Title of Invention

A METHOD FOR MAKING AMORPHOUS MATERIAL

Abstract

ABSTRACT 108/CHENP/2005 A method for making amorphous material A method for making amorphous material, the method comprising: feeding particles into a plasma to provide a melt, the particles comprising at least 35 percent by weight AI2O3, based on the total weight of the particles, and a metal oxide other than Al<sub>2</sub>O<sub>3</sub>, wherein the particles contain not more than 10 percent by weight collectively As<sub>2</sub>O<sub>3</sub>, B<sub>2</sub>O<sub>3</sub>, GeO<sub>2</sub>, P<sub>2</sub>O<sub>5</sub>, SiO<sub>2</sub> ,TeO<sub>2</sub>, and V<sub>2</sub>O<sub>5</sub>, based on the total weight of the particles, with the proviso that if the metal oxide other than Al<sub>2</sub>O<sub>3</sub> is ZrO<sub>2</sub>, then the particles comprise a metal oxide other than Al<sub>2</sub>O<sub>3</sub> and ZrO<sub>2</sub>; and spraying and cooling the melt to provide amorphous material, the amorphous material comprising at least 35 percent by weight Al<sub>2</sub>O<sub>3</sub>, based on the total weight of the amorphous material, and the metal oxide other than Al<sub>2</sub>O<sub>3</sub>, wherein the amorphous material contains not more than 10 percent by weight collectively As<sub>2</sub>O<sub>3</sub>, B<sub>2</sub>O<sub>3</sub>, GeO<sub>2</sub>, P<sub>2</sub>O<sub>5</sub>, SiO<sub>2</sub>, TeO<sub>2</sub>and V<sub>2</sub>O<sub>5</sub>, based on the total weight of the amorphous material, wherein the amorphous material has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and % dimensions is at least 25 micrometers, with the proviso that if the metal oxide other than Al<sub>2</sub>O<sub>3</sub> is ZrO<sub>2</sub>, then the particles comprise a metal oxide other than Al<sub>2</sub>O<sub>3</sub> and ZrO<sub>2</sub> at least a portion of which forms at least one distinct crystalline phase when the amorphous material is crystallized.

Full Text

This invention relates to plasma spraying. Description of Related An Plasma spraying to provide amorphous, ceramic, metal, metallic alloy, and intcrmetallic materials is well known in the art. While plasma spraying is commonly used for surface modification and/or to provide coatings, it has also been used to form bulk materials. Plasma spraying is typically conducted by introducing feed particles into a plasma (typically at temperatures over JO,000°C), to convert the feed particles into a melt (molten droplets), which are then brought in contact with a substrate to cool them (typically at cooling rates over 10,000oC/scc). Upon contact with the substrate, the molten droplets rapidly solidify resulting in an amorphous, partially crystalline, or crystalline material. Plasma spray processing has been used to form a variety of materials including, metals, metallic alloys, mtermctallies, and ceramics. Depending, for example, on the length of the operation, the operating conditions, the substrate, and feed material, a variety of structures varying from thin, thick, multi-layered and composite films to bulk materials may be deposited. Furthermore, the nature of the deposited materials, such as the composition, density, the structure can be varied continuously or in a stepwise manner. Plasma-sprayed coatings and bulk materials are employed in a wide array of applications ranging from microelectronic components to large engineered structures. For example, the plasma sprayed coatings find applications as protective (abrasion-,oxidation-, and corrosion-resistant, thermal-barrier) coatings. Similarly, use of plasma processing for making bulk materials is increasing. Among the wide variety of plasma processed materials, oxide ceramics hold a special place due to their desirable properties including their insulating abilities and abrasive, corrosive, and thermal-shock resistance. The most commonly plasma-spray processed oxide ceramics have been alumina, alumina-titania, stabilized zirconia, and chromia. The very high quench rales typically associated with plasma-spray processing facilitate formation of non-equilibrium, mctastable or non-stoichiometrie phases, For example, plasma-sprayed alumina, and alumina-titania typically form mctastable transitional alumina. Similarly, p! asm a-sprayed fully-oi" partially- stabilized zirconia typically form non-equilibrium tetragonal phase. In another aspect, the relatively high quench rates associated with plasma-spraying can lead to the formation of ceramics with extremely Fine (such as nanocrystalline) crystals within each splat {i.e., within each solidified droplet) making up the plasma-sprayed ceramic. In genera!, it is known in the art that ceramics with fine crystalline structures, particularly in combination with high density (i.e., at least 70% of theoretical, preferably at least 90, 95, 96, 97, 98, 99, or even 100%) have more desirable properties as compared to coarser and/or less dense materials. There is a continuing desire for new materials to use for plasma spraying, as well as new plasma sprayed materials. Summary of the invention in one aspect, the present invention provides a method for making amorphous materia], the method comprising: feeding particles into a plasma to provide a melt, the particles comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight AI1O3, based on the total weight of the particles, and a metal oxide other than Al;03 (e.g.. Y203, REO, ZrO;, TiO:, CaO, Cr:03, MgO, NIO, CuO, and complex metal oxides thereof), wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zero) percent by weight collectively As;03, B;Oj. GeO:, P:Oj, Si02l Te02, and V:Oj, based on the total weight of the panicles, with the proviso that if the metal oxide other than AI1O3 is ZrOi, then the particles further comprises a metal oxide other than A1;05 and ZrO:; und spraying and cooling the melt to provide amorphous material, the amorphous material comprising at least 35 (in some embodiments, preferably at least 35 40, 45, 50, 55, 60, 65, or even at feast 70) percent by weight Al:0:„ based on the tola! weight of the amorphous material, and the metal oxide other than AhO], and complex metal oxides thereof), wherein the amorphous material contains not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, J, or zero) percent by weight collectively As;03, B1O3, GeO:. P205, Si02, Tc02, and V205, based on the total weight of the amorphous material, wherein the amorphous material has x, y, and 2 dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least J, 5, 10, 25 micrometers (in some embodiments, preferably, at least at least 30 micrometers, 35 micrometers, 40 micrometers, 45 micrometers, 50 micrometers, 75 micrometers, 100 micrometers, 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, I mm, 5 mm, or even at least 10 mm), with the proviso that if the metal oxide other than AI;0:, is Zr02, then the particles further comprises a metal oxide other than AI2O3 and Zr02 that forms at least one distinct crystalline phase when the amorphous material is crystallized. The x, y, and z dimensions of a material arc determined cither visually or using microscopy, depending on the magnitude of the dimensions. The reported z dimension is, for example, the diameter of a sphere, the thickness of a coating, or the longest length of a prismatic shape. In another aspect, the present invention provides a method for making glass, the method comprising: feeding particles into a plasma to provide a melt, the particles comprising at least 35 (in some embodiments, preferably at least 40,45,50, 55,60, 65. or even at least 70) percent by weight AI2O3, bused on the total weight of the particles, and a metal oxide other than Al:03 (e.g., Y20.-i, REO, Z1O2. TI02, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zero) percent by weight collectively As;03. B;03, Gc02, P205. S1O2, Te02, and V205, based on the total weight of the particles; and spraying and cooling the melt 10 provide glass, the glass comprising at least 35 (in some embodiments, preferably at least 35 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight AUG);,, based on the total weight of the glass, and the metal oxide other than AI2O3, and complex metal oxides thereof), wherein the glass contains not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zero) percent by weight collectively As203, B203, GeO;, P205, Si02,Te02, and V205, based on the total weight of the "lass. In some embodiments, the "lass has x, y. and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 1,5, 10, 25 micrometers (in some embodiments, preferably, at least 30 micrometers, 35 micrometers, 40 micrometers, 45 micrometers, 50 micrometers, IS micrometers, 100 micrometers, 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm, 5 mm, or even at least 10 mm). In one aspect, the present invention provides a method for making amorphous material, the method comprising: . feeding panicles into a plasma to provide a melt, the particles comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight A1203, based on the total weight of the particles, a first metal oxide other than Al203 (e.g., Y203. REO, Zr03, Ti02, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), and a second, different metal oxide other than Al203 (e.g., Y203. REO, Zr02, Ti02, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), wherein the AN03, first metal oxide, and second metal oxide collectively comprise at least 80 (in some embodiments, preferably, at least 85, 90, 95. 97, 98, 99, or even 100) percent by weight of the particles, and wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5,4, 3, 2. 1. or zero) percent by weight collectively As203, B203, GeO;, P203, Si03, Te02, and V205, based on the total weight of the particles, with the proviso that if the first or second metal oxide other is Zr02, then the particles further comprises a metal oxide other than Al303 and Zr02 that at least a portion of which forms a distinct crystalline phase when the amorphous material is crystallized; and spraying and cooling the melt to provide the amorphous material, the amorphous material comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight A1203, based on the total weight of the amorphous material, the first metal oxide other than Al203, and complex metal oxides thereof), and the second, different metal oxide other than A1203, and complex metal oxides thereof), wherein the AI2O3, first metal oxide, and second metal oxide collectively comprise at least SO (in some embodiments, preferably, at least 85, 90, 95, 97. 98, 99, or even 100) percent by weight of the amorphous material, wherein the amorphous material contains not more than 10 (in some embodiments, preferably not more than 5. 4, 3, 2, I, or zero) percent by weight collectively As203, B2O3, Ge02, Pi05, Si02, TeO:, and V2Oj, based on the total weight of the amorphous material, with the proviso that if the first or second metal oxide is ZrOi, then the amoiphous material further comprises a metal oxide other than AI2O3 and ZrCh at least a portion of which forms at least one distinct crystalline jiha.se when the amorphous material is crystallized, wherein the amorphous material has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least I, 5, 10, 25 micrometers (in some embodiments, preferably, at least at least 30 micrometers, 35 micrometers, 40 micrometers, 45 micrometers, 50 micrometers, 75 micrometers, 100 micrometers, 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, I mm, 5 mm, or even at least 10 mm). In another aspect, the present invention provides an apparatus for generating a thermal spray of metal oxide droplets, comprising: a plasma arc spray gun operable to generate a plasma gas jet in a delivery direction, the plasma gas jet being substantially symmetrical about a jet axis; and a first carrier conduit operable to deliver metal oxide particles to the plasma gas jet, the first carrier conduit comprising a conduit axis that intersects the jet axis at an angle of not greater than 75 (in some embodiments, preferably, not greater than 70, 65, 60, 55, 50, 45, 40, 35, 30, 25, 20, 15, 10, or even not greater than 5; in a range from 75 to 60. 70 to 60, or 65 to 60) degrees, wherein the first conduit extend away from the jet axis in the delivery direction. Optionally, the apparatus further comprises a second (third, or more) carrier conduit operable to deliver metal oxide particles to the plasma gas jet, the second (third, or more) carrier conduit may comprise a conduit axis that intersects the jet axis at an angle of not greater than 75 (in some embodiments, preferably, not greater than 70, 65, 60, 55, 50, 45, 40, 35, 30, 25, 20, 15, 10, or even not greater than 5; in a range from 75 to 60, 70 to 60, or65 to 60) degrees, wherein the second conduit extend away from the jet axis in the delivery direction. Although not wanting to be bound by theory, it is believed that the use of specified angle desirably changes (e.g., increases) the residence time or the interaction of" the feed particles in the plasma, wherein residence time increases, for example as the angle decreases. In another aspect, the present invention provides an apparatus for generating a thermal spray of metal oxide droplets, comprising: a plasma arc spray gun operable to generate a plasma gas jet in a delivery , direction, the plasma gas jet being substantially symmetrical about a jet axis; and a first carrier conduit operable to deliver metal oxide particles to the plasma gas jet, the first carrier conduit comprising a particle delivery vector that intersects the jet axis at an angle of not greater than 75 (in some embodiments, preferably, not greater than 70,65,60,55,50,45,40,35,30,25,20, 15, 10, or even not greater than 5; in a range from 75 to 60, 70 to 60, or 65 to 60) degrees, wherein the particle delivery vector comprises a vector component having a direction that is substantially opposite the delivery direction. Optionally, the apparatus further comprises a second (third or more) carrier conduit for delivering particles into the plasma gas jet, the second (third or more) currier conduit may comprise a particle delivery vector that intersects the jet axis at an angle of not greater [fian 75 (in some embodiments, preferably, not greater than 70, 65. 60, 55, 50, 45, 40, 35, 30, 25, 20, 15, 10, or even not greater than 5; in a range from 75 to 60, not greater than 70 to 60, or not greater than 65 to 60) degrees, wherein the particle delivery vector of the second (third or more) earner conduit comprises a vector component having a direction that is substantially opposite the delivery direction, and is different than the vector component of the first earner conduit. Although not wanting to be bound by theory, it is believed that the use of specified angle desirably changes (e.g., increases) the residence time or the interaction of the feed particles in the plasma, wherein residence time increases, for example as the angle decreases. In another aspect, the present invention provides a method for making amorphous material, the method comprising: generating a plasma gas jet in a delivery direction, the plasma gas jet being substantially symmetrical about a jet axis; delivering particles into the plasma gas jet through a first earner conduit to provide a melt, the first carrier conduit comprising a conduit axis that intersects the jet axis at an angle of not greater than 75 (in some embodiments, preferably, not greater than 70, 65,60,55,50,45,40,35,30,25,20, 15, 10, or even not greater than 5; in a range from 75 to 60, 70 lo 60, or 65 to 60) degrees, wherein the first conduit extends away from the jet axis in the delivery direction; and spraying and cooling the melt to provide amorphous material. Optionally, method further comprises a second (third or more) carrier conduit for delivering particles into the plasma gas jet, the second (third or more) carrier conduit may comprise a conduit axis that intersects the jet axis at an angle of not greater than 75 (in some embodiments, preferably, not greater than 70, 65, 60, 55, 50, 45,40, 35, 30, 25, 20, 15, 10, or even not greater than 5; in a range from 75 to 60, 70 to 60, or 65 to 60) degrees, wherein the second (third or more) conduit extends away from the jet axis in the delivery direction. Although not wanting to be bound by theory, it is believed that the use of specified angle desirably changes (e.g., increases) the residence time or the interaction of the feed particles in the plasma, wherein residence time increases, for example as the angle decreases. In another aspect, the present invention provides a method for making amorphous material, the method comprising: generating a plasma gas jet in a delivery direction, the plasma gas jet being substantially symmetrical about a jet axis; delivering particles into the plasma gas jet through at least a first carrier conduit to provide a melt, the first carrier conduit comprising a particle delivery vector that intersects the jet axis at an angle of not greater than 75 degrees, and further wherein the particle delivery vector comprises a vector component having a direction that is substantially opposite the delivery direction; and spraying and cooling the melt to provide amorphous material. Optionally, the method further comprises a second (third or more) carrier conduit for delivering particles into the plasma gas jet, the second (third or more) earner conduit may comprise a particle delivery vector that intersects the jet axis at an angle of not greater than 75 (in some embodiments, preferably, not greater than 70, 65, 60, 55, 50, 45, 40, 35, 30, 25,20, 15, 10. or even not greater than 5; in a range t'vom 75 to 60, 70 to 60, or 65 to 60) degrees, wherein the particle delivery vector of the second (third or more) carrier conduit comprises a vector component having a direction that is substantial!