Abstract: A continuous fiber-reinforced Ti-based composite material comprises a Ti alloy matrix containing 3 to 7% by weight of Al, 2 to 5% by weight of v, 1 to 3% by weight of Mo, 1 to 3% by weight of Fe, 0.06 to 0.20% by weight of 0, and the balance of Ti and unavoidable impurities, and SiC continuous fibers arranged within said matrix in one direction.

Abstract: A method for making titanium alloy products comprises the steps of:superplastic-forming .alpha.+.beta.-titanium alloy at a predetermined temperature, said .alpha.+.beta.-titanium alloy consisting essentially of 3.45 to 5 wt. % Al, 2.1 to 5 wt. % V, 0.85 to 2.85 wt. % Mo, 0.85 to 3.15 wt. % Fe, 0.01 to 0.25 wt. % 0 and the balance being titanium;cooling the superplastically formed titanium alloy at a cooling rate of 0.05 to 5.degree. C./sec; andaging the cooled titanium alloy at a temperature of 400.degree. to 600.degree. C.The superplastically formed titanium alloy can be diffusion-bonded, thereafter the diffusion-bonded titanium alloy can be cooled and aged.

Abstract: A high strength and corrosion resistant titanium alloy having excellent corrosion-wear properties may be prepared in that Al and Mo are added as alloying elements in specific amounts, and if Zr in a specific amount is further added, the strength and the corrosion-wear properties would be more improved.

Abstract: A .beta. type titanium alloy material is passed through processes and heating treatments of cold working--intermediate solution treatment--final cold working--final solution treatment--aging. In this process, a structure, which has been provided with strains by the cold working performed prior to the final cold working, will be changed into a recrystallized structure by carrying out the intermediate solution treatment, where uniform and fine micro substructure of dislocations, remain with grains. If such an intermediate solution-treated material is processed with a slight cold working by the final cold working and further with the solution treatment, only a recovery phenomenon progresses, and it is possible to provide such a micro substructure containing more uniform and finer dislocation network not only in grains but also in grain boundaries. Therefore, in the aging, expedition of precipitation and uniform distribution of .alpha.

Abstract: For producing titanium clad steel plates by hot rolling, oxide of Mo or V is used as an intermediate material, and a slab assembly is formed with ferrous bases and titanium cladding materials. At least one side of cladding surfaces of the bases and the cladding materials is coated with an oxide of Mo or V of 20 to 300 g/m.sup.2, and an interior of the slab assembly is air-discharged less than 10.sup.-1 torr, and the slab assembly is heated at temperatures between a melting point of the employed oxide plus 50.degree. C. and 1050.degree. C. and undertaken with hot rolling.

Abstract: A method for producing Ti alloy plates, comprising heating an .alpha.+.beta. Ti alloy ingot to a temperature within the .alpha.+.beta. two phase range, forging or rolling said heated alloy ingot to reduce it more than 30% whereby strain energy accumulates in said ingot as it is being reduced, and reheating said reduced ingot containing said accumulated strain energy to a temperature of the .alpha.+.beta. phase range and then hot rolling said reheated reduced ingot so that it is further reduced in an amount more than an additional 30% whereby said accumulated strain energy accelerates recrystallization during said hot rolling to produce a uniform alloy structure, said heating and reheating being carried out in an atmosphere having not more than 0.02 atm oxygen partial pressure.

Abstract: A method of manufacturing a rolled titanium alloy sheet comprises breaking down an .alpha. or .alpha.+.beta. titanium alloy ingot into a slab, working the slab in sequential stages of(A) cross rolling the slab in the .alpha.+.beta. region under a condition of a reduction ratio of at least 1.2 and a cross rolling ratio of 0.6 to 1.4,(B) annealing the workpiece for recrystallization at a temperature 20.degree. to 100.degree. C., preferably 20.degree. to 70.degree. C., below the .beta.-transus of the alloy, and(C) further cross rolling it in the .alpha.+.beta. region under a condition of a reduction ratio of at least 1.6 and a cross rolling ratio of 0.6 to 1.4,and thereafter heat treating the rolled workpiece for annealing, solution treatment and aging or the like, depending on the intended use of the product. The method may include an additional stage (D) of repeating stages (B) and (C) at least once each. The ingot breakdown is preferably carried out by forging or rolling at a temperature of the two-phase .

