alloy, and (b) aging the thus-shaped article at a temperature between about 750.degree. and 1050.degree. C. for about 4 to 150 hours. Shaping is preferably carried out at a temperature about 0.degree. to 50.degree. C. below the alpha-transus temperature. A second method for producing articles of gamma titanium aluminide alloy having improved properties comprises the steps of: (a) shaping the article at a temperature in the approximate range of about 130.degree. C. below the titanium-aluminum eutectoid temperature of the alloy to about 20.degree. C. below the alpha-transus temperature of the alloy; (b) heat treating the thus-shaped article at about the alpha-transus temperature of the alloy for about 15 to 120 minutes; and (c) aging the thus-heat treated article at a temperature between about 750.degree. and 1050.degree. C. for about 4 to 300 hours.

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Beavercreek, OH, United States of America

Dennis M Dimiduk