} opposite the delivery direction, and is different than the vector component of the first earner conduit. Although not wanting to be bound by theory, it is believed that the use of specified angle desirably changes (e.g., increases) the residence time or the interaction of the feed particles in the plasma, wherein residence time increases, for example as the angle decreases. In another aspect, the present invention provides a method for making amorphous material, the method comprising: generating a plasma gas jet in a delivery direction, the plasma gas jet being substantially symmetrical about a jet axis that extends along the delivery direction; delivering particles entrained in a carrier gas into the plasma gas jet to provide a melt, the carrier gas comprising at least 50 (in some embodiments, preferably at least 55, 60, 65, 70, 75, 80, 85, 90, 95, or even at least 100) percent by volume nitrogen, based on the total weight of the carrier gas, and the particles comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight ANO;„ based on the total weight of the particles, and a metal oxide other than AN03 (e.g., Y203, REO, ZrO., Ti02l CaO, Cr:03l MgO, NiO, CuO, and complex metal oxides thereof), wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5,4, 3, 2, 1, or zero) percent by weight collectively AS2O3, B;0;;, GeO:, P:Oj, SiOi, TeO:, and V:05, based on the total weight of the particles, with the proviso that if the metal oxide other than AI2O3 is Zr02, then the particles further comprises a metal oxide other than AI2O3 and ZrO;; and spraying and cooling the melt to provide amorphous material, the amorphous material comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight AI2O3. based on the total weight of the amorphous material, and the metal oxide other than AI2O3, wherein the amorphous material contains not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zero) percent by weight collectively AsiOj, B203, GcOi, P2O5, SiO?, Te02, and V2O5, based on the total weight of the amorphous material, wherein the amorphous material has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 1, 5, 10, 25 micrometers (in some embodiments, preferably, at least at least 30 micrometers, 35 micrometers, 40 micrometers. 45 micrometers, 50 micrometers, 75 micrometers, LOO micrometers. 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, I mm, 5 mm, or even at least 10 mm), with the proviso that if the metal oxide other than AhO.i is Zr02, then the particles further comprises a metal oxide other than ANO; and Zr02 that forms at least one distinct crystalline phase when the amorphous material is crystallized. Surprisingly, it was found that when nitrogen is used to deliver the particles, the size of the plasma jet increases significantly. The larger plasma jet size is beneficial, for example, because it tends to lead to increased residence time of the feed particles in the plasma jet, and thus enhanced, often desirable heat transfer to the particles, which in turn tends to lead to more complete and homogeneous melt formation, and a denser and stronger plasma sprayed material. In another aspect, the present invention provides_a method for making glass, the method comprising: generating a plasma gas jet in a delivery direction, the plasma gas jet being substantially symmetrical about a jet axis that extends along the delivery direction; delivering particles entrained in a earner gas into the plasma gas jet to provide a melt, the carrier gas comprising at least 50 (in some embodiments, preferably at least 55, 60, 65, 70, 75, 80, 85, 90, 95, or even at least 100) percent by volume nitrogen, based on the total weight of the carrier gas, and the particles comprising at least 35 (in =ome embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight A1203, based on the total weight of the particles, and a metal oxide other than AhOj (e.g., Y2O3, REO, Zr02, TiO;. CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3,2, 1, or zero) percent by weight collectively AsiOj, BzO-J% Ge02, P2O5, S1O2. Te02, and V205, based on the total weight of the particles; and spraying and cooling the melt to provide glass, the glass comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65. or even at least 70) percent by weight Al203, based on the total weight of the glass, and the metal oxide other than AI2CK. wherein the "lass contains not more than 10 (in some embodiment nn=f>nthiv not more than 5,4, 3, 2, 1, or zero) percent by weight collectively As203, B203, Ge02, P205, SiO;, Te02, and V:05, based on the total weight of the glass. In some embodiments, the glass hasx.y, and z dimensions each perpendicular to each oilier, and wherein each of the x, y. and z dimensions is at least I, 5, 10, 25 micrometers (in some embodiments, preferably, at least at least 30 micrometers, 35 micrometers, 40 micrometers, 45 micrometers, 50 micrometers, 75 micrometers, 100 micrometers, 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm, 5 mm, or even at least 10 mm. Surprisingly, it was found that when nitrogen is used to deliver the particles, the size of the plasma jet increases significantly. The larger plasma jet size is beneficial, for example, because it tends to lead to increased residence time of the feed particles in the plasma jet, and thus enhanced, often desirable heat transfer to the particles, which in turn tends to lead to more complete and homogeneous melt formation, and a denser and stronger plasma sprayed material. In another aspect, the present invention provides a method for making amorphous material, the method comprising: generating a plasma gas jet in a delivery direction, the plasma gas jet being substantially symmetrical about a jet axis that extends along the delivery direction; delivering particles entrained in a carrier gas into the plasma gas jet to provide a melt, the carrier gas comprising at least 50 (in some embodiments, preferably at least 55, 60, 65, 70, 75, 80, 85, 90, 95, or even at least 100) percent by volume nitrogen, based on the total weight of the carrier gas, and the particles comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight A1203, based on the total weight of the particles, a first metal oxide other than AhOj, and a second, different metal oxide other than AI203 (e.g., Y203, REO, ZrO;, Ti02, CaO, Ci":03. MgO, NiO, CuO, and complex metal oxides thereof), wherein the AI2O3, first metal oxide, and second metal oxide collectively comprise at least 80 (in some embodiments, preferably, at least 85, 90, 95, 97, 98, 99, or even 100) percent by weight of the particles, and wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zero) percent by weight collectively As203, B203, Ge02, P20;. Si02. Tc02, and V2O5, based on the total weight of the particles, with the proviso that if the first or second metal oxide other is Zr02, then the panicles fuithcr comprises a metal oxide other than A1203 and Zr03 that at least a portion of w htch forms a distinct crystalline phase when the amoiphous material is crystallized; and spraying and cooling the melt to provide amorphous material, the amorphous material comprising at icast 35 (in some embodiments. preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight AI2O3, based on the total weight of the amorphous material, the first metal oxide other than AI2O3, and the second, different metal oxide other than AI1O3, wherein the AI2O3, first metal oxide, and second metal oxide collectively comprise at least SO (in some embodiments, preferably, at least 85, 90, 95, 97, 98,99, or even 100) percent by weight of the amorphous material, wherein the amorphous material contains not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, I, or zero) percent by weight collectively As203,B203, GeO;, P2O5, SiO;, TeO;, and V1O5, based on the total weight of the amorphous material, with the proviso that if the first or second metal oxide is ZrOi, then the amoiphous material further comprises a metal oxide other than AI2O3 and ZrOj at least a portion of which forms at least one distinct crystalline phase when the amoiphous material is crystallize. Surprisingly, it was found that when nitrogen is used to deliver the particles, the size of the plasma jet increases significantly. The larger plasma jet size is beneficial, for example, because it tends to increased residence time of the feed particles in the plasma jet, and thus enhanced, often desirable heat transfer to the particles, which in turn tends to lead to more complete and homogeneous melt formation, and a denser and stronger plasma sprayed material. Optionally, the amorphous material made according to methods of the present invention may be present as part of ceramic material (i.e., the method may make ceramic comprising the amorphous material. In another aspect, in some embodiments, the spraying and cooling of the melt of methods according to the present invention includes spraying the melt onto a substrate and cooling to provide the amoiphous material In another aspect, in some embodiments, the spraying and cooling of the melt of methods according to the present invention includes spraying the melt into a liquid to cool the melt and provide panicles comprising the amorphous material. The latter may provides beads comprising ihe amorphous material (including 100 percent amoiphous beads.). Methods according to the present invention optionally further comprise heating the amorphous material such that that at least a portion of the amorphous material is converted to a glass-ceramic. In this application: "amorphous material" refers to material derived from a melt or a \apor phase that lacks any long range crystal structure as determined by X-ray diffraction and/or has an exothermic peak corresponding to the crystallization of the amoiphous material as determined by a DTA (differential thermal analysis) as determined by the test described herein entitled "Differential Thermal Analysis"; "ceramic" includes amoiphous material, glass, crystalline ceramic, glass-ceramic, and combinations thereof; "complex metal oxide" refers to a metal oxide comprising two or more different metal elements and oxygen (e.g., CcAh jO|S, Dy3AI;Oi2, MgAI;04, and Y3AI5O12); "complex Al;0_i •metal oxide" refers to a complex metal oxide comprising, on a theoretical oxide basis, AI2O3 and one or more metal elements other than Al (e.g., CcAl iiO[S, Dy3Al50,2, MgAI:04, and Y3AI5O1:): 'complex AhO.i* Y;0;s" refers to a complex metal oxide comprising, on a theoretical oxide basis, ANO.i and Y2O3 (e.g., Y3AI5O12); "complex AIJO.T-REO" refers to a complex metal oxide comprising, on a theoretical oxide basis, AI2O3 and rare earth oxide (e.g., CeAInds and Dy^AljOii); "glass" refers to amoiphous material exhibiting a glass transition temperature; "glass-ceramic" refers to ceramics comprising crystals formed by heat-treating amorphous material; "T:" refers to the glass transition temperature as determined by the test described herein entitled "Differential Thermal Analysis"; "T^" refers to the crystallization temperature as determined by the test described herein entitled "Differential Thermal Analysis"; "rare earth oxides" refers to cerium oxide (e.g.,CeOi), dysprosium oxide (e.g., Dy:Oj), erbium oxide (e.g., Ei'203), europium oxide (e.g., EuiOj), gadolinium (e.g., GdiO;,), holmium oxide (e.g., H02O3), lanthanum oxide (e.g., La^O^), lutctium oxide (e.g., LU2O3}, neodymium oxide (e.g., Nd20;), praseodymium oxide (e.g., Pr()Ou). samarium oxide (e.g., Sm;03), [erbium (eg-, Tb203), thorium oxide (e.g., Tin07), thulium {e.g., Tm20:,), and ytterbium oxide (e.g., Yb:03), and combinations thereof; and "REO" refers to rare earth oxide(s). Further, it is understood herein that unless it is stated that a metal oxide (e.g., ANOj, complex ANOs'inetal oxide, etc.) is crystalline, for example, in a glass-ceramic, it may be amorphous, crystalline, or portions amorphous and portions crystalline. For example if a glass-ceramic comprises AI2O3 and ZrO:, the AI2O3 and ZrO; may each be in an amorphous state, crystalline state, or portions in an amorphous state and portions in a crystalline state, or even as a reaction product with another metal oxide(s) (e.g., unless it is stated that, for example, AI2O3 is present as crystalline AI1O3 or a specific crystalline phase of AI2O3 (e.g., alpha AI2O3), it may be present as crystalline AI2O3 and/or as part of one or more crystalline complex Al203*metal oxides. Further, it is understood that glass-ceramics formed by heating amorphous material not exhibiting a T„ may not actually comprise glass, but rather may comprise the crystals and amorphous material that docs not exhibiting a T,,, Embodiments of coatings prepared according to the present invention may be useful, for example, as abrasion-, corrosion-, oxidation-resistant, and/or thermal-barrier coatings. Some embodiments of coatings prepared according to the present invention may be useful as components in electrochemical devices (e.g. fuel cell electrolytes with higher ionic conductivity compared to conventional YSZ (yttria. stabilized zirconia) and/or electrodes). Bulk forms prepared according to the present invention may be useful, for example, for structural applications {e.g., engine components, cutting tool inserts, medical implants, surgical instruments, substrates, and crucibles), and reinforcing members. Examples of articles according of the present invention include kitchenware (e.g., plates), denial brackets, and reinforcing fibers, cutting tool inserts, abrasive materials, and structural components of gas engines, (e.g., valves and bearings). Other articles include those having a protective coating of ceramic on the outer surface of a body or other substrate. Embodiments may also be useful, for example, as abrasive particles. The abrasive particles may be incorporated into abrasive articles or utilized in loose form, such as in slurries of abrading compounds (e.g., polishing compounds), milling media, shot blast media, and vibratory mill media. Brief Description of (he Drawing FIG. 1 is a fragmentary cross-sectional .schematic view of a coated abrasive article including abrasive particles made according to a method of the present invention; FIG. 2 is a perspective view of a bonded abrasive article including abrasive particles made according to a method of the present invention; FIG. 3 is an enlarged schematic view of a nonwoven abrasive article including abrasive particles made according to a method of the present invention; FIG. 4 is a schematic of an exemplary plasma spray apparatus for practicing embodiments of the present invention; FIG. 5 Scanning Electron Micrograph (SEM) of fractured surface of material prepared in Example 1; and FIG- 6 Scanning Electron Micrograph (SEM) of fractured surface of material prepared in Example 3. Detailed Description An exemplary, and in some embodiments preferred, thermal spray or plasma spray apparatus 400 including plasma spray gun 401 is diagrammatically illustrated in FIG. 4. Plasma spray gun 401, generally, is adapted to generate plasma gasjet 416 substantially symmetric about jet axis 417. Plasma gasjet 416 contains mcta! oxide droplets 407. Plasma spray gun 401 includes housing 403 having nozzle 402 located therein. Nozzle 402 forms nozzle bore 405 adapted to direct and focus plasma gas jet 416 in a delivery direction 418. To produce plasma gas jet 416, plasma spray gun 401 includes various electrodes. For example, in the illustrated embodiment of FIG. 4, first electrode 404 is located proximate an entrance to nozzle 402 and is configured as a cathode (e.g., connected to a negative terminal of a power supply (not shown)). Nozzle 302 may itself form second electrode 402' configured as an anode (e.g., connected to a positive terminal of the power supply). While the actual materials used to form first and second electrodes 404 and 402' may vary, one exemplary embodiment of plasma spray gun 401 utilizes first electrode 404 made from tungsten or tungsten alloy and second electrode 402' (nozzle 402) made from copper or copper alloy. Those of skill in the art will realize that this electrode configuration is merely exemplary and that other electrode configurations are certainly possible. For example, the polarity and/or material of the first and second electrodes may be different that described above. Alternatively, for example, second electrode 402' may be independent of nozzle 402. In fact, most any electrode configuration that yields an acceptable plasma spray is possible without departing from the scope of the invention-Arc gas inlet 414 may be provided to allow for the introduction of arc gas 410 into gas chamber 412 of housing 403. While most any gas complimentary to arc formation is potentially suitable, preferred arc gases include argon, helium, hydrogen, nitrogen, and combinations thereof. One or more carrier conduits 420 may be formed in housing 403. As further described below, carrier conduits 420 may deliver particles 430 to plasma gas jet 416. While the actual geometry of earner conduits 420 may vary, they are, in one embodiment, formed by holes drilled to intersect nozzle bore 405. In the illustrated embodiment, each earner conduit 420 intersects bore 405 at or proximate the smallest diameter of bore 405. One or more carrier conduits 420 are each preferably symmetric about conduit axis 422. Each conduit axis 422 may intersect jet axis 417 at angle 424 of 75 degrees or less, wherein one or more carrier conduits 420 diverge or extend away from jet axis 417 in delivery direction 418. In some embodiments, angle 424 is preferably 45 degrees to 75 degrees, and more preferably, 60 degrees to 75 degrees; Other configurations of carrier conduits 420 are also possible without departing from the scope of the invention. For example, conduits 420 may have other (e.g., non¬linear) shapes, or they may penetrate bore 405 at a point offset from its centerline. These and other conduit configurations are certainly possible if they are operable to direct particles within conduit 420 to plasma gas jet 416 aiong particle delivery vector 426, where; particle delivery vector 426 intersects jet axis 417 at angle 424 of 75 degrees or less; and the particle delivery vector 426 comprises vector component 426' having a direction that is substantially opposite delivery direction 418. Once again, in some embodiments, angle 424 is preferably 45 degrees to 75 degrees, and more preferably, 60 degrees to 75 degrees. Although the term "intersects" is used herein, those of skill in the art will realize that conduit axis 422 may not necessarily be coplanar with jet axis 417 {e.g., one may be skewed with respect to the other). In these instances, it is understood that "intersects" indicates angle 424 between the two axes when the axes arc moved parallel to themselves to a common point of intersection. Having described plasma gas jet 401 in detail, operation of the same in accordance with an exemplary embodiment of the present invention is now described. Arc gas 410 may be introduced into chamber 412 and accelerated through converging bore 405 of nozzle 402 as described above. When first electrode 404 and second electrode 402' are coupled to respective terminals of a power supply, an electric field is created between first electrode 404 and nozzle 402. The resulting plasma gas jet 416 exits housing 403 in delivery direction 418 alongjet axis 417, the latter which is substantially parallel and coaxial to axis 406 of nozzle 402. A cooling system, represented by arrows 408 in FIG. 4, may be activated to maintain the temperature of housing 403 at the desired levels. To generate the desired spray of droplets 407, particles 430 are delivered to the plasma gas jet 416 through earner conduits 420. In one embodiment, the particles 430 are entrained in a earner "as that travels through carrier conduits 420 toward the nozzle bore 405. While nitrogen is preferred, other carrier gases may be used. When the metal oxide particles 430 reach plasma gas jet 416, at least a portion are at least partially liquefied to form the desired droplets 407. Droplets 407 may then be cooled and deposited on a substrate or otherwise collected. By orienting carrier conduits 420 as shown and described herein, particles 430 achieve increased residence time within plasma gas jet 416. This longer residence time allows for the production of courser droplets 407 when compared to droplets produced by existing apparatus and methods. For embodiments of the invention that do not specify a particular composition particles, any of a variety particulate feed may be used, including amorphous materials, cciamics, metals, etc.. known in the art for plasma spraying. Similarly, for some embodiments of the present invention any of a variety of plasma spraying techniques known in the art may be suitable. In some embodiments, feed particles for methods according to the present invention, as well as for use with apparatuses according to the present invention include those comprising at least 35 (in some embodiments, preferably at least 40, 45. 