Abstract: An austenitic stainless steel plate containing up to 0.08 wt. % of carbon, up to 1.0 wt. % of silicon, up to 2.0 wt. % of manganese, 8.0-16.0 wt. % of nickel, 16.0-20.0 wt. % of chromium, 0-30 wt. % of molybdenum, up to 0.25 wt. % of nitrogen and the balance of iron and inherent impurities, is manufactured by rolling a stainless steel blank at a temperature higher than T.sub.R (.degree.C.)=940+30(%Mo), and then cooling the rolled blank from a temperature above 800.degree. C. to a temperature below 500.degree. C. at a cooling speed higher than Rc (.degree.C./sec.) shown by the following equations:log (Rc)=-0.32+14(%C+%N)-0.067(%Mo)when (%C+%N).ltoreq.1.0 wt. %; andlog (Rc)=1.08-0.067(%Mo)when (%C+%N)>1.0 wt. %.

Abstract: An improved method of continuously casting nickel containing steel wherein the formation of surface cracks is prevented. The molten steel which is cast contains less than 0.0020% S, less than 0.0045% N, Ca in an amount of from 0.0020 to 0.0070%, Ni in an amount from 5.5 to 10%, the remainder being Fe and unavoidable impurities.

Abstract: Low nonmagnetic steel having a thermal expansion coefficient of 1.0.about.1.3.times.10.sup.-5 /.degree. C. and a high yielding point of higher than 36 Kg/mm.sup.2 consists of less than 0.5% by weight of C, less than 2% by weight of Si, 20.about.30% by weight of Mn, and 0.005.about.0.04% by weight of N and the balance of iron and impurities, wherein the following relationships between the amounts of C and Mn are simultaneously satisfied.Mn (%)>16.times.C (%)+18Mn (%)>-12.times.C (%)+21.5The steel described above is heated to a temperature of less than 1220.degree. C., and then hot rolled. A finishing rolling temperature is maintained to be less than 800.degree. C.+400.degree. C..times.C (%) depending upon the amount of carbon. After cold working the nonmagnetic steel has a permeability of less than 1.1.

Abstract: The nonmagnetic alloy consists of 0.22-0.30% by weight of carbon, 22-28% by weight of manganese, up to 4% by weight of silicon, 0.030-0.10% by weight of sulphur, 0.001-0.008% by weight of calcium, 0.001-0.008% by weight of sol.Al and the balance of iron. If desired, either one or both of up to 2.0% by weight of chromium and up to 2.0% by weight of vanadium may be incorporated.

Abstract: Low nonmagnetic steel having a thermal expansion coefficient of 1.0.about.1.3.times.10.sup.-5 /.degree.C. and a high yielding point of higher than 36 Kg/mm.sup.2 consists of less than 0.5% by weight of C, less than 2% by weight of Si, 20.about.30% by weight of Mn, and 0.005.about.0.04% by weight of N and the balance of iron and impurities, wherein the following relationships between the amounts of C and Mn are simultaneously satisfied.Mn(%)>16.times.C(%)+18Mn(%)>-12.times.C(%)+21.5The steel described above is heated to a temperature of less than 1220.degree. C., and then hot rolled. A finishing rolling temperature is maintained to be less than 800.degree. C.+400.degree. C..times.C(%) depending upon the amount of carbon. After cold working the nonmagnetic steel has a permeability of less than 1.1.

Abstract: A steel slab or bloom containing 0.3.about.0.15% by weight of C, 0.05.about.0.60% by weight of Si, 0.60.about.2.5% by weight of Mn, 0.010.about.0.15% by weight of Nb, 0.005.about.0.10% by weight of soluble Al and the remainder of iron is heated to such a temperature region above 1050.degree. C. and below the reheating temperature where the austenitic grain size would be 150.mu.. The heated slab or bloom is then hot rolled with total rolling reduction of more than 40% with respect to a finished thickness at the non-recrystallized austenitic region and the hot rolled stocks are subjected to accelerated cooling at a rate of 5.degree..about.20.degree. C./sec. from a temperature higher than the Ar.sub.3 transformation point to a temperature within 550.degree..about.650.degree. C. Finally the stocks are air cooled.