Abstract: A cast slab containing C: less than 0.02 mass % and made of an Fe-based metal of an ?-? transforming component is subjected to hot rolling at a temperature of an A3 point or higher and is subjected to ?-region rolling at a temperature of 300° C. or higher and lower than the A3 point, and thereby a base metal sheet having a {100} texture in a surface layer portion is fabricated. Then, by performing a heat treatment under predetermined conditions, an Fe-based metal sheet is obtained in which a Z value is not less than 2.0 nor more than 200 when intensity ratios of respective {001}<470>, {116}<6 12 1>, and {223}<692> directions in a sheet plane by X-ray diffraction are set to A, B, and C respectively and Z=(A+0.97B)/0.98C is satisfied.

Abstract: On at least one surface of a base metal plate (1) of an ?-? transforming Fe or Fe alloy, a metal layer (2) containing ferrite former is formed. Next, the base metal plate (1) and the metal layer (2) are heated to an A3 point of the Fe or the Fe alloy, whereby the ferrite former are diffused into the base metal plate (1) to form an alloy region (1b) in a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less. Next, the base metal plate (1) is heated to a temperature higher than the A3 point of the Fe or the Fe alloy, whereby the accumulation degree of the {200} planes is increased and the accumulation degree of the {222} planes is decreased while the alloy region (11b) is maintained in the ferrite phase.

Abstract: A cast slab containing C: less than 0.02 mass % and made of an Fe-based metal of an ?-? transforming component is subjected to hot rolling at a temperature of an A3 point or higher and is subjected to ?-region rolling at a temperature of 300° C. or higher and lower than the A3 point, and thereby a base metal sheet having a {100} texture in a surface layer portion is fabricated. Then, by performing a heat treatment under predetermined conditions, an Fe-based metal sheet is obtained in which a Z value is not less than 2.0 nor more than 200 when intensity ratios of respective {001}<470>, {116}<6 12 1>, and {223}<692> directions in a sheet plane by X-ray diffraction are set to A, B, and C respectively and Z =(A+0.97B)/0.98C is satisfied.

Abstract: A cast slab containing C: less than 0.02 mass % and made of an Fe-based metal of an ?-? transforming component is subjected to hot rolling at a temperature of an A3 point or higher and is subjected to ?-region rolling at a temperature of 300° C. or higher and lower than the A3 point, and thereby a base metal sheet having a {100} texture in a surface layer portion is fabricated. Then, by performing a heat treatment under predetermined conditions, an Fe-based metal sheet is obtained in which a Z value is not less than 2.0 nor more than 200 when intensity ratios of respective {001}<470>, {116}<6 12 1>, and {223}<692> directions in a sheet plane by X-ray diffraction are set to A, B, and C respectively and Z=(A+0.97B)/0.98C is satisfied.

Abstract: A cast slab containing C: less than 0.02 mass % and made of an Fe-based metal of an ?-? transforming component is subjected to hot rolling at a temperature of an A3 point or higher and is subjected to ?-region rolling at a temperature of 300° C. or higher and lower than the A3 point, and thereby a base metal sheet having a {100} texture in a surface layer portion is fabricated. Then, by performing a heat treatment under predetermined conditions, an Fe-based metal sheet is obtained in which a Z value is not less than 2.0 nor more than 200 when intensity ratios of respective {001}<470>, {116}<6 12 1>, and {223}<692> directions in a sheet plane by X-ray diffraction are set to A, B, and C respectively and Z=(A+0.97B)/0.98C is satisfied.

Abstract: On at least one surface of a base metal plate (1) of an ?-? transforming Fe or Fe alloy, a metal layer (2) containing ferrite former is formed. Next, the base metal plate (1) and the metal layer (2) are heated to an A3 point of the Fe or the Fe alloy, whereby the ferrite former are diffused into the base metal plate (1) to form an alloy region (1b) in a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less. Next, the base metal plate (1) is heated to a temperature higher than the A3 point of the Fe or the Fe alloy, whereby the accumulation degree of the {200} planes is increased and the accumulation degree of the {222} planes is decreased while the alloy region (11b) is maintained in the ferrite phase.