50, 55, 60, 65, or even at least 70) percent by weight AI2O3, based on the total weight of the particles, and a metal oxide other than Al205 (e.g., Y203, REO, Zr02, TiO;, CaO, Cr30.5, MgO, NiO, CuO, and complex metal oxides thereof), wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5,4, 3, 2,1, or zero) percent by weight collectively As:03, B205, Ge02, P;0Sl SiOi. Te02> and V2Os, based on the total weight of the particles, with the proviso that if the metal oxide other than AI2O3 is Z1O2, then the panicles further comprises a metal oxide other than AI2O3 and Z1O2. Embodiments of amorphous material made from such panicles comprise at least 35 (in some embodiments, preferably at least 40,45,50,55,60,65, or even at least 70) percent by weight Al20.i, based on the total weight of the amorphous material, and the metal oxide other than Al20.-i (e.g., Y203, REO, Zi02, TiOj, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), wherein the amorphous material contains not more than 10 (in some embodiments, preferably not more than 5,4,3,2,1, or zero) percent by weight collectively As203, B:03, GcO;, P205, Si02, Te02, and V205, based on the total weight of the amorphous material, wherein the amorphous material has x, y, and z dimensions each perpendicular to each oilier, and wherein each of the x, y, and z dimensions is at least 1, 5, 10,25 micrometers (in some embodiments, preferably, at least at least 30 micrometers, 35 micrometers, 40 micrometers, 45 micrometers, 50 micrometers, 75 micrometers, 100 micrometers, 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm, 5 mm, or even at least 10 mm), with the proviso that if the metal oxide other than Al2Q3 is Z1O2, then the amorphous material further comprises a metal oxide other than AI1O3 and Zr02 that forms at least one distinct crystalline phase when the amorphous material is crystallized. Optionally, if the amorphous material is heat-treated, the invention can provide a glass- ceramic comprising at least 35 (in some embodiments, preferably at least 40,45, 50, 55, 60, 65, or even at least 70) percen t by weight Al203, based on the total weight of the glass- ceramic, and the metal oxide other than AI2O3, wherein the glass-ceramic contains not more than 10 in some embodiments, preferably not more than 5 a 1 "> 1 nr-**^ by weight collectively As203, B203, Ge02, P205, SiO:, TeO:, and V203, based on the total weight of the glass-ceramic, wherein the glass-ceramic has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 25 micrometers (in some embodiments, preferably, at least at least 30 micrometers, 35 micrometers, 40 micrometers, 45 micrometers, 50 micrometers, 75 micrometers, 100 micrometers, 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micro meters, 2500 micrometers, I mm,-5 mm, or even at least 10 mm). In some embodiments, feed particles for methods according to the present invention, as well as for use with apparatuses according to the present invention include those comprising at least 35 (in some embodiments, preferably at least 40. 45, 50, 55, 60, 65, or even at least 70) percent by weight Al203, based on the total weight of the particles, a first metal oxide other than A1203 (e.g., Y203, REO, Zr02, TiO:, CaO, Cr203( MgO, NiO, CuO, and complex metal oxides thereof), and a second, different metal oxide other than AhOj (e.g., Y203, REO, Zr02, Ti02( CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), wherein the Al20;;, first metal oxide, and second metal oxide collectively comprise at least 80 (in some embodiments, preferably, at least 85, 90, 95, 97, 9S, 99, or even 100) percent by weight of the particles, and wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zero) percent by weight collectively As203, B203, Ge02, P2O5, Si02, Te02, and V205, based on the total weight of the particles, with the proviso that if the first or second metal oxide other is Zr02, then the particles further comprises a metal oxide other than Al2Or, and Zi02 that at least a poi'tion of which forms a distinct crystalline phase when the amorphous material is crystallized. Embodiments of amorphous material made from such particles comprise at least 35 (in some embodiments, preferably at least 40,45, 50, ?5,60, 65, or even at least 70) percent by weight Ali03, based on the total weight of the amorphous material, the first metal oxide other than A1203 (e.g., Y203, REO, Zr02, TiO:, CaO, Cr203l MgO, NiO, CuO. and complex metal oxides thereof), and the second, different metal oxide other than A120:, (e.g., Y203, REO, Zr02, Ti02, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), wherein the A1203, first metal oxide, and second metal oxide collectively comprise at least 80 (in some embodiments, preferably, at least 85, 90, 95, 97, 98, 99, or even J 00) percent by weight of the amorphous material, wherein the amorphous material contains not more than JO fin some embodiments, preferably not more than 5. 4, 3, 2, 1, or zero) percent by weight collectively AS2,, B2O3, Gc02. P2O5, SiO;, TcO:, and VSOj, based on the total weight of the amorphous material- Optionally, if the amorphous materia! is heat-treated, the invention can provide a glass-ceramic comprising comprise at least 35 (in some embodiments, preferably at least 40, 45, 50, 55. 60, 65, or even at least 70) percent by weight AI2O3, based on the total weight of the glass-ceramic, the first metal oxide other than AI2O3, and the second, different metal oxide other than AI;Oj, wherein the AI2O3, first metal oxide, and second metal oxide collectively comprise at least SO (in some embodiments, preferably, at least 85, 90, 95, 97, 98, 99, or even 100) percent by weight of the glass-ceramic, wherein the glass-ceramic contains not more than 10 (in some embodiments, preferably not more than 5,4, 3, 2, 1, or zero) percent by weight collectively As:03, B2O3, Ge02, P2O5, SiOi, Te02l and V205, based on the total weisht of the glass-ceramic. Sources, including commercial sources, of (on a theoretical oxide basis) AI1O3 include bauxite (including both natural occurring bauxite and synthetically produced bauxite), calcined bauxite, hydra ted aluminas (e.g., boehmite, and gibbsitc), aluminum, Bayer process alumina, aluminum ore, gamma alumina, alpha alumina, aluminum salts, aluminum nitrates, and combinations thereof. The AI2O3 source may contain, or only provide. Al:03. Alternatively, the AI2O3 source may contain, or provide AI2O3, as well as one or more metal oxides other than AI2O3 (including materials of or containing complex Al203»metal oxides (e.g., Dy3Al5Oi2,Y3Al50i2,CeAliiOi8, etc.))- Sources, including commercial sources, of rare earth oxides include rare earth oxide powders, rare earth metals, rare earth-containing ores {e.g., bastnasite and monazite), rare earth salts, rare earth nitrates, and rare earth carbonates. The rare earth oxide(s) source may contain, or oniy provide, rare earth oxide(s). Alternatively, the rare earth oxide(s) source may contain, or provide rare earth oxide(s), as well as one or more metal oxides other than rare earth oxide(s) (including materials of or containing complex ruvc earth oxideother metal oxides (e.g., Dy:,A!jO)2, CcAlnOis, etc.)). Sources, including commercial sources, of (on a theoretical oxide basis) Y2O3 include ytmum oxide powders, yttrium, yttrium-containing ores, and yttrium salts (e.g., yttrium carbonates, nitrutcs, chlorides, hydroxides, and combinations thereof). The Y2O3 source may contain, or only provide, Y2O3. Alternatively, the Y20:, source may contain, or provide Y2O3. as well as one or more metal oxides other than Y1O3 (including materials of or containing complex Y20.vmetal oxides (e.g., Y3AI5O12)). Sources, including commercial sources, of (on a theoretical oxide basis) Z1O2 include zirconium oxide powders, zircon sand, zirconium, zirconium-containing ores, and zirconium salts (e.g., zirconium carbonates, acetates, nitrates, chlorides, hydroxides, and combinations thereof). In addition, or alternatively, the Zr(> source may contain, or provide ZrOi, as well as other metal oxides such as hafnia. Sources, including commercial sources, of {on a theoretical oxide basis) Hf02 include hafnium oxide powders, hafnium, hafnium-containing ores, and hafnium salts. In addition, or alternatively, the HfOj source may contain, or provide Hf02, as well as other metal oxides such as Zr02. Other useful metal oxide may also include, on a theoretical oxide basis, BaO, CaO, Cr203, CoO, Fe203, Ge02, Li20, MgO, MnO. NiO, Na2G, Sc203, SrO, Ti02, ZnO, and combinations thereof. Sources, including commercial sources, include the oxides themselves, complex oxides, ores, carbonates, acetates, nitrates, chlorides, hydroxides, etc. These metal oxides are added to modify a physical property of the resulting abrasive particles and/or improve processing. These metal oxides are typically are added anywhere from 0 to 50% by weight, in some embodiments preferably 0 to 25% by weight and more preferably 0 to 50% by weight of the glass-ceramic depending, for example, upon the desired property. In some embodiments, it may be advantageous for at least a portion of a metal oxide source (in some embodiments, preferably, 10 15, 20, 25, 30, 35, 40, 45, or even at least 50 percent by weight) to be obtained by adding particulate, metallic material comprising at least one of a metal (e.g., Al, Ca, Cu, Cr, Fe, Li, Mg, Ni, Ag, Ti, Zr, and combinations thereof), M, that has a negative enthalpy of oxide formation or an alloy thereof to the melt, or otherwise metal them with the other raw materials. Although not wanting to be bound by theory, it is believed that the heat resulting from the exothermic reaction associated with the oxidation of the metal is beneficial in the formation of a homogeneous melt and resulting amorphous material. For example, u is believed that the additional heat generated by the oxidation reaction within the raw material eliminates or minimizes insufficient heat transfer, and hence facilitates formation and homogeneity of the melt, particularly when forming amorphous particles with \, y, and z dimensions over 150 micrometers. It is also believed that the availability of the additional heat aids in driving various chemical reactions and physical processes (e.g., densification. and sphcrodization) to completion. Further, it is believed for some embodiments, the presence of the additional heat generated by the oxidation reaction actually enables the formation of a melt, which otherwise is difficult or otherwise not practical due to high melting point of the materials. Further, the presence of the additional heat generated by the oxidation reaction actually enables the formation of amorphous material that otherwise could not be made, or could not be made in the desired size range. Another advantage of the invention include, in forming the amorphous materials, that many of the chemical and physical processes such as melting, densification and sphcrodizing can be achieved in a short time, so that very high quench rates be can achieved. For additional details, see copending application having U.S. Serial No. 10/211,639, filed August 2, 2002. The feed particles for carrying out the process of the invention can be of a variety of sizes, although typically the feed particles have an average size below 100 micrometers, typically in a range of 20-40 micrometers. Excessively small particles can be undesirably difficult lo handle, while panicles that are loo coarse may not completely or uniformly melt. The feed particles can be agglomerated together into particles (i.e., the various raw materials arc agglomerated together into particles). Particles made, for example, by plasma spraying or a flame forming process can also be used as feed particles. Surprisingly, amorphous particles generated by plasma sphcrodization, or flame forming processes arc particularly useful feed panicles, even with diameters larger than 100 micrometers. Further, for example, the f^ccd particles maybe prepared by dry milling raw materials to provide the desired particle size and/or uniformly of mixture. Particulate, including milled material may be made into a slurry and spray dried to provide feed particles. The feed panicles can also be screened to provide a desired particle size distribution. Further with regard to generating a plasma and melting the feed particles a variety of DC, AC. RF plasma processing systems can be used. For some embodiments, it is preferred thai there is sufficient power to uniformly and completely melt the feed particles. Suitable plasma systems useful for the invention typically have about 40 k\V of power although smaller or larger systems may be useful depending, for example, on the production demands. Gases for generating the plasma include those known in the art such as argon, helium, nitrogen, hydrogen, and mixtures thereof. Most commonly, argon gas is used as the plasma gas, but to increase the enthalpy (i.e., the heat content of the plasma, one or more of helium, hydrogen, or nitrogen) may also be added. The feed panicles are commonly introduced into the plasma by a carrier gas. Gases for delivering the feed particles to the plasma gas jet include argon, helium, nitrogen, and mixtures thereof. The earner gas maybe same as the plasma gas (i.e., argon) or it may provide the second or the third gas to modify the energetics of the plasma. Surprisingly, it was found that when nitrogen is used to deliver the particles, the size of the plasma jet increases significantly. The larger plasma jet size is beneficial, for example, because it tends to increased residence time of the feed particles in the plasma jet, and thus enhanced, often desirable heat transfer to the particles, which in turn tends to lead to more complete and homogeneous melt formation, and a denser and stronger plasma sprayed material. It is also possible, for example, to introduce the fed into the plasma along the axis of the plasma jet in the particulate form or as a feed stick (the feed material is formed in to a rod shape and is fed into the plasma slowly as the tip of the rod is molten and broken into droplets, which are then sprayed by the plasma jet) In some embodiments, the feed particles can be introduced into the plasma just outside of the gun. Although not wanting to be bound by theory, it is believed that feeding the feed particles into the plasma through an orifice machined in the anode of the plasma gun desirably increases the residence time or the interaction of the particles in the plasma, fn another aspect, some cases, although not wanting to be bound by theory, it is believed that the residence time or the interaction of the feed particles in the plasma may be desirably changed (e.g., increased) by orienting the orifice towards the front or back of the gun at an angle (e.g., at least 10, 20 or 30 degrees, etc.). In another aspect of the invention, the plasma processing may be carried out in air, in a blanket of gasses, at higher or lower pressures, even under vacuum. The melt from the plasma is typically sprayed onto a substrate or into a liquid (e.g., water), although the liquid may also be on a substrate. The substrate or liquid aid in cooling the melt. In some cases, it is desirable to provide a coating onto a substrate. In other cases, the substrate may be merely serving to cool and collect material which is subsequently removed from the substrate (e.g., bulk material is provided). It is understood that then substrate is selected to be of sufficient integrity to withstand the heat from the plasma. Common substrate materials are metals and ceramics.. With regard to using liquid to cool the plasma sprayed melt, the result is typically particulate, most commonly in the form of spheres or beads (e.g., in some embodiments having a diameter(s) in a range from about 1, to at least 150 micrometers). Although for some embodiments of the invention that specify particular compositions of the particles, embodiments are directed to amorphous materials, for those not specifying particular compositions, the resulting plasma sprayed material may be amorphous material or crystalline material (including nanosized crystal and coarser). Surprisingly, embodiments of the present invention can provide amorphous materials having x, y, and i dimensions each perpendicular to each other, wherein each of the x, y, and z dimensions is at least 1, 5, 10, 25 micrometers (in some embodiments, preferably, at least at least 30 micrometers, 35 micrometers, 40 micrometers. 