The role of chemical reactions in the mechanism of comminution of ductile metals into ultrafine powders by grinding
Role of chemical reactions in comminution mechanism of ductile metals into ultrafine powders by grinding
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Role of chemical reactions in comminution mechanism of ductile metals into ultrafine powders by grinding
Ductility ratio data for high strength titanium alloys from specially designed experiments and notch strength tests
Reduction of ductile-to-brittle transition temperature for unalloyed chromium achieved in alloys resembling Cr-Re system
To produce high strength alloy steel with retention of ductility, include tempering, cooling and subsequent tempering. Five parameters for optimum results are pretempering temperature, amount of strain, strain rate, temperature during strain, and retempering temperature.
Development and testing of ductile niobium alloy with silicide coating for rocket engine combustion chamber
Ductilizing of Group 6A elements by rhenium and other solutes
Reinforcement of ductile aluminum and epoxies with brittle high modulus filaments
Development of ductile oxidation-resistant cladding alloys for thoria dispersion, strengthened nickel and nickel-chromium
Ductile metal powder chemical reactions during comminution in pure or oxygenated water
Ductile fracture of polymers under stresses
Reactor irradiation effects on ductile brittle transition and stress-strain behavior of tungsten
Analytical and experimental investigation of ductile fracture of polymers using adaptation of Dugdale model
Anisotropic materials ductile fracture involving crack initation and propagation, using Dugdale mathematical model
Fatigue process analysis through crack initiation and propagation and final fracture, considering ductility, tensile strength and fracture toughness roles
Bend angles for columbium-base alloys, WC3015 and Cb752, at temperatures between -300 F and +500 F are reported. WC3015 exhibited a bend transition temperature well below -100 F, but was severely embrittled by silicide coatings. Cb 752 exhibited a bend transition temperature below -300 F, and the silicide coating application did not influence bend angle of the substrate. However, coating failure on both alloys was observed at less than 60 deg bend, even at 500 F. The effect of electron beam welding and gas tungsten-arc welding on the properties of WC3015 and Cb752 are also reported. Both techniques are shown to produce a marked reduction in the bend angle of WC3015. Unlike WC3015, ductility is restored in Cb752 after a suitable postweld anneal. Microstructural and hardness tests results for both alloys are reported and discussed.
It is shown that, by rolling, tungsten-tantalum laminar composites can be reduced in thickness as much as 90 to 1, with a resulting improvement in strength of nearly 66%. Further reductions in laminar thickness are believed to be possible with further increases in the strength of the composite material. The rolled tungsten-tantalum laminar material shows also a remarkable low-temperature ductility, sustaining a 3-T bend at room temperature without incurring macrodamage.
A program was conducted to determine if aging embrittlement occurs in the columbium alloys C-103, CB-1Zr, and Cb-752 or in the molybdenum alloy Mo-TZM. Results showed that aging embrittlement does not occur in C-103, Cb-1Zr, or Mo-TZM during long-term (1000 hr) aging at temperatures in the range 700 to 1025 C. In contrast, aging embrittlement did occur in the Cb-752 alloy after similar aging at 900 C. A critical combination of the solute additions W and Zr in Cb-752 led to Zr segregation at grain boundaries during long-term aging. This segregation subsequently resulted in embrittlement as indicated by an increase in the ductile-brittle transition temperature from below -1960 C to about -150 C.
A central crack, symmetrically growing at a constant speed in a two dimensional ductile material subject to uniform tension at infinity, is investigated using the integral transform methods. The crack is assumed to be the Dugdale crack, and the finite stress condition at the crack tip is satisfied during the propagation of the crack. Exact expressions of solution are obtained for the finite stress condition at the crack tip, the crack shape, the crack opening displacement, and the energy release rate. All those expressions are written as the product of explicit dimensional quantities and a nondimensional dynamic correction function. The expressions reduce to the associated static results when the crack speed tends to zero, and the nondimensional dynamic correction functions were calculated for various values of the parameter involved.