Abstract: On at least one surface of a base metal plate (1) of an ?-? transforming Fe or Fe alloy, a metal layer (2) containing ferrite former is formed. Next, the base metal plate (1) and the metal layer (2) are heated to an A3 point of the Fe or the Fe alloy, whereby the ferrite former are diffused into the base metal plate (1) to form an alloy region (1b) in a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less. Next, the base metal plate (1) is heated to a temperature higher than the A3 point of the Fe or the Fe alloy, whereby the accumulation degree of the {200} planes is increased and the accumulation degree of the {222} planes is decreased while the alloy region (11b) is maintained in the ferrite phase.

Abstract: A cast slab containing C: less than 0.02 mass % and made of an Fe-based metal of an ?-? transforming component is subjected to hot rolling at a temperature of an A3 point or higher and is subjected to ?-region rolling at a temperature of 300° C. or higher and lower than the A3 point, and thereby a base metal sheet having a {100} texture in a surface layer portion is fabricated. Then, by performing a heat treatment under predetermined conditions, an Fe-based metal sheet is obtained in which a Z value is not less than 2.0 nor more than 200 when intensity ratios of respective {001}<470>, {116}<6 12 1>, and {223}<692> directions in a sheet plane by X-ray diffraction are set to A, B, and C respectively and Z=(A+0.97B)/0.98C is satisfied.

Abstract: On at least one surface of a base metal plate (1) of an ?-? transforming Fe or Fe alloy, a metal layer (2) containing ferrite former is formed. Next, the base metal plate (1) and the metal layer (2) are heated to an A3 point of the Fe or the Fe alloy, whereby the ferrite former are diffused into the base metal plate (1) to form an alloy region (1b) in a ferrite phase in which an accumulation degree of {200} planes is 25% or more and an accumulation degree of {222} planes is 40% or less. Next, the base metal plate (1) is heated to a temperature higher than the A3 point of the Fe or the Fe alloy, whereby the accumulation degree of the {200} planes is increased and the accumulation degree of the {222} planes is decreased while the alloy region (11b) is maintained in the ferrite phase.

Abstract: Steel sheet having a high {222} plane integration comprising steel sheet having an Al content of less than 6.5 mass % characterized by one or both of (1) a {222} plane integration of one or both of an ?Fe phase and ?Fe phase with respect to the steel sheet surface being 60% to 99% and (2) a {200} plane integration of one or both of an ?Fe phase and ?Fe phase with respect to the steel sheet surface being 0.01% to 15%.

Abstract: An alloy having a low melting point for liquid-phase diffusion bonding capable of bonding both Ni-based heat resistance alloy material and Fe-based steel material. The alloy comprises in atom percent (%): 22<Ni?60, B: 12-18, C: 0.01-4, and the balance being Fe and residual impurities; or comprises in atom percent (%): 22<Ni?60, B: 7-18, 4?C?11, and the balance being Fe and residual impurities.

Abstract: A TiAl intermetallic compound-base alloy material having excellent strength properties at high temperatures and ductility, characterized by comprising: a fine alumina (Al.sub.2 O.sub.3) dispersed so as to give an O.sub.2 concentration of 1000 to 5000 ppm by weight and in a particle diameter of 200 to 500 nm; a boride (TiB.sub.2) dispersed to give a B concentration of 0.1 to 10 at % and in a particle diameter of not more than 500 nm; 1 to 3 at % of at least one of Cr, Mn, and V; and TiAl having a Ti content of 50 to 53 at % and an Al content of 47 to 50 at %, said TiAl intermetallic compound-base alloy material having been directly cast at a cooling rate of 10.sup.3 to 10.sup.5 .degree. C./sec and a process for producing the same. According to the present invention, exhaust valves for automobiles and materials for engine turbines for jet airplanes and the like having excellent tensile strength at high temperatures and ductility at high temperatures and room temperature are provided.