45 micrometers, 50 micrometers, 75 micrometers, 100 micrometers, 150 micrometers, 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm, 5 mm, or even at least 10 mm). The mici'ostructure or phase composition (glassy/amorphous/crysiallinc) of a material can be determined in a number of ways. Various information can be obtained using optical microscopy, electron microscopy, differential thermal analysis (DTA), and x-ray diffraction (XRD), for example. Using optical microscopy, amorphous material is typically predominantly transparent due to the lack of light scattering centers such as crystal boundaries, while crystalline materia! shows a crystalline structure and is opaque due to light scattering effects. A percent amorphous yield can be calculated for beads using a -lOO-j-120 mesh size traction (i.e., the fraction collected between 150-micrometer opening size and 125- micrometer opening size screens). The measurements arc done in the following manner. A single layer of beads is spread out upon a glass slide. The beads are observed using an optical microscope. Using the crosshairs in the optical microscope eyepiece as a guide, beads that lay along a straight line are counted either amorphous or crystalline depending on their optical clarity. A total of 500 beads are counted and a percent amorphous yield is determined by the amount of amorphous beads divided by total beads counted. , Using DTA. the material is classified as amorphous if the corresponding DTA trace of the material contains an exothermic crystallization event (Tx). If the same trace also contains an endothermic event (T„) at a temperature lower than T, it is considered to consist of a glass phase. If the DTA trace of the material contains no such events, it is considered to contain crystalline phases. Differential thermal analysis (DTA) can be conducted using the following method. DTA runs can be made (using an instrument such as that obtained from Netzsch Instruments, Selb, Germany under the trade designation "NETZSCH STA 409 DTAATGA") using a -140+170 mesh size fraction (i.e., the fraction collected between 105-micromcter opening size and 90-micrometer opening size screens). An amount of each screened sample (typically about 400 milligrams (mg)) is placed in a 100-microliter AIJJOJ sample holder. Each sample is heated in static air at a rate of 10°C/minute from room temperature (about 25°C) to 1100°C. Using powder x-ray diffraction, XRD, (using an x-ray diffractometer such as that obtained under the trade designation "PHILLIPS XRG 3100" from Phillips. Mahwah, NJ, with copper K al radiation of 1,54050 Angstrom) the phases present in a material can be determined by comparing the peaks present in the XRD trace of the crystallized material to XRD patterns of crystalline phases provided in JCPDS (Joint Committee on Powder Diffraction Standards) databases, published by International Center for Diffraction Data. Furthermore, an XRD can be used qualitatively to determine types of phases. The presence of abroad diffused intensity peak is taken as an indication of the amorphous nature of a material. The existence of both a broad peak and well-defined peaks is taken as an indication of existence of crystalline matter within an amorphous matrix. For some uses of the plasma sprayed material, for example, abrasive particles and fillers, the as formed amorphous material or ceramic (including glass prior to crystallization) may be larger in size than that desired. The amorphous material or ceramic can be converted into smaller pieces using crushing and/or comminuting techniques known in the art, including roll crushing, canary milling, jaw crushing, hammer milling, ball milling, jet milling, impact crushing, and the like- hi some instances, it is desired to have two or multiple crushing steps. For example, after the ceramic is formed (solidified), it may be in a form larger man desired. The first crushing step may involve crushing these relatively large masses or "chunks" to form smaller pieces. This crushing of these chunks may be accomplished with a hummer mill, impact crusher or jaw crusher. These smaller pieces may then be subsequently crushed to produce the desired particle size distribution. In order to produce the desired particle size distribution (sometimes referred to as grit size oi' grade), it may be necessary to perform multiple crushing steps. In general the crushing conditions are optimized to achieve the desired particle shape(s) and particle size distribution. Resulting particles that are of the desired size may be recrushed if they are [oo large, or "recycled" and used as a raw material, for example, for plasma spraying-melting if they are too small. The shape of the ceramic (including glass prior to crystallization) may depend, for example, on the composition and/or microstmeturc of the ceramic, the geometry in which it was cooled, and the manner in which the ceramic is crushed (i.e., the crushing technique used). In general, where a "blocky" shape is preferred, more energy may be employed to achieve this shape. Conversely, where a "sharp" shape is preferred, less energy may be employed to achieve this shape. The crushing technique may also be changed to achieve different desired shapes. The resulting particle may have an average aspect ratio ranging from 1:1 to 5:1, typically 1.25:1 to 3:1 and preferably 1.5:1 to 2.5:1. It is also within the scope of the present invention, for example, to fabricate ceramics (including glass prior to crystallization) by coalescing. This coalescing step in essence forms a larger sized t^pdy from two or more smaller particles. For example, amorphous material comprising particles (obtained, for example, by crushing) (including beads and microspheres), fibers, etc. may formed into a larger particle size. For example, ceramic (including glass prior to crystallization), may also be provided by heating, for example, particles comprising the amorphous material, and/or fibers, etc. above the Ta such that the particles, etc. coalesce to form a shape and cooling the coalesced shape. The temperature and pressure used tor coalescing may depend, for example, upon composition of the amoiphous material and the desired density of the resulting material. The temperature should below glass crystallization temperature, and for glasses, greater than the glass transition temperature. In certain embodiments, the heating is conducted at at least one temperature in a range of about 850°C to about 1100"C (in some embodiments, preferably 900"C to 1000DC). Typically, the amorphous material is underpressure (e.g., greater than zero to 1 GPa or more) during coalescence to aid the coalescence of the amorphous material. In one embodiment, a charge of the particles, etc. is placed into a die and hot-pressing is performed at temperatures above glass transition where viscous flow of glass leads to coalescence into a relatively large part. Examples of typical coalescing techniques include hot pressing, hot isostatic pressure, hot extrusion and the like. Typically, it is generally preferred to cool the resulting coalesced body before further heat treatment. After heat treatment if so desired, the coalesced body may be crushed to smaller particle sizes or a desired particle size distribution. It is also within the scope of the present invention to conduct additional hcat-treatment to further improve desirable properties of the material. For example, hot-isostatic pressing may be conducted (e.g., at temperatures from about 900°C to about I400°C) to remove residual porosity, increasing the density of the material. Optionally, the resulting, coalesced article can be heat-treated to provide glass-ceramic, crystalline ceramic, or ceramic otherwise comprising crystalline ceramic. If a crystalline or partially crystalline material is desired, it is preferred to heat treat the amorphous material. Heat-treatment can be carried out in any of a variety of ways, including those known in the art for heat-treating glass to provide glass-ceramics. For example, heat-treatment can be conducted in batches, for example, using resistive, inductively or gas heated furnaces. Alternatively, for example, heat-treatment can be conducted continuously, for example, using rotary kilns. In the case of a rotary kiln, the material is fed directly into a kiln operating at the elevated temperature. The time at the elevated temperature may range from a few seconds (in some embodiments even less than 5 seconds) to a few minutes to several hours. The temperature may range anywhere from 900°Cto 1600°C, typically between 1200°C to I500°C. It is also within the scope of the present invention to perform some of the he at-treatment in batches (e.g., for the nucleation siep) and another continuously (e.g., for the crystal growth step and to achieve the desired density). For the nucleation step, the temperature typically ranges between about 900°C to about 1100°C, in some embodiments, preferably in a range from about 925~C to about 1050°C. Likewise for the density step, the temperature typically is in a range from about 1 W0°C to about 1600°C, in some embodiments, preferably in a range from about 1200°C to about 1500°C. This heat treatment may occur, for example, by feeding the material directly into a furnace at the elevated temperature. Alternatively, for example, the material may be feed into a furnace at a much lower temperature (e.g., room temperature) and then healed to desired temperature at a predetermined heating rate. It is within the scope of the present invention to conduct heat-trcatment in an atmosphere other than air. In some cases it might be even desirable to heat-treat in a reducing atmosphere(s). Also, for, example, it may be desirable to heat-treat under gas pressure as in, for example, hot-isostatic press, or in gas pressure furnace. It is within the scope of the present invention to convert (e.g., crush) the resulting article or heat-treated article to provide particles (e.g., abrasive particles). The amoiphous material is heat-treated to at least partially crystallize the amoiphous material to provide glass-ceramic. The heat-trcatment of certain glasses to i form glass-ceramics is well known in the art. The heating conditions to nucleate and grow glass-ceramics are known for a variety of glasses. Alternatively, one skilled in the art can determine the appropriate conditions from a Time-Temperature-Transformation (TTT) study of the glass using techniques known in the art. One skilled in the art, after reading the disclosure of the present invention should be able to provide TTT curves for amorphous materials made according to the present invention, determine the appropriate nuclealion and/or crystal growth conditions to provide glass-ceramics of the abrasive particles. Typically, glass-ceramics are stronger than the amoiphous materials from which they are formed. Hence, the strength of the material may be adjusted, for example, by the degree to which the amoiphous material is conveited to crystalline ceramic phase(s). Alternately, or in addition, the strength of the material may also be affected, for example, by the number of nucleation sites created, which may in turn be used to affect the number, tind in turn the siivc. of thf» fi-vcfttc ^F ti-i" "—"•»"";«—u„-~/-.\ r. • ••.- regarding forming glass-ceramics, see, for example Glass-Ceramics. P.W. McMillan, Academic Press. Inc., 2"d edition, 1979. For example, during heat-treat merit of some exemplary amorphous materials made according to methods according to present invention for making the glass-ceramics, formation of phases such as L^ZnO?, and, if ZrO: is present, cubic/tetragonal Z1O2, in some cases monoclinic ZrO:, have been observed at temperatures above about 900°C. Although not warning to be bound by theory, it is believed that zirconia-related phases are the first phases to nucleate from the amorphous material. Formation of Al203, ReAIOj (wherein Re is at least one rare earth cation), ReAlnOis, Rc3AIjO|2, Y3AI5O12, etc. phases arc believed to generally occur at temperatures above about 925CC. Typically, crystallite size during this nucleation step is on order of nanometers. For example, crystals as small as 10-15 nanometers have been observed. For at least some embodiments, heat-treatment at about 1300°C for about 1 hour provides a full crystallization. In generally, heat-treatment times for each of the nucleation and crystal growth steps may range of a few seconds (in some embodiments even less than 5 seconds) to several minutes to an hour or more. The size of the resulting crystals can typically controlled at least in part by the nucleation and/or crystallization times and/or temperatures. Although it is generally prcfeijcd to have small crystals (e.g., on the order not greater than a micrometer, or even not greater than a nanometer) the glass-ceramics may be made with larger crystal sizes (e.g., at least i-10 micrometers, at least 10-25 micrometers, at least 50-100 micrometers, or even greater than 100 micrometers). Although not wanting to be bound by theory, it is generally believed in the art that the finer the size of the crystals (for the same density), the higher the mechanical properties (e.g., hardness and strength) of the ceramic. Examples of crystalline phases which may be present in embodiments of glass-ceramics include: A1203 (e.g., a-Al203), Y;03, REO, Hf02 ZrO: (e.g., cubic Zr02 and tetragonal ZrO:). BaO. CaO, Cr203, CoO, Fe:03, GeO:, U20, MgO, MnO, NiO, Na20, P:05, Sc20:„ SiO:, SrO, TeO;, Ti02, V203, Y203, ZnO, "complex meta.1 oxides" (including "complex AhOj-meUil oxide (e.g., complex A^OyREO (e.g., ReAIOs (e.g., GdA103 LaAlO;), ReAln018 (e.g., LaAIM0|s.). and Re3AI50,2 (e.g., Dy3AI50i;)), complex Ai;Oy Y;0., (e.g., Y3AI5O12), and complex ZrOyREO (e.g., Rc:Z]';07 (e.g., LihZriO?))), MgAN04, TiAI^Os, and combinations thereof. It is also with in the scope of the present invention to substitute a portion of the yttrium and/or aluminum cations in a complex Al;0.vmetal oxide (e.g.. complex ANOyYiO;, (e.g.. yttrium aluminate exhibiting a garnet crystal structure)) with other cations. For example, a portion of the AI cations in a complex AbCvYiOj may be substituted with at least one cation of an element selected from the group consisting of: Cr, Ti, Sc, Fe, Mg. Ca, Si, Co, and combinations thereof. For example, a portion of the Y cations in a complex AI2O.VY1O3 may be substituted with at least one cation of an element selected from the group consisting of: Ce, Dy, Er, En, Gd, Ho. La, Lu, Nd, Pr, Sm, Th, Tm, Yb, Fe, Ti, Mn, V, Cr, Co, Ni, Cu, Mg, Ca, Sr, and combinations thereof. Similarly, it is also with in the scope of the present invention to substitute a portion of the aluminum cations in alumina. For example, Cr, Ti, Sc, Fe, Mg, Ca, Si, and Co can substitute for aluminum in the alumina. The substitution of cations as described above may affect the properties (e.g. hardness, toughness, strength, thermal conductivity, etc.) of the fused material. U is also with in the scope of the present invention to substitute a portion of the rare earth and/or aluminum cations in a complex AliOj-metal oxide (e.g., complex ANOyREO) with other cations. For example, a portion of the Ai cations in a complex AI203-REO may be substituted with at least one cation of an element selected from the group consisting of: Cr, Ti,Sc, Fe, Mg, Ca, Si, Co, and combinations thereof. For example, a portion of the Y cations in a complex AliOyREO may be substituted with at least one cation of an element selected from the group consisting of: Y, Fc,Ti,Mn, V, Cr, Co. Ni, Cu, Mg, Ca, Sr, and combinations thereof. Similarly, it is also with in the scope of the present invention to substitute a portion of the aluminum cations in alumina. For example, Cr, Ti, Sc, Fe, Mg, Ca, Si. and Co can substitute for aluminum in the alumina. The substitution of cations LIS described above may affect the properties (e.g. hardness, toughness, strength, thermal conductivity, etc.) of the fused material. The average crystal size can be determined by the line intercept method according to Uic ASTM standard E 112-96 "Standard Test Methods for Determining Average Grain Size". The sample is mounted in mounting resin (such as that obtained under the trade designation 'TRANSOPTIC POWDER" from Buehler, Lake Bluff, IL) typically in a cylinder of resin about 2.5 cm in diameter and about 1.9 cm high. The mounted section is prepared using conventional polishing techniques using a polisher (such as that obtained from Buehler. Lake Bluff. IL under the trade designation "ECOMET 3"). The sample is polished for about 3 minutes with a diamond wheel, followed by 5 minutes of polishing with each of 45. 30, L5, 9, 3, and 1-micromcter slurries. The mounted and polished sample is sputtered with a thin layer of gold-palladium and viewed using a scanning electron microscopy (such as the JEOL SEM Model JSM S40A). A typical back-scattered election (BSE) micrograph of the micros tructure found in the sample is used to determine the average crystal size as follows. The number of crystals that intersect per unit length (NL) of a random straight line drawn across the micrograph are counted. The average crystal size is determined from this number using the following equation. Average Crystal Size = —:— NLM Where NL is the number of crystals intersected per unit length and M is the magnification of the micrograph. Some embodiments of" the glass-ceramics include glass-ceramics comprising alpha alumina having at least one of an average crystal size not greater than 150 nanometers. Some embodiments of the glass-ceramics include glass-ceramics comprising alpha alumina, wherein at least 75 (in some embodiments preferably, 80, 85, 90, 95, or even 100) percent by number of the alpha alumina present in such portion have crystal sizes not greater than 200 nanometers. Some embodiments of the glass-ceramics include glass-ceramics comprising alpha AI2O5, crystalline ZrOz, and a first complex AI2O3-Y2O3, and wherein at least one of the alpha AI;03, the crystalline Z1O2, or the first complex AliOyYiOj has an average crystal size not greater than 150 nanometers. In some embodiments preferably, the glass-ceramics further comprise a second, different complex AhOyY2C>3. In some embodiments preferably, the glass-ceramics further comprise a complex AI2O3REO. Some embodiments of the glass-ceramics include glass-ceramics comprising a first complex Al;03-Y;03, a second, different complex AbCVYjOj, and crystalline ZrO?, and wherein lor at least one of the first complex AliOyY^, the second complex ANOJ-YJOJ, or the crystalline Zr02, at least 75 (in some embodiments preferably, SO, 85. 