University of Virginia Patent Foundation

General Electric Company

Gary J Shiflet

S Joseph Poon

Vijayabarathi Ponnambalam

Xiaofeng Gu

Xiao-Jun Gu

Joseph Poon

Pazhayannur Ramanathan Subramanian

Francis Johnson

Luana Emiliana Iorio

Sriparna Bhattacharya

Yi He

Dongjian Li

The present invention relates to novel non-ferromagnetic amorphous steel alloys represented by the general formula: Fe&#x2014;Mn-(Q)-B-M, wherein Q represents one or more elements selected from the group consisting of Sc, Y, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, and M represents one or more elements selected from the group consisting of Cr, Co, Mo, C and Si. Typically the atomic percentage of the Q constituent is 10 or less. An aspect is to utilize these amorphous steels as coatings, rather than strictly bulk structural applications. In this fashion any structural metal alloy can be coated by various technologies by these alloys for protection from the environment. The resultant structures can utilize surface and bulk properties of the amorphous alloy.

Non-ferromagnetic amorphous steel alloys containing large-atom metals

Amorphous steel composites with enhanced mechanical properties and related methods for toughening amorphous steel alloys. The composites are formed from monolithic amorphous steel and hard ceramic particulates, which must be embedded in the glass matrix through melting at a temperature above the melting point for the steel but below the melting point for the ceramic. The ceramics may be carbides, nitrides, borides, iron-refractory carbides, or iron-refractory borides. The produced composites may be one of two types, primarily distinguished by the methods for embedding the ceramic particulates in the steel. These methods may be applied to a variety of amorphous steels as well as other non-ferrous amorphous metals, and the resulting composites can be used in various applications and utilizations.

Amorphous steel composites with enhanced strengths, elastic properties and ductilities

Amorphous steel composites with enhanced mechanical properties and related methods for toughening amorphous steel alloys. The composites are formed from monolithic amorphous steel and hard ceramic particulates, which must be embedded in the glass matrix through melting at a temperature above the melting point for the steel but below the melting point for the ceramic. The ceramics may be carbides, nitrides, borides, iron-refractory carbides, or iron-refractory borides. An optical micrograph of such a composite including niobium carbide particulates is shown in FIG.A. The produced composites may be one of two types, primarily distinguished by the methods for embedding the ceramic particulates in the steel. These methods may be applied to a variety of amorphous steels as well as other non-ferrous amorphous metals, and the resulting composites can be used in various applications and utilizations.

An amorphous magnetic alloy is presented. The alloy has the general formula: (FeCo)MoPBCSi, wherein n is the atomic percent of iron and cobalt; x is the fraction of n; a, b, c, d and e are the atomic percent of molybdenum, phosphorous, boron, carbon and silicon respectively and n, x, a, b, c, d and e are defined by following relationship: 76&#x2266;n&#x2266;85; 0.05&#x3c;x&#x2266;0.50; 0&#x2266;a&#x2266;4; b&#x2267;10; 0&#x2266;c&#x3c;d; and 0.1&#x2266;e&#x2266;2. Articles comprising the alloy and methods employing the alloy for making articles are also presented.

Amorphous magnetic alloys, associated articles and methods

Iron based amorphous steel alloy having a high Manganese content and being non-ferromagnetic at ambient temperature. The bulk-solidifying ferrous-based amorphous alloys are multicomponent systems that contain about 50 atomic percent iron as the major component. The remaining composition combines suitable mixtures of metalloids (Group b elements) and other elements selected mainly from manganese, chromium, and refractory metals. Various classes of non-ferromagnetic ferrous-based bulk amorphous metal alloys are obtained. One class is a high-manganese class that contains manganese and boron as the principal alloying components. Another class is a high manganese-high molybdenum class that contains manganese, molybdenum, and carbon as the principal alloying components. These bulk-solidifying amorphous alloys can be obtained in various forms and shape for various applications and utlizations. The good processability of these alloys can be attributed to the high reduced glass temperature T(e.g., about 0.6 to 0.63) and large supercooled liquid region &#x394;T(e.g., about 50-100&#xb0; C.).

Bulk-solidifying high manganese non-ferromagnetic amorphous steel alloys and related method of using and making the same

The present invention relates to novel non-ferromagnetic amorphous steel alloys represented by the general formula:Fe&#x2014;Mn-(Q)-B-M,wherein Q represents one or more elements selected from the group consisting of Sc, Y, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu, and M represents one or more elements selected from the group consisting of Cr, Co, Mo, C and Si. Typically the atomic percentage of the Q constituent is 10 or less. FIG.B represents a differential thermal analysis plot for several exemplary alloys according to the invention.

Iron based amorphous steel alloy having a high Manganese content and being non-ferromagnetic at ambient temperature. The bulk-solidifying ferrous-based amorphous alloys are multicomponent systems that contain about 50 atomic percent iron as the major component. The remaining composition combines suitable mixtures of metalloids (Group b elements) and other elements selected mainly from manganese, chromium, and refractory metals. Various classes of non-ferromagnetic ferrous-based bulk amorphous metal alloys are obtained. One class is a high-manganese class that contains manganese and boron as the principal alloying components. Another class is a high manganese-high molybdenum class that contains manganese, molybdenum, and carbon as the principal alloying components. These bulk-solidifying amorphous alloys can be obtained in various forms and shape for various applications and utlizations. The good processability of these alloys can be attributed to the high reduced glass temperature T(e.g., about 0.6 to 0.63) and large supercooled liquid region &#x394;T(e.g., about 50&#x2013;100&#xb0; C.).

Bulk nanocrystalline Ti-based alloys were produced by conventional cooling from the corresponding liquid or high temperature solid phase followed by annealing at an appropriate temperature for a certain amount of time. The titanium-based alloys have a composition represented by the following formula, Ti.sub.a Cr.sub.b Cu.sub.c M.sub.d wherein

Bulk nanocrystalline titanium alloys with high strength

Ductile, strong, and stable (crystallization temperature above 250.degree. C.) Al-X-Z metallic classes contain 90 at. % Al where X-Fe, Co, Ni, Rh; Z-rare earths, Hf, Y, Stable (crystallization temperatures reaching 500.degree. C.) Al-Y-Fe-Si glasses have superior hardness properties upon consolidation. The present alloys are at least twice as strong in tensile strength as the strongest commercial aluminum alloys.

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Charlottesville, VA, United States of America

Gary J Shiflet