Abstract: TiAl-besed intermetallic compound alloys contain chromium and consist essentially of a dual-phase microstructure of .gamma. and .beta. phases, with the .beta. phase precipitating at .gamma. grain boundaries. The .beta. phase precipitating at .gamma. grain boundaries is 2% to 25% by volume fraction. A process for preparing TiAl-based intermetallic compound alloys comprises the steps of preparing a molten TiAl-based intermetallic compound alloy of a desired composition, solidifying the molten alloy, homogenizing the solidified alloy by heat treatment, and thermomechanically working the homogenized alloy.

Abstract: TiAl-based intermetallic compound alloys contain chromium and consist essentially of a dual-phase microstructure of .gamma. and .beta. phases, with the .beta. phase precipitating at .gamma. grain boundaries. The .beta. phase precipitating at .gamma. grain boundaries is 2% to 25% by volume fraction. A process for preparing TiAl-based intermetallic compound alloys comprises the steps of preparing a molten TiAl-based intermetallic compound alloy of a desired composition, solidifying the molten alloy, homogenizing the solidified alloy by heat treatment, and thermomechanically working the homogenized alloy.

Abstract: TiAl-besed intermetallic compound alloys contain chromium and consist essentially of a dual-phase microstructure of .gamma. and .beta. phases, with the .beta. phase precipitating at .gamma. grain boundaries. The .beta. phase precipitating at .gamma. grain boundaries is 2% to 25% by volume fraction. A process for preparing TiAl-based intermetallic compound alloys comprises the steps of preparing a molten TiAl-based intermetallic compound alloy of a desired composition, solidifying the molten alloy, homogenizing the solidified alloy by heat treatment, and thermomechanically working the homogenized alloy.

Abstract: TiAl-besed intermetallic compound alloys contain chromium and consist essentially of a dual-phase microstructure of .gamma. and .beta. phases, with the .beta. phase precipitating at .gamma. grain boundaries. The .beta. phase precipitating at .gamma. grain boundaries is 2% to 25% by volume fraction. A process for preparing TiAl-based intermetallic compound alloys comprises the steps of preparing a molten TiAl-based intermetallic compound alloy of a desired composition, solidifying the molten alloy, homogenizing the solidified alloy by heat treatment, and thermomechanically working the homogenized alloy.

Abstract: This invention relates to TiAl based intermetallic compound alloy and process for producing; the object of this invention is to improve high temperature deformability. The alloy comprises basic components: Ti.sub.y AlCr.sub.x, wherein 1%.ltoreq.X.ltoreq.5%, 47.5%.ltoreq.Y.ltoreq.52%, and X+2Y.gtoreq.100%, and comprises a fine-grain structure with a .beta. phase precipitated on a grain boundary of equiaxed .gamma. grain having grain size of less than 30 .mu.m, and possessing a superplasticity such that the strain rate sensitivity factors (m value) is 0.40 or more and tensile elongation is 400% or more tested at 1200.degree. C. and a strain rate of 5.times.10.sup.-4 S.sup.-1.

Abstract: This invention relates to TiAl based intermetallic compound alloy and process for producing; the object of this invention is to improve high temperature deformability. The alloy comprises basic components: Ti.sub.y AlCr.sub.x, wherein 1%.ltoreq.X.ltoreq.5%, 47.5%.ltoreq.Y.ltoreq.52%, and X+ 2Y.gtoreq.100%, and comprises a fine-grain structure with a .beta. phase precipitated on a grain boundary of equiaxed .gamma. grain having grain size of less than 30 .mu.m, and possessing a superplasticity such that the strain rate sensitivity factors (m value) is 0.40 or more and tensile elongation is 400% or more tested at 1200.degree. C. and a strain rate of 5.times.10.sup.-4 S.sup.-1.