90, 95, or even 100) percent by number of the crystal sizes thereof are not greater than 200 nanometers. In some embodiments preferably, the glass-ceramics further comprise a second, different complex AI2OyY203. In some embodiments preferably, the glass-ceramics further comprise a complex AI2O3-REO. Some embodiments of the glass-ceramics include glass-ceramics comprising alpha Al;0_-i, crystalline Zr02, and a first complex AI2OyREO, and wherein at least one of the alpha AhOj, the crystalline Zr02, or the first complex AhOj'REO has an average crystal size not greater than 150 nanometers. In some embodiments preferably, the glass-ceramics further comprise a second, different complex Al20yREO. In some embodiments preferably, the glass-ceramics further comprise a complex AUCVYjO-s. Some embodiments of the glass-ceramics include glass-ceramics comprising a first complex AI2O3REO, a second, different complex AI2O3-REO, and crystalline Zr02, and wherein for at least one of the first complex AlzC^REO, the second complex AhOj-REO, or the crystalline ZrCh, at least 75 (in some embodiments preferably, 80, 85, 90, 95, or even 100) percent by number of the crystal sizes thereof arc not greater than 200 nanometers. In some embodiments preferably, the glass-ceramics further comprise a complex AIiOj-Y^Oj. Some embodiments of the glass-ceramics include glass-ceramics comprising a first complex AliOs-YiO^, a second, different complex AhOj-YiOj, and crystalline Zr02, and wherein at least one of the first complex Al20yY203, the second, different complex AI2OyY20:, or the crystalline Zr02 lias an average crystal size not greater than 150 nanometers. In some embodiments preferably, the glass-ceramics further comprise a second, different complex AhOyYiOv In some embodiments preferably, the ghiss-ccramics further comprise a complex AliOyREO. Some embodiments of the glass-ceramics include glass-ceramics comprising a first complex AUOyYiO:,, u second, different complex AhOs^Ch, and crystalline ZrG2, and wherein for at least one of the first complex AhCVY^Oy the second, different complex Al:OrY:03, or the crystalline Zr02. at least 75 (in some embodiments preferably, 80, 85, 90, 95, or even 100) percent by number of the crystal sizes thereof are not greater than 200 nanometers. In some embodiments preferably, the glass-ceramics further comprise a complex Al:OyREO. Some embodiments of the glass-ceramics include glass-ceramics comprising a first complex AbOyREO, a second, different complex AKOyREO, and crystalline Zr02, and wherein at least one of the first complex AhCVREO, the second, different complex AI1O3REO, or the crystalline Z1O2 has an average crystal size not greater than 150 nanometers. In some embodiments preferably, the glass-ceramics further comprise a second, different complex A)203REO. In some embodiments preferably, the glass-ceramics further comprise a complex AhOyYiO-}. Some embodiments of the glass-ceramics include glass-ceramics comprising a first complex AI;05-REO, a second, different complex A!2OyREO, and crystalline Zr02, and wherein for at least one of the first complex AI203*REO, the second, different complex Al>0;,-REO, or the crystalline Zr02, at least 75 {in some embodiments preferably, 80, 85, 90, 95, or even 100) percent by number of the crystal sizes thereof are not greater than 200 nanometers. In some embodiments preferably, the glass-ceramics further comprise a complex AUOyY;03. In some embodiments, glass-ceramics made according to the present invention comprise at least 75, SO, 85, 90, 95, 97, 98, 99, or even 100 percent by volume crystallites, wherein the crystallites have an average size of less than 1 micrometer. In some embodiments, glass-ceramics made according to the present invention comprise not greater than a: least 75, 80, 85,90,95, 97, 98, 99, or even 100 percent by volume crystallites, wherein the crystallites have an average size not greater than 0.5 micrometer. In some embodiments, glass-ceramics made according to the present invention comprise less than at 75, SO, 85, 90, 95, 97, 98, 99, or even 100 percent by volume crystallites, wherein the crystallites have an average size not greater than 0.3 micrometer. In some embodiments, the glass-ceramics comprise less than at least 75, 80, S5, 90. 95, 97, 98, 99, or even 100 percent by volume crystallites, wherein the crystallites have an average size not greater than 0.15 micrometer. Crystals formed by heat-treating amorphous material made according to methods of the present invention to provide embodiments of glass-ceramics may be, for example, cquiaxed, acicular, columnar, or flattened splat-like features. Typical!}, the (true) density, sometimes refeired to as specific gravity, of amorphous and ceramics made according to methods of the present is at least 70% of theoretical densitv More desirably, the (true) density of ceramics made according to methods of Hie present invention is at least 75%. 80%, 85%. 90%, 92% . 95%\ 96%, 97%, 9S%. 99%, 99.5% or even 100%' of theoretical density. TUe abrasive particles have (true) densities of at [cast 85%, 90%, 92%, 95%, 96%, 97%, 9S%. 99%. 99.5% or even 100% ot theoretical densitv The average hardness of the material of the present invention can be determined as follous. Sections of the material are mounted in mounting resin (obtained under the trade designation "TRANSOPTIC POWDER" from Buehlcr, Lake Bluff, IL) typically in a cylinder of resin about 2.5 cm in diameter and about 1.9 cm high. The mounted section is prepared using conventional polishing techniques using a polisher (such as that obtained from Buehlcr, Lake Bluff, IL under the trade designation "ECOMET 3'"). The sample is polished for about 3 minutes witli a diamond wheel, followed by 5 minutes of polishing with each of 45, 30, 15, 9, 3, and 1-micrometer slurries. The microhardness measurements arc made using a conventional microhardness tester (such as that obtained under the trade designation "MITUTOYO MVK-VL" from Miuttoyo Corporation, Tokyo. Japan) fitted wuh a Vickcrs indentcr using a 100-»ram indent load. The microhardness measurements are made according to (lie guidelines staled in ASTM Test Method E3S4 Test Methods for Microhardness of Materials (1991). In some embodiments, the average hardness of glass-ceramics made according to methods of the present invention is at least 12, 13, 14, 15, 16, 17, or even at least 18 Gpa. Abrasive particles made according to the present invention have an average hardness of at least 15 GPa, in some embodiments, at least 16 GPa. at least 17 GPa, or even at least IS GPa. Additional details regarding amorphous materials, glass-ceramics, including making, using, and properties thereof, can be found in application having U.S. Serial Nos. 09/922.526. 09/922.527, and 09/922,530, filed August 2, 2001. and U.S. Serial Nos. 10/211,59S; 10/211.630; 10/2U.639; 10/211,034; 10/211,044-. 10/211,620; and 10/211,640. filed Aueust 2. 2002. Embodiments of amorphous materia!, glass-ceramic, etc. made according to the present invention may in some embodiments desirably comprise a composite. Such a composite may comprise, for example, a phase or particulate (e.g., mc:al o\ide particles, boride particles, carbide particles, nitride particles, diamond particles, metallic particles, glass particles, and combinations thereof) dispersed in an amorphous material, glass-ceramic, etc. made according to the present invention, invention or a la\ered-composite structure (e.g., a gradient of glass-ceramic to amorphous material used to make the glass-ceramic and/or layers of different compositions of glass-ceramics). In making composites comprising a phase or particulate dispersed in an amorphous material, glass-ceramic, etc. made according to the present invention, the feed particles having compositions of the invention arc typically mixed with the feed particles of the particles to be dispersed. The particles or phases may also, for example, be dispersed in the amorphous or glass-ceramic compositions of the invention may simply have a different particle size, composition or thermal history than the feed particles of the matrix phase. Layered composites can be made, for example, by changing the composition of the feed particles overtime to provide a layer having diHerein compositions along its thickness. In addition, or alternatively, for example, an amoiphous layer can be deposited and heat-treated after which another layer of the same or a different composition can be deposited. In some embodiments, a gradient structure can be formed so that the thermal expansion mismatch between the substrate and the coatings can be gradually changed along the coating thickness, so that spalling of coatings can be desirably reduced. It is within the scope of the invention to apply intermediate (e.g.. a metallic or intermetallic) coating layers between the substrate and an amorphous layer, for example, to impro\e adhesion, or to eliminate thermal, mechanical or chemical incompatibility between them. The following are some exemplary embodiments of materials that can be made by embodiments of methods according to the present invention. One embodiment is a composite material comprising discrete crystalline regions within an amorphous (continuous) matrix, wherein the crystalline regions and the amorphous material each independently comprise at least 35 (in some embodiments, preferably at least 40,45, 50, 55, 60. 65, or even at least 70) percent by weight AI1O3, based on the total weight of the crystalline regions and ihc amorphous matrix, respectively, and a metal oxide other than ANOi (e.g.. Y20.i. REO, ZrO:, TiO:, CaO, CY20:„ MgO, NiO. CuO, and complex metal oxides thereof), wherein the crystalline regions and the amorphous matrix each contain not more than 10 (in some embodiments, preferably not more than 5, 4, j. 2. 1. or zero) percent by weight collectively As^O^, B:0.i, GeO:, P2O5, SiO:. TcO:. and V2O5, based on the total weight of the crystalline regions and the amorphous matrix, respectively, and wherein the composite material has x, y, unci z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 150 micrometers (in some embodiments, preferably, at least 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm, 5 mm. or even at least 10 mm). The x, y, and z dimensions of a material are determined either visually or using microscopy, depending on the magnitude of the dimensions. The reported z dimension is, for example, the diameter of a sphere, the thickness of a coating, or the longest length of a prismatic shape. In some embodiments, the interface between the discrete crystalline regions may be diffuse to some extent, for example due to reaction between the a discrete crystalline region and the amorphous matrix. In some embodiments, the discrete crystalline regions have an average crystal size not greater than 200 nanometers. In some embodiments, for example, the composition of the discrete crystalline region and the amorphous matrix are the same, while in others they are different. In some embodiments, the metal oxide other than AbOr, for at least one of the discrete crystalline regions or the amorphous matrix is ZrO;, wherein m some preferred embodiments, at least one of the discrete crystalline regions or the amorphous matrix comprises Al:Ch in a range of about 55 to about 65 percent by weight to a range of about 45 to about 35 percent by weight ZrO;, based on the total AI1O3 and ZvO: content of the discrete crystalline regions or the amorphous matrix, as applicable. In some embodiments, at least one of the discrete crystalline regions or the amorphous matrix further comprises (e.g., greater than 0 to 50 percent by weight, based on the total weight of the at least one of the discrete crystalline regions or the amorphous material, as applicable) additional metal oxidc(s) (e.g., Y:0;„ REO, ZrO;. TiO;. CaO, Ci":0:,, MgO, NiO. CuO, and complex metal oxides thereof). In some embodiments, at least one of the discrete crystalline regions or the amorphous matm comprises AI1O3, Y203. and ZrOv In some embodiments, at least one of the discrete crystal line regions or the amorphous matrix comprises Al'O], REO, andZrO;. In some embodiments, tiie composite material is in the form of a Ia>er. In some embodiments, a composite layer comprises an amorphous layer and a layer of the composite material. Compositions of the amorphous layer include those disclosed in the instant application. In some embodiments, tfie composite material comprises a first portion and a second portion, v. herein the first portion has an average number of the discrete crystalline regions per mnr\ wherein the second portion has an average number of the discrete crystalline regions per mmJ, and wherein the average number of the discrete crystalline regions per mmJ of the first portion is than greater (in some embodiments at least 25, 50, 75, 100, 150, 200, or even at least 500 percent by volume greater than) the average number of the discrete crystalline regions per mm3 of the second portion. Further, for example, in some embodiments, the composite material comprises a third portion disposed between the first mid second portions, wherein the third portion has un average number of the discrete crystalline regions per mm , and wherein the average number ot the discrete crystalline regions per mm"1 of the third portion is greater than (in some embodiments at least 25, 50, 75, 100, 150, 200, or even at least 500 percent by volume greater than) the average number of the discrete crystalline regions per mm"' of the second portion, and less than the average number of the discrete crystalline regions per mm"5 of the first portion. Another exemplary embodiment is a composite material comprising discrete crystalline regions within an amorphous matrix, wherein the crystalline regions and the amorphous matrix each independently comprise at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight Al:0.i, based on the total weight of the discrete crystalline regions and the amorphous matrix, a first metal oxide other than A1203 (e.g., Y203, REO, ZrO:, TiCK CaO, Cr>03, MgO, NiO, CuO, and complex metal oxides thereof), and a second, different metal oxide other than AI203 (e.g.. V;0:, REO, ZrO:, TiO;, CaO, Cr;03, MgO, NiO, CuO, and complex metal oxides thereof), wherein the AN03, first metal oxide, and second metal oxide collectively comprise at least 80 (in some embodiments, preferably, at least S5, 90, 95. 97. 9S, 99, or even 100) percent by weight of the discrete crystalline regions and the amorphous matrix, and wherein the discrete crystalline regions and the amorphous matrix contain not more than JO (in some embodiments, preferably not more than 5, 4. 3, 2, 1, or zero) percent by weight collective;}' As;Cb. B;03, Gc02, P:05, SiOj. TeO:, and V;05, based on the total weight of the discrete crystalline regions and the amorphous matrix, with the proviso with the proviso that if the first or second metal oxide other than AI;0,-, of the discrete crystalline regions is Zr02, then the discrete crystalline regions further comprise a metal oxide other than AKOj and ZrO; that at Least a portion of which is present as a distinct crystalline phase, and with the proviso that if the first or second metal oxide other than A NO;; of the amorphous matrix is ZrO:. then the amorphous matrix further comprises a metal oxide other than Al;0.i and ZrO; that at least a portion of which forms a distinct crystalline phase when the amorphous matrix is crystallized. In some embodiments, the composite material has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 150 micrometers (in some embodiments, preferably, at least 200 micrometers, 250 micrometers, 500 micrometers, J000 micrometers. 2000 micrometers, 2500 micrometers, 1 mm, 5 mm, or even at least 10 mm). In some embodiments, the discrete crystalline regions have an average crystal size not greater than 200 nanometers. In some embodiments, for example, the composition of the discrete crystalline region and the amorphous matrix are the same, while in others they are different. In some embodiments, the metal oxide other than AhO.-; for at least one of the discrete crystalline regions or the amorphous matrix is ZrO:, wherein in some preferred embodiments, at least one of the discrete crystalline regions or the amorphous matrix comprises Al:03 in a range of about 55 to about 65 percent by weight to a range of about 45 to about 35 percent by weight ZrO;, based on the total Al;03 and ZvO; content of the discrete crystalline regions or the amorphous matrix, as applicable. In some embodiments, at least one of the discrete crystalline regions or the amorphous matrix further comprises (e.g., greater than 0 to 50 percent by weight, based on the total weight of the at least one of the discrete crystalline regions or the amorphous matrix, as applicable) additional metal oxide(s) (e.g., Y;Oj, REO. ZrO>. TiO;, CaO, Cr;03, MgO, NiO, CuO, and complex metal oxides thereof). In some embodiments, at least one of the discrete crystalline regions or the amorphous matrix comprises AliO-?. YiOj, and ZrO;. hi some embodiments, at least one of the discrete cr\stul!:ne regions or the amoiphous matrix comprises AI2O3, REO, and ZrO;. In some embodiments, the composite material is in the form of a la\er. In some embodiments, a composite layer comprises an amorphous layer and a layci of tiie composite materia]. Compositions of the amorphous layer include those disclosed in the instant application. In some embodiments, the composite material comprises a first portion and a second portion, wherein the first portion has an average number of the discrete crystalline regions per mmJ, wherein the second portion has an average number of the discrete crystalline regions per mm\ and wherein the average number of the discrete crystalline regions per mmJ of the first portion is than greater (in some embodiments at least 25, 50, 75, 100, 150, 200, or even at least 500 percent by volume greater than) the average number of the discrete crystalline regions per mm of the second portion. Further, for example, in some embodiments, the composite material comprises a third portion disposed between the first and second portions, wherein the third portion has an average number of the discrete crystalline regions per mmJ, and wherein the average number of the discrete crystalline regions per mm' ot the third portion is greater than (in some embodiments at least 25, 50, 75. 100. 150, 200, or even at least 500 percent by volume greater than) the average number of the discrete crystalline regions per mm' of the second portion, and less than the average number of the discrete crystalline regions per mmJ of the first portion. Another exemplary embodiment is a composite ceramic comprising discrete crystalline regions in a glass-ceramic matrix, wherein the discrete crystalline regions and the glass-ceramic matrix independently comprise at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight AI2O3 (e.g., Y:03, REO, Zr02, Ti02, CaO, Cr202, MgO, NiO, CuO, and complex metal oxides thereof), based on the total weight of the crystalline regions and the glass-ceramic matrix, respectively, and a metal oxide other than AI2O3 (e.g., Y2C1;. REO, ZrO;, TiO:, CaO, Ct'iO.-;. MgO, NiO, CuO, and complex metal oxides thereof), wherein the discrete crystalline regions and the glass-ceramic matrix each contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zeroj percent by weight collectively As2Oi, B2O3, Ge02. P2O5, Si02, TcO;, and V2O5, based on the total weight of the discrete crystalline regions and the glass-ceramic matrix, respectively, and whcicin [he composite ceramic has x, >. and z dimensions each perpendicular to each other, and wherein each of the x. y, and z dimensions is at least 150 micrometers (in some embodiments, preferably, at least 200 micrometers. 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm, 5 mm, or even at least 10 mm). In some embodiments, at least 50, 60, 70, 75, 80, 90, or e\en at least 95 percent by \olume ol' the glass-ceramic is crystalline. In some embodiments, the glass-ceramic and/or the discrete crystalline regions have an average crystal size not greater than 200 nanometers. In some embodiments, the metal oxide other than ANOj for at least one of the discrete crystalline regions or the glass-ceramic is ZrOi, wherein in some preferred embodiments, at least one of the discrete crystalline regions or the glass-ceramic comprises A NO;, in a range of about 55 to about 65 percent by weight to a range of about 45 to about 35 percent by weight ZrOi, based on the total AI1O3 and ZrO: content of the discrete crystalline regions or the glass-ceramic, as applicable. In some embodiments, at least one of the discrete crystalline regions or the glass-ccramic further comprises (e.g., greater than 0 to 50 percent by weight, based on the total weight of the at least one of the discrete crystalline regions or the glass-ceramic, as applicable) additional metal oxide(s) (e.g., Y20:, REO, ZrO:, T1O2, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), In some embodiments, at least one of the discrete crystalline regions or the glass-ceramic comprises ANO3, Y2O3, and ZrO;). In some embodiments, at least one of the discrete crystalline regions or the glass-ceramic comprises Al;03. REO, and ZrCK In some embodiments, the composite ceramic is in the form of a layer. In some embodiments, a composite layer comprises an amorphous layer and a la>er of the composite ceramic. Compositions of the amorphous layer include those disclosed in the instant application. Another exemplary embodiment is a composite ceramic comprising discrete crystalline regions in a glass-ceramic matrix, wherein the discrete crystalline regions and the glass-ceramic matrix independently comprise at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65, or even at least 70) percent by weight AI2O3, based on the total weight of the discrete crystalline regions and the amorphous matrix, a first metal oxide other than AI:Oi (e.g., Y20?, REO, ZrO:, TiO;. CaO. Cr:03, MgO, NiO, CuO, and complex metal oxides thereof), and a second, different metal ov.de other than Ai:0 (e.g.. Y:0.-. REO, ZrO:. TiO;, CaO, Ci >0;. MgO, NiO, CuO, and complex metal oxides thereof), wherein the AhOi, first metal oxide, and second metal oxide collectively comprise at least SO fin some embodiments, preferably, at least S5, 90. 95, l>7, 98, 99, or even 100) percent by weight of the discrete crystalline regions and the glass-ceramic matrix, and wherein the discrete crystalline regions and the glass-ceramic matrix contain not more than 10 (in some embodiments, preferably not more than 5, 4. 3, J, I, or zero) y percent by weight collectively AS^OT, B^Cb, GeO^, P:Oj, SiO;, TeO;, and V;05, based on the total weight of the discrete crvstallinc regions and the glass-ceramic matrix, with the proviso that if the first or second metal oxide other than AhO; of the discrete crystalline regions is ZrOi, then the discrete crystalline regions further comprise a metal oxide other than A1;03 and ZvOi that at least a portion of which is present as a distinct crystalline phase, and with the proviso that if the first or second metal oxide other than AhO;, of the glass-ceramic matrix is ZrO;, then the glass-ceramic matrix further comprises a metal oxide other than AhO-, and ZrO: that at least a portion of which is present as a distinct crystalline phase when the amorphous matrix is crystallized. In some embodiments, the composite ceramic litis x, y, and z dimensions each perpendicular to each other, and wherein each of the x. y. and z dimensions is at least 150 micrometers (in some embodiments, preferably, at least 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm. 5 mm. or even at least 10 mm), hi some embodiments, at least 50, 60, 70, 75, SO, 90, or even at least 95 percent by volume of the glass-ceramic is crystalline. In some embodiments, the glass-ceramic and/or the discrete crystalline regions have an average crystal size not greater than 200 nanometers. In some embodiments, the metal oxide other than Al;Oj for at letiit one of the discrete crystalline regions or the glass-ceramic is ZrO;, wherein m some preferred embodiments, at least one of the discrete crystalline regions or tire glass-ceramic comprises A1;0:, in a range of about 55 to about 65 percent by weight to a range of about 45 to about 35 percent by weight ZrO:, based on the total AI2O3 and ZrO; content or the discrete crystalline regions or the glass-ceramic, as applicable. in some embodiments at least one of the discrete crystalline regions or the glass-ceramic further comprises (e.g., greater than 0 to 50 percent by weight, based on tfie total weight of the at least one of the discrete crystalline regions or the glass-ceramic, as applicable) additional metal oxide(s) (e.g., Y203. REO, ZrO:. Ti02, CaO, Cr:03, MgO, NiO, CuO, and complex metal oxides thereof), In some embodiments, at least one of the discrete crystalline regions or the glass-ceramic comprises AI203, Y203, and ZrO;. In some embodiments, at least one of the discrete crystalline regions or the glass-ceramic comprises A1;0?. REO, and Zr02. In some embodiments, the composite ceramic is in the form of a layer. In some embodiments, a composite layer comprises an amorphous layer and a layer of the composite ceramic. Compositions of the amorphous layer include those disclosed in the instant application. Another exemplary embodiment is a glass-ceramic layer having first and second opposite surfaces, a first ceramic compositional region comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60. 65, or even at least 70) percent by weight AhOr,. based on the total weight of the first ceramic compositional region, and a metal oxide other than AljCh. wherein first ceramic compositional region contains not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2. 1, or zero) percent by weight collectively AS2OT, B20i, GcO;, P2O5, SiO:. TeO:, and V;Oj, based on the total weight of the first ceramic compositional region, and a second ceramic compositional region comprising at least 35 (in some embodiments, preferably at least 40, 45. 50. 55, 60, 65, or even at least 70) percent by weight AI203. based on the total weight of the second ccvamic compositional region, and a metal oxide other than AI2O3 (e.g., Y203, REO, Zr02, Ti02, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides ihercofi. wherein the second ceramic compositional region contains not more than 10 (in some embodiments, preferably not more than 5,4,3,2, L, or zero) percent by weight collectively As:03, B203, Ge02, P20>, Si02, TeO:, and V205, based on the total weight of the second ceramic compositional region, wherein the first ceramic compositional region is closer to the first surface than it is to the second surface, and wherein the second ceramic compo-Kiona! region is closer to the second surface than it is to the first surface, and wherein the first compositional region has x, y, and z dimensions each perpendicular to each other, and w herein each of the x, y, andz dimensions is at least 150 micrometers (in some embodiments, preferably, at least 200 micrometers, 250 micrometers. 500 micrometer;.. 1000 micrometers, 2000 micrometers. 2500 micrometers. 1 rim, 5 mm, or even a! least 10 mm). In some embodiments, the metal oxide other than Al;0;. lor at least one of the first or second ceramic compositional regions is ZrCK wherein in some prcleired embodiments, at least one of the first or second ceramic compositional regions comprises AI7O3 in a range of about 55 to about 65 percent by weight to a range of about 45 to about 35 percent by weight ZrO:, based on the total AKO.i and ZrOi content of the first or second ceramic compositional regions, as applicable. In some embodiments, at least one of the first or second ceramic compositional regions further comprises (e.g., greater than 0 to 50 percent by weight, based on the total weight of the at least one of the first or second ceramic compositional regions, as applicable) additional metal oxide(s) (e.g., Y203, REO, Z1O2, TiOj, CaO, Cr203, MgO, N'iO, CuO, and complex metal oxides thereof), In some embodiments, at least one of the first or second ceramic compositional regions material comprises AI2O;,. Y2O3, and ZrCY. In some embodiments, at least one of first or second ceramic compositional regions comprises AhO;,, REO, and ZrCK In some embodiments, a composite layer comprises an amorphous layer and the ceramic layer. Compositions of the amorphous layer include those disclosed in the instant application. in some embodiments, for example, the first ceramic compositional region is amoiphous, and the second ceramic compositional region is at least partially crystalline. In some embodiments, for example, the composition of the first and ceramic compositional regions are the same, while in others they are different. Another exemplary embodiment is a glass-ceramic layer having first and second opposite surfaces, a first ceramic compositional region and a second compositional region each independently comprise at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60. 65, or even at least 70) percent by weight Al^O;, based on the total weight of the first or second compositional region, respectively, a first metal oxide other than A1:0;, (e.g., Y203, REO, ZrCK TICK CaO, Cr;0_i. MgO, NiO, CuO, and complex metal oxides thereof), and a second, different metal oxide other than ANOj (e.g., Y:Oi. REO, Zr02, TiO;. CaO, Cr:0:, MgO, NiO, CLIO, and complex mclal oxides thereof), wherein the AhCK first metal oxide, and second metal oxide collectively comprise at least SO (in some embodiments, preferably, at least 85, 90, 95, 97. 9S, 99, or even 100) percent by weight of the first, or second compositional region, respceii\ eiy, and wherein the fus: or second compositional region, respectively, contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, I, or zero) percent by weight collectively AsiOj, B2O3, GeCK P2O5, SiO:, Te02, and V2O5, based on the total weight of the first or second compositional region, respectively, with the proviso that if the first or second metal oxide other than AI2O.-, of the first or second compositional region, respectively, is Zr02 then the first or second compositional region, respectively, further comprises a metal oxide other than A 1:0 3 and ZrO: that at least a portion of which is present as a distinct crystalline phase. In some embodiments, the composite material has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 150 micrometers (in some embodiments, preferably, at least 200 micrometers, 250 micrometers, 500'micrometers, 1000 micrometers. 2000 micrometers, 2500 micrometers, I mm. 5 mm, or even at least 10 mm). In some embodiments, the metal oxide other than AI2O3 for at least one of the first or second ceramic compositional regions is ZrO;. wherein in some preferred embodiments, at least one of the first or second ceramic compositional regions comprises ANOj in a range of about 55 to about 65 percent by weight to a range of about 45 to about 35 percent by weight Z1O2, based on the total Al203 and ZrO: content of the first or second ceramic compositional regions, as applicable. In some embodiments at least one of the first or second ceramic compositional regions further comprises (e.g., greater than 0 to 50 percent by weight, based on the total weight of the at least one of the first or second ceramic compositional regions, as applicable) additional metal oxide(s) (e.g., Y203, REO. Zr02, Ti02, CaO, Cr2Oi, MgO, NiO. CaO, and complex metal oxides thereof). In some embodiments, at least one of the first or second ceramic compositional regions material comprises AI1O3, Y:Oj, and Zr02. In some embodiments, at least one of first or second ceramic compositional regions comprises Al20;,, REO, and Zr02. Ill some embodiments, a composite lnycr comprises uti amorphous layer und the ceramic layer. Compositions of the amorphous layer include those disclosed in the instant application. In some embodiments, for example, the first ceramic compositions! region is amorphous, and the second ceramic compositional region is at least partially crystalline. In some embodiments, for example, the composition of the first and ceramic compositional regions are the same, while in others they are different. Another exemplary embodiment is a ceramic comprising at least 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60. 65, or even at least 70) percent by weight Al;0:„ based on the total weight of the ceramic, and a metal oxide other than AI1O3 (e.g., Y;03, R£0, ZrO:, T1O2, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), wherein ceramic layer contains not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, 1, or zero) percent by weight collectively AS2O3, B2O3, GeO:. P20i, SiO>, TcO;, and V1O5, based on the total weight of the ceramic, the ceramic-having first and second crystalline comprising regions having first and second degrees of crystal linity. respectively, wherein the degree of crystallinity of the first region is greater than (e.g.. at least 25, 50, 75. 100, 150, 200, or even at least 500 percent by volume) the degree of crystallinity of the second region, and wherein the first region has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 150 mici'omcters(in some embodiments, preferably, at least 200 micrometers, 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, I mm. 5 mm, or even at least 10 mm). In some embodiments, the discrete crystalline regions have an average crystal size not greater than 200 nanometers. In some embodiments, each of the first and second discrete crystalline regions each have an average crystal size not greater than 200 nanometers. In some embodiments, for example, the composition of the first and second discrete crystalline regions are the same, while in others they are different. In some embodiments, the metal oxide other than Al:0_- for at least one of the first or second discrete crystalline regions is ZrO-'. wherein in some preferred embodiments, at least one of the first or second discrete crystalline regions comprises A1:03 in a range of about 55 to about 05 percent by weight to a range of about 45 to about 35 percent by weight ZiO;, based on the total Al20;, and Zr02 content of the first or second discrete crystalline regions, as applicable. In some embodiments at least one of the first or second discrete crystalline regions further comprises (e.g., greater than 0 to 50 percent by weight, based on the total weight of the first and second discrete crystalline regions, as applicable) additional metal oxide(s) (e.g.. Y;05, REO, Zr02, Ti02, CaO, Cr203, MgO, NiO, CuO, and complex metal oxides thereof), In some embodiments, at least one of the first and second discrete crystalline regions comprises AljO.i, Y20>. and Zr02. In some embodiments, at least one of the first und second discrete crystalline regions comprises Al203, REO, and Zv02. In some embodiments, the composite material is in the form of a layer. In some embodiments, a composite layer comprises an amorphous layer and a layer of the composite material. Compositions of the amorphous layer include those disclosed in the instant application. In some embodiments, at least 50, 60, 70, 75, SO, 90, or even at least 95 percent by volume of the glass-ceramic is crystalline. Another exemplary embodiment is a ceramic comprising 35 (in some embodiments, preferably at least 40, 45, 50, 55, 60, 65. or even at least 70) percent by weight Al2O1, based on the total weight of the ceramic, a first metal oxide other than ANO? (e.g., y203l REO. Zr02, Ti02, CaO, Cr203, MgO, NtO, CuO, and complex metal oxides thereof), and a second, different metal oxide other than AliO, wherein the A!:0:, (e.g.. Y2O3, REO, Zr02, TiO:, CaO, Cr203. MgO, NiO, CuO, and complex metal oxides thereof), the first metal oxide, and second metal oxide collectively comprise at least SO (in some embodiments, preferably, at leas' 85, 90, 95,97, 98,99, or even 100) percent by weight of the ceramic, and wherein the particles contain not more than 10 (in some embodiments, preferably not more than 5, 4, 3, 2, I, or zero) percent by weight collectively Ab20.-„ BnO.7, GeO:, P205. Si02, Te02, and V205, based on the total weight of the ceramic, the ceramic having first and second crystalline comprising regions having first and second degrees of crystal 1 inky, respectively, wherein the degree ol crystalhnky of the lirst region is greater than the degree of crystallinity of the second region, with the proviso that if the first or second metal oxide other than Al20^ of the first or second regions is ZrO?, then the ceramic further comprise a metal oxide other than AI2O3 and ZrO; that at least a portion of which is present as a distinct crystalline phase. In some embodiments, the first region has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 150 micrometers (in some embodiments, preferably, at least 200 micrometers. 250 micrometers, 500 micrometers, 1000 micrometers, 2000 micrometers, 2500 micrometers, 1 mm, 5 mm. or even at least 10 mm). In some embodiments, for example, the composition of the first -arid second discrete crystalline regions ure the same, while in others they are different. In some embodiments, the metal oxide other than AI;Oj for at least one of the first and second discrete crystalline regions is ZiOi, wherein in some preferred embodiments, at least one of the first and second discrete crystalline regions comprises A1:0:, in a range of about 55 to about 65 percent by weight to a range of about 45 to about 35 percent by weight ZrO:. based on the total A1203 and Zr02 content of the first and second discrete crystalline regions, as applicable. In some embodiments at least one of the first and second discrete crystalline regions further comprises (e.g., greater than 0 to 50 percent by weight, based on the total weight of the at least one of the first and second discrete crystalline regions, as applicable) additional metal oxide(s) (e.g., Y;0:„ RED, ZrO:. TiO:, CaO. Cr:0:„ MgO, NiO. CuO, and complex metal oxides thereof), In some embodiments, at least one of the first and second discrete crystalline regions comprises AI2O3, Y2O3, and ZrCK In some embodiments, at least one of the first and second discrete crystalline regions comprises AI:03,REO,andZrO2. In some embodiments, the composite material is in the form of a layer. In some embodiments, a composite layer comprises an amoiphous layer and a layer of the composite material. Compositions of the amoiphous layer include those disclosed in the i visum application. In some embodiments, at least 50, 60, 70, 75, SO, 90, ore\en at least 95 percent by volume of the glass-ceramic is crystalline. Such exemplary materials can be made by embodiment; of methods according to the present in\ention. although it is also within the scope of making such materials to substitute the specified compositions or other material requirement-, (including in some cases and minimum x, y, z, dimensions). In one method, for example, the Iced particles may comprise a mixture of particles having, for example, different composition. In some embodiments, one component of the mixture may form an amorphous matrix while another component forms discrete crystalline regions. Different components making up the feed particles may have different chemical, different phases, different physical sates (e.g.. porosity, HZQ, and/or shape), or combinations thereof. In some embodiments the particles making up the feed may have been formed via flame forming or plasma spraying into amorphous and/or crystalline particles. In some embodiments, the relative proportions of different components making up the fed may be varied continuously to provide a material having gradient features (e.g., a compositional gradient and/or various degrees of crystal I inity). In some embodiments a gradient may comprise a compositional gradient of two or more different compositions varying, for example, chemically. In some embodiments, the relative proportions of different components making up the feed particles may be varied in a step wise manner to form a layered composite. Each layer, for example, may have different compositions, degrees of crystallinity (including different phases), combinations thereof. In some embodiments, amorphous material is heat-treated to convert at least a portion thereof to glass-ceramic. Abrasive particles made by methods according to the present invention generally comprise crystalline ceramic (in some embodiments, preferably at least 75. SO, 85, 90, 91, 92, 93, 94, 95, 96, 97, 98, 99, 99.5, or even 100 percent by volume) crystalline ceramic. The abrasive particles can be incorporated into an abrasive article, or used in loose form. The abrasive articles comprise binder and a plurality of abrasive panicles, wherein nt least a portion of the abrasive particles are the abrasive panicles made by a method according to the present invention. Exemplary abrasive products include coated abrasive articles, bonded abrasive articles (e.g., wheels), non-woven abrasive articles, and abrasive brushes. Coated abrasive articles typically comprise a backing having first and second, opposed major surfaces, and wherein the binder and the plurality of abrasive particles form an-abrasive layer on at least a portion of the first major surface. In some embodiments, preferably, at least 5. 10, 15, 20. 25, 30. 35, 40, 45, 50 55, 60, 65. 70, 75, SO, S5, 90, 95, or even 100 percent by weight of the abrasive particles in an abrade article arc the abrasive particles made by a method according to the present invention, based on the total weight of the abrasive particles in the abrasive article. Abrasive panicles arc usually graded to a given particle size JiSLiituition before use. Such distributions typically have a range of particle sizes, Irom coarse particles fine particles. In the abrasive art this range is sometimes ret erred to us a "coarse", "control" and "fine" fractions. Abrasive particles graded according to industry accepted grading standards specify the particle size distribution for each nominal grade within numerical limits. Such industry accepted grading standards (i.e.. specified nominal grades) include those known as the American National Standards Institute, Inc. (ANSI) standards, Federation of European Producers of Abrasive Products (FEPA) standards, and Japanese Industrial Standard (JIS) standards. In one aspect, the present invention provides a plurality of abrasive particles having a specified nominal grade, wherein at least a portion of the plurality of abrasive particles are abrasive particles made by a method according to the present invention. In some embodiments, preferably, at least 5, 10, 15, 20, 25, 30, 35, 40, 45,50 55,60, 65,70, 75,80, 85,90, 95, or even 100 percent by weight of the plurality of abrasive particles arc the abrasive particles made by a method according to the present invention, based on the total weight of the plurality of abrasive particles. ANSI grade designations include. ANSI 4, ANSI 6, ANSI S, ANSI 16, ANSI 24, ANSI 36, ANSI 40, ANSI 50, ANSI 60, ANSI 80, ANSI 100, ANSI 120, ANSI 150, ANSI ISO. ANSI 220, ANSI 240. ANSI 280, ANSI 320, ANSI 360. ANSI 400. and ANSI 600. Prcfeired ANSI grades comprising abrasive particles according to the present invention arc ANSI S-220. FEPA grade designations include PS, P12, P16, P24, P36. P40, P50, P60, PS0, P100, P120, PL50, PIS0, P220, P320,P400,P500,P60Q.P800,PL0Q0,and PL200. Prefened FEPA grades comprising abrasive particles according to the present invention arc P12-P220. JIS grade designations include JIS8, JIS12, JIS 16, JIS24, JIS36, JIS46, JIS54. JIS60. JISS0. JISI00, JIS150, JIS180, JIS220, JIS240, JIS2S0, JIS320, J1S360, J1S400, JIS400, JIS600, JISS00, JIS 1000, JIS 1500, JIS2500. JIS4000, JIS6000, JISS000, and JIS 10,000. Preferred JIS grades comprising abrasive particles according to the present invention are JISS-220. After crushing and screening, there will typically be a multitude of different abrasi\e particle size distributions or grades. These multitudes of grades may not match a man ill ue Hirer'i or supplier's needs at that particular time. To minimize inventory, it is possible to recycle the off demand grades back into melt to form amorphous material. This recycling may occur after the crushing step, where the particles are n large chunks or smaller pieces (.sometimes referred to as "fines") (hat have not been screened to a particular distribution. In another aspect, the present invention provides a method for making abrasive particles, the method comprising heat-treating amorphous (e.g., glass) comprising particles such til at at leas; a portion of the amorphous material converts to glass-ceramic to provide abrasive particles comprising the glass-ceramic. The present invention also provides a method for making abrasive particles comprising a glass-ceramic, the method comprising heat-treating amorphous material such that at least a portion of the amorphous material converts to glass-ceramic, and crushing the resulting heat-treated material to provide the abrasive particles. When crushed, glass tends to provide sharper particles than crushing significantly crystallized glass-ceramics or crystalline material. In another aspect, the present invention provides agglomerate abrasive grains each comprise a plurality of abrasive particles made by a method according to the present invention bonded together via a binder. In another aspect, the present invention provides an abrasive article (e.g., coated abrasive articles, bonded abrasive articles (including vitrified, resinoid, and metal bonded grinding wheels, cutoff wheels, mounted points, and honing stones), nonwoven abrasive articles, and abrasive brushes) comprising a binder and a plurality of abrasive particles, wherein at least a portion of the abrasive particles arc abrasne particles (including where the abrasive particles arc agglomerated) made by a method according to the present invention. Methods of making such abrasive articles and using abrasive articles using abrasive particles arc well known to those skilled in the ait. Furthermore, abrasive particles made by a method according to the present invention can be used in abrasive applications that utilize abrasive particles, such as slurries of abrading compounds (e.g., polishing compounds), milling media, shot blast media, vibratory mill media, and the like. Coated abrasive articles generally include a backing, abrasive particles, and at least one binder to hold the abrasive particles onto the backing. The backing can be any suitable material, including cloth, polymeric film, fibre, nonwoven webs, paper, combinations thereof, and treated versions thereof. The binder can be any suitable binder, including an inorganic or organic binder (including thermally curable vesins and radiation curable resins). The abrasive panicles can be present in one layer or in two lasers of the coated abrasive article. An example of a coated abrasive article is depicted in FIG. I, Referring to this figure, coated abrasive article according to the present invention 1 has a backing (substrate) 2 and abrasive layer 3. Abrasive layer 3 includes abrasive particles made by a method according to the present invention 4 secured to a major surface of backing 2 by make coat 5 and size coat 6. In some instances, a supersize coat (not shown) is used. Bonded abrasive articles typically include a shaped mass of abrasive particles held together by an organic, metallic, or vitrified binder. Such shaped mass ran be, for example, in the form of a wheel, such as a grinding wheel or cutoff wheel. The diameter of grinding wheels typically is about I cm to over 1 meter; the diameter of cut off wheels about I cm to over SO cm {more typically 3 cm to about 50 cm). The cut off wheel thickness is typically about 0.5 mm to about 5 cm, more typically about 0.5 mm to about 2 cm. The shaped mass can also be in the form, for example, of a honing stone, segment, mounted point, disc (e.g. double disc grinder) or other conventional bonded abrasive shape. Bonded abrasive articles typically comprise about 3-50% by volume bond material, about 30-90'7c by volume abrasive particles (or abrasive particle blends), up to 50% by-volume additives (including grinding aids), and up to 70% by \olumc pores, based on the total volume of the bonded abrasive article. A preferred form is a grinding wheel. Referring to FIG. 2, grinding wheel 10 is depicted, which includes abrasive particles made by a method according to the present invention 11, molded in a wheel and mounted on hub 12. Nonwoven abrasive articles typically include an open porous lofty polymer filament structure having abrasive particles made by a method according to the present invention distributed throughout the structure and adherently bonded therein by an organic binder. Examples of filaments include polyester fibers, polyamide fibers, and polyaramid fibers. In FIG. 3, a schematic depiction, enlarged about lOOx. of a typical nonwoven abrasive article is provided. Such a nonwoven abrasive article according to the present invention comprises fibrous mat 50 as a substrate, onto which abrasive particles made by a method according to the present invention 52 are adhered by binder 54. Useful abrasive brushes include those having a plurality of bristles unitary with a bucking (sec, e.g., U.S. Pat. Nos. 5,427,595 (Pilil et al.J, 5,443,906 (Pihl et al.), 5,679,067 (Johnson ct alA-and 5,903,951 (Ionta et a!)). Desirably, such brushes are made by injection molding a mixture of polymer and abrasive particles. Suitable organic binders for making abrasive articles include thermosetting organic polymers. Examples of suitable thermosetting organic polymers include phenolic resins, u re a-formaldehyde resins, melamine-formaldehyde resins, urethane resins, aery I ate resins, polyester resins, aminoplast resins having pendant a,(3-unsaturatcd carbonyl groups, epoxy resins, acrylated urethane, acrylated epoxies, and combinations thereof. The binder and/or abrasive article may also include additives such as fibers, lubricants, wetting agents, thixotropic materials, surfactants, pigments, dyes, antistatic agents (e.g., carbon black, vanadium oxide, graphite, etc.), coupling agents (e.g., silanes, titanates, zircoaluminates, etc.), plasticizers, suspending agents, and the like. The amounts of these optional additives are selected to provide the desired properties. The coupling agents can improve adhesion to the abrasive particles and/or filler. The binder chemistry may thermally cured, radiatic" cured or combinations thereof. Additional details on binder chemistry may be found in . U.S. Put. Nos. 4.5SS.4L9 (Caul ct al.), 4,75 L, 138 (Tumey ct iiU, and 5.436,063 (Folleti ct al.). More specifically with regard to vitrified bonded abrasives, vitreous bonding materials, which exhibit an amorphous structure and are typically hard, arc well known in the art. In some cases, the vitreous bonding material includes crystalline phases. Bonded, vitrified abrasive articles may be in the shape of a wheel (including cut off wheels), honing stone, mounted pointed ov other conventional bonded abrasi\e shape. A preferred vitrified bonded abrasive article is a grinding wheel. Examples of metal oxides that are used to form vitreous bonding materials include: silica, silicates, alumina, soda, calcia, potassia, titania, iron oxide, zinc oxide, lithium oxide, magnesia, bona, aluminum silicate, borosilicate glass, lithium aluminum silicate, ;ombmations thereof, and the like. Typically, vitreous bonding materials can be formed "'rom composition comprising from 10 to 100% glass frit, although more typically the imposition comprises 20% to S0% glass frit, or 30% to 70e/7 glass frit. The remaining ration of the vitreous bonding material can be a non- frit material. Alternatively, the vitreous bond may be derived from a non-frit containing composition. Vitreous bonding materials arc t>pically matured at a tcmperature(s) in a range of about 700°C to about 1500°C, usually in a range of about 800"C to about 1300°C. sometimes i:i a range of about 900JC to about 1200°C, or even in a range of about 950°C to about 1100'C. The actual temperature at which the bond is matured depends, for example, on the particular bond chemistry. Preferred vitrified bonding materials may include those comprising silica, alumina (desirably, at least 10 percent by weight alumina), and bona (desirably, at least 10 percent by weight boria). In most eases the vitrified bonding material further comprise alkali metal oxide(s) (e.g., Na;0 and K2O) (in some cases at least 10 percent by weight alkali metal oxide(s)). Binder materials may also contain filler materials or grinding aids, typically in the form of a particulate material. Typically, the particulate materials are inorganic materials. Examples of" useful fillers for this invention include: metal carbonates (e.g., calcium carbonate (e.g., chalk, calcite, marl, travertine, marble and limestone,), calcium magnesium carbonate, sodium carbonate, magnesium carbonate), silica (e.g., quart/, glass beads, glass bubbles and glass fibers) silicates (e.g., talc, cla\s, (montmorillonitc) feldspar, mica, calcium silicate, calcium mctasilicale, sodium aluminosilicaie. sodium silicate) metal sulfates (e.g., calcium sulfate, barium sulfate, sodium sulfate, aluminum sodium sulfate, aluminum sulfate), gypsum, vermiculite, wood flour, aluminum trihydrate, carbon black, metal oxides (e.g., calcium oxide (lime), aluminum oxide, titanium dioxide), and metal sulfites (e.g., calcium sulfite). In general, the addition of a grinding aid increases the useful life of the abrasive article. A grinding aid is a material that has a significant effect on the chemical and physical processes of abrading, which results in improved performance. Although not wanting to be bound by theory, it is believed that a grinding aid(s) will (a) decrease the friction between the abrasive particles and the workpiece being abraded, (b) prevent the abrasive particles from "capping" (i.e., prevent metal particles from becoming welded to the tops of the abrasive particles), or at least reduce the tendency of abrasive particles to cap. f'-ij decrease the interface temperature between the abrasr. e particles and the workpiece, or (d) decreases the grinding forces. Grinding aids encompass a wide variety of different materials and can be inorganic or organic based. Examples of chemical groups of grinding aids include waxes, organic halide compounds, halide salts and metals and their alloys. The organic halide compounds will typically break down during abrading and release a halogen acid or a gaseous halide compound. Examples of such materials include chlorinated waxes like tetrachloronaphtalene, pentachloronaphthalene, and polyvinyl chloride. Examples of halide salts include sodium chloride, potassium cryolite, sodium cryolite, ammonium cryolite, potassium tetrafluoroboate, sodium tetrafluoroborate, silicon fluorides, potassium chloride, and magnesium chloride. Examples of metals include, tin, lead, bismuth, cobalt, antimony, cadmium, and iron titanium. Other miscellaneous grinding aids include sulfur, organic sulfur compounds, graphite, and metallic sulfides. It is also within the scope of the present invention to use a combination of different grinding aids, and in some instances this may produce a synergistic effect. The preferred grinding aid is cryolite; the most preferred grinding aid is potassium tetrafluoroborate. Grinding aids can be particularly useful in coated abrasive and bonded abrasive articles. In coated abrasive articles, grinding aid is typically used in the supersizc coat, which is applied over the surface of the abrasive particles. Sometimes, however, the grinding aid is added to the size coat. Typically, the amount of grinding aid incorporated into coated abrasive articles arc about 50-300 g/rrf (desirably, about $0-160 g/m"). In vitrified bonded abrasive articles grinding aid is typically impregnated into the pores of the article. The abrasive articles can contain 100% abrasive particles made by a method according to the present invention, or blends of such abrasive particles with other abrasive particles and/or diluent particles. However, at least about 2% by weight, desirably at least about 5% by weight, and more desirably about 30-100% by weight, of the abrasive particles in the abrasive articles should be abrasive particles made by a method according to the present invention. In some instances, the abrasive particles made by a method according to the present invention may be blended with another abrasive particles and/or diluent particles at a ratio between 5 to 75% by weight, about 25 to 75% by weight about 40 to 60% by weight, or about 50% to 50% by weight (i.e., in equal amounts by weight). Examples of suitable conventional abrasive particles include fused aluminum oxide (including white fused alumina, heat-treated aluminum oxide and brown aluminum oxide), silicon carbide, boron carbide, titanium carbide, diamond, cubic boron nitride, garnet, fused alumina-iiirconia. and sol-gel-derivcd abrasive particles, and the like. The sol-gel-derived abrasive particles may be seeded or non-seeded. Likewise, the sol-gel-derived abrasive particles may be randomly shaped or have a shape associated u ith them, such as a rod or a triangle. Examples of sol gel abrasive particles include those described U.S. Pat, Nos. 4,314.S27 (.Leiiheiser et al.), 4,518,397 (Leitheiser et a!.), 4,623,364 (Cottnnger et a!.), 4.744,802 (Schwabel), 4,770,671 (Monroe et al.), 4,881.951 (Wood et al.), 5,011,508 (VValdet al.), 5.090.968 (Pellow), 5,139,978 (Wood), 5,201,916 (Berg et al.), 5,227,104 (Bauer), 5,366.523 (Rovvenhorst et al.), 5,429,647 (Larmie), 5,498,269 (Larmie), and 5,551,963 (Larmie). Additional details concerning sintered alumina abrasive particles made by using alumina powders as a raw material source can also be found, for example, in U.S. Pat. Nos. 5,259,147 (Falz), 5,593,467 (Monroe), and 5,665,127 (Moltgen). Additional details concerning fused abrasive particles, can be found, for example, in U.S. Pat. Nos. 1,161,620 (Coulter), 1,192,709 (Tone), 1,247,337 (Saunders et al.), 1,268,533 (Allen), and 2,424,645 (Baumann ct al.) 3,891,408 (Rowsc et al.), 3,7S 1,172 (Pctt et al.), 3.893.826 (Quinan et al.), 4,126,429 (Watson), 4,457,767 (Poon et al.), 5,023,212 (Dubois ct. al), 5,143,522 (Gibson et al.), and 5,336,280 (Dubois et. al), and applications having U.S. Serial Nos. 09/495.97S, 09/496,422, 09/496,638, and 09/496,713, each filed on February 2, 2000, and 09/618,876, 09/618,879, 09/619,106, 09/619,191,09/619,192, 09/619,215. 09/619,289, 09/619,563, 09/619,729, 09/619,744. and 09/620.262, each filed on July 19, 2000, and 09/772,730, filed January 30, 2001. In some instances, blends of abrasive particles may result in an abrasive article that exhibits improved grinding performance in comparison with abrasive articles comprising 100% of either type of abrasive particle. If there is a blend of abrasive particles, the abrasive particle types forming the blend may be of the same size. Alternatively, the abrasive particle types may be of different particle sizes. For example, the larger sized abrasive particles may be abrasive particles made by a method according to the present invention, with the smaller sized panicles being another abrasive particle type. Conversely, for example, the smaller sized abrasive particles may be abrasive particles made by a method according to the present invention, with the larger sized particles being another abrasive panicle type. Examples of suitable diluent particles include marble, gypsum, fhnt, silica, iron oxide, aluminum silicate, glass (including glass bubbles and glass beads), alumina bubbles, alumina beads and diluent agglomerates. Abrasive particles made by a method according to the present invention can also be combined in or with abrasive agglomerates. Abrasive agglomerate particles typically comprise a plurality of abrasive particles, a binder, and optional additi\es. The binder may be organic and/or inorganic. Abrasi\e agglomerates may be randomly shape or have u predetermined shape associated with them. The shape may be a block, cylinder, pyramid, coin, square, or the like. Abrasive agglomerate particles typically have particle sizes ranging from about LOO to about 5000 micrometers, typically about 250 to about 2500 micrometers. Additional details regarding abrasive agglomerate particles may be found, for example, in U.S. Pat. Nos. 4,311.489 (Kressner), 4,652,275 (Bloeeher et al.), 4,799,939 (Bloechcr et a].), 5,549,962 (Holmes et al,), and 5,975,988 (Chnstianson), and applications having U.S. Serial Nos. 09/6SS,444 and 09/688,484, filed October 16, 2000. The abrasive particles may be uniformly distributed in the abrasive article or concentrated in selected areas or portions of the abrasive article. For example, in a coated abrasive, there may be two layers of abrasive particles. The first layer comprises abrasive particles other than abrasive particles made by a method according to the present invention, and the second (outermost) layer comprises abrasive particles made by a method according to the present invention. Likewise in a bonded abrasive, there may be two distinct sections of the grinding wheel. The outermost section may comprise abrasive particles made by a method according to the present invention, whereas the innermost section does not. Alternatively, abrasive particles made by a method according to the present invention may be uniformly distributed throughout the bonded abrasive article. Further details regarding coated abrasive articles can be found, for example, in U.S. Put. Nos. 4,734,104 (Broberg), 4,737,163 (Lurkcy), 5,203,884 (Buchnnan ct a!.), 5,152,917 (Picper et al.), 5,378,251 (Culler ct al.), 5.417,726 (Stout et al J. 5,436,063 (Follett et al.), 5,496.3S6 (Broberg et al.}, 5, 609,706 (Benedict et al.). 5,520,711 (Helmin), 5,954,844 (Law et al.), 5,961,674 (Gagliardi et al.), and 5,975,988 (Christianson). Further details regarding bonded abrasive articles can be found, for example, in U.S. Pa:. Nos. 4,543,107 (Rue), 4,741,743 (Narayanan et a!.), 4,800,685 (Haynes et al.), 4,89S,597 (Hay et al.), 4,997,461 (Markhoff-Matheny et al.), 5,037,453 (Narayanan ct al.). 5,110.332 (Narayanan et al.), and 5,Sd3,30S (Qi et al). Further details regarding vitreous bonded abrasives can be found, for example, in U.S. Pat. Nos. 4,543,107 \Ruc), 4.S9S.597 (Hay et al.), 4,997,461 (Markhoff-Matheny ct al.), 5,094,672 (Giles Jr. et al.), 5,118,326 (Sheldon et al.), 5,131,926 (Sheldon et al.), 5,203,886 (Sheldon et al.), 5,282,875 (Wood et al.), 5,738,696 (Wu ct al.), and 5,863,308 (Qi). Further details regarding nonwoven abrasive articles can be found, for example, in U.S. Pat. No. 2,958,593 (Hoover ct al.). The present invention, provides a method of abrading a surface, the method comprising contacting at least one abrasive particle made by a method according to the present invention, with a surface of a workpiece; and moving at least of one the abrasive particle or the contacted surface to abrade at least a portion of said surface with the abrasive particle. Methods for abrading with abrasive particles made by a method according to the present invention range of snagging (i.e., high pressure high stock removal) to polishing (e.g., polishing medical implants with coated abrasive belts), wherein the latter is typically done with finer grades (e.g., less ANSI 220 and finer) of abrasive particles. The abrasive particle may also be used in precision abrading applications, such as grinding cam shafts with vitrified bonded wheels. The size of the abrasive particles used for a particular abrading application will be apparent to those skilled in the art. Abrading with abrasive particles made by a method according to the present invention may be done dry or wet. For wet abrading, the liquid may be introduced supplied in tiie form of a light mist to complete flood. Examples of commonly used liquids include: water, water-soluble oil, organic lubricant, and emulsions. The liquid may serve to reduce the heat associated with abrading and/or act as a lubricant. The liquid may contain minor amounts of additives such as bactericide, ami foaming agents, and the like. Abrasive particles made by a method according to the present invention may be used to abrade workpieces such as aluminum metal, carbon steel:-., mild steels, tool steels, stainless steel, hardened steel, titanium, glass, ceramics, wood, wood like materials, paint, painted surfaces, organic coated surfaces and the like. The applied force dunng abrading typically ranges from about 1 to about 100 kilograms. Embodiments of particulate amorphous and glass-ceramics made according to a method of the present invention may be useful, for example, as fillers in polymeric, metallic, or ceramic matrix composites, as raw materials for forming ceramic materials. Transparent forms may be used as retro-reflective beads. Embodiments of particulate amorphous and glass-ceramics made according to a method of the present invention may be viscoclastically deformed into simple or complex shaped bulk materials. Advantages and embodiments of this invention are further illustrated by the following examples, but the particular materials and amounts thereof recited in these examples, as well as other conditions and details, should not be construed to unduly limit this invention. All parts and percentages are by weight unless otherwise indicated. Unless otherwise stated, all examples contain no significant amount of SiO;, B^C^, P^Oj, GcO:, TeO:, As203, andV205. Examples Example I A 250-ml polyethylene bottle (7.3-cm diameter) was charged with the following 50-gram mixture: 19.3 grams of alumina particles (obtained from Alcoa Industrial Chemicals, Bauxite, AR, under the trade designation "A16SG"'), 9.5 grams of zirconium oxide particles (obtained from Zirconia Sales, Inc. of Marietta, GA under the trade designation "DK-2"), and 21.2 grams of lanthanum oxide particles (obtained from Mol>eorp Inc.. Mountain Pass, CA), 75 grams of isopropyl alcohol, and 200 grams of alumina milling media (cylindrical in shape, both height and diameter of 0.635 cm; 99.9% alumina; obtained from Coors, Golden, CO). The contents of the polyethylene bottle were milled for 16 hours at 60 revolutions per minute (rpm). The ratio of alumina to zirconia in the starting material was 2:1, and the alumina and zirconia collectively made up about 5S weight percent (wt-%). After the milling, the milling media were removed and the slurry was poured onto a warm (approximately 75°C) glass ("PYR£X") pan and dried. The dried mixture was screened through a 70-mcsh screen (212-micrometer opening size) with the aid of a paint brush. After grinding and screening, the mixture of milled feed particles was fed slowly (0.5 gram/minute) into a hydrogen/oxygen torch flame to melt the particles. The torch used to melt the particles, thereby generating molten droplets, was a Bethlehem bench burner PM2D Model B obtained from Bethlehem Apparatus Co.. Hellertown, PA. Hydrogen and oxygen flow rates for the torch were as follows. For the inner ring, the hydrogen flow rate was S standard liters per minute (SLPM) and the oxygen How rate was 3.5 SLPM. For the outer ring, the hydrogen flow rate was 23 SLPM and the oxygen flow rale v. as 12 SLPM, The dried and sized particles were fed slowly (0.5 gram/minute) into the torch flame, which melted the particles and earned them on to an inclined stainless steel surface (approximately 51 centimeters (20 inches) wide with a slope angle of 45 degrees) with cold water running over (approximately 8 liters/minute) the surface to rapid!) quench the molten droplets. The resulting molten and quenched beads were colier.ed and dried at 110"C. Trie particles were spherical m shape and varied in size from a few micrometers (i.e., microns) up to 250 micrometers. Subsequently, the flame-formed beads having, diameters less than L25 micrometers were then passed through a plasma gun and deposited on stainless steel substrates as follows. Four 304 stainless steel substrates (76.2 millimeter (mm) x 25.4 mm x 3.175 mm dimensions), and two 10S0 carbon steel substrates (76.2 mm x 25.4 mm x 1.15 mm) were prepared in the following manner. The sides to be coated were sandblasted, washed in an ultrasonic bath, and then wiped clean with isopropyl alcohol. Four stainless steel and one 1080 carbon steel substrates were placed approximately 10 centimeters (em) in front of the nozzle of a plasma gun (obtained under the trade designation '"Praxair SG-100 Plasma Gun" from Praxair Surface Technologies, Concord, NH). The second 10S0 carbon steel was placed IS cm in front of the nozzle of the plasma gun. The coatings made on the second 10S0 carbon steel samples at a distance of 18 cm in front of the nozzle of the plasma gun were not further characterized. The plasma unit (described above with reference to FIG. 4) had a power rating of 40 kW. The plasma gas was argon (50 pounds per square inch (psi), 0.3 megapascal (MPa)) with helium as the auxiliary gas (150 psi, 1 MPa). The beads were passed through the plasma gun by using argon as the carrier gas (50 psi, 0.3 MPa) using a Praxair Model 1270 computerized powder feeder (obtained from Praxair Surface Technologies, Concord, NH). During deposition, a potential of about 40 volts and a current of about 900 amperes was applied and the plasma gun was panned left to right, up and down, to evenly coat the substrates. When the desired thickness was achieved, the plasma spray was shut off and the samples were recovered. The 1080 carbon steel substrate uas flexed, thus separating the coating from the substrate resulting in a free-standing bulk material. The deposited material had a z dimension (thickness) of about 1350 micrometers, as determined using optical microscopy. The phase composition (glassy/amorphous/crystalline) uas determined through Differential Thermal Analysis (DTA) as described below. The material was classified as amorphous if the corresponding DTA trace of the material contained an exothermic crystallization event (J\). If the same trace also contained an endothermic event (Tg) at a temperature lower than Ts it was considered to consist of a glass, phase. U~ the DTA trace of the material contained no such events, it was considered to contain crystalline phases. Differential thermal analysis (DTA) was conducted using the following method. DTA runs were made (using an instrument obtained from Nctzsch Instruments, Sclb, Germany under die trade designation "NETZSCH ST A 409 DTA/TGA"\ using a -140+170 mesh size fraction (i.e., the fraction collected between 105-micrometer opening size and 90-micrometev opening size screens). The amount of each screened sample placed in a 100-microliter AI2O3 sample holder was about 400 milligrams. Each sample was heated in static air at a rate of I0DC/minute from room temperature (about 25°C) to U00°C. The coated material (on 304 stainless steel substrates) exhibited an endothermic event at a temperature around 8S0°C, as evidenced by a downward change in the curve of the trace. It is believed this event was due to the glass transition (TB) of the glass material. The same material exhibited an exothermic event at a temperature around 931°C, as evidenced by a sharp peak in the trace. It is believed that this event was due to the crystallization (Tx) of the material. Thus, the coated material (on 304 stainless steel substrates) and the free-standing bulk material were glassy as determined by a DTA trace. A portion of the glassy free-standing bulk material was then heat-treated at 1300°C for 4S hours. Powder X-ray diffraction, XRD, fusing an X-ra> diffractometer (obtained under the trade designation "PHILLIPS XRG 3100" from Phillips, Mahwah, NJ) with copper K al radiation of 1.54050 Angstrom) was used to determine the phases present. The phases were determined by comparing the peaks present in the XRD trace of the crystallized material to XRD patterns of crystalline phases provided in JCPDS databases, published by International Center for Diffraction Data. The resulting crystalline material included LaAI03. ZrO; (cubic, tetragonal), LaAlnO]8, and transitional AI1O3 phases. Another portion of the glassy free-standing bulk material was crystallized at 1300'C for 1 hour in an electrically heated furnace (obtained from CM Furnaces, Bloomfield, NJ under the trade designation "Rapid Temp Furnace"). The crystallized coating was crushed with a hammer into particles of-30+35 mesh size (i.e., the fraction coIIcc:ed between 600-micrometer opening size and 500-micromctcr opening size screens;. The particles were cleaned of debris by washing in a sonic bath ("obtained trom Cole-Parmer. Vernon Hills, IL, under the trade designation "SS9L") for 15 minutes, dried at 100'C, and several were mounted on a metal cylinder (3 cm in diameter and 2 cm high) using carbon tape. The mounted sample was sputter coated with a thin layer of gold-palladium and viewed using a JEOL scanning electron microscopy (SEM) (Mode! JSM 840AJ. The fractured surface was rough and no crystals coarser than 200 nanometers (nm) were observed (see FIG. 5) in the SEM. Example 2 Feed particles were made as described in Example I using the following 50-gram mixture: 21.5 grams of alumina particles (obtained from Alcoa Industrial Chemicals, Bauxite, AR under the trade designation "A16SG"). 9 grams of zirconium oxide particles (obtained from Zirconia Sales, Inc. of Marietta, GA under the trade designation "DK-2"), and 19.5 grams of cerium oxide particles (obtained from Rhone-Poulence, France). The ratio of alumina to zirconia in the starting material was 2.4:1 and the alumina and zirconia collectively made up about 61 weight percent. Feed particles were flame-formed into beads (of a size that varied from a few micrometers up to 250 micrometers) as described in Example 1. Subsequently, the flame-formed beads having diameters between 180 micrometers and 250 micrometers were sprayed through a plasma gun and deposited on stainless and carbon steel substrates as described in Example 1. The 10S0 carbon steel substrates were flexed, thus separating the coating from the substrate resulting in a free-standing bulk material. The resulting bulk material bad a z dimension (thickness) of about 700 micrometers, as determined using optical microscopy. Tiie micros! met Lire was also observed using optical microscopy. The material consisted of generally spherical and oblique crystalline particles, which were opaque, within a predominantly amorphous matrix, which was transparent. Amorphous material is typically transparent due to the lack of light scattering centers such as crystal boundaries, while the crystalline particles show a crystalline structure and are opaque due to light scattering effects. The crystalline phases, determined by powder XRD analysis as described in Example 1, consisted of Zi'o4Cea. A second deposition experiment was carried out using the flame-formed beads having diameters less than 125 micrometers. The resulting coating had a z dimension (thickness) of 'about 1100 micrometers, as determined using optical microscopy. The microstructure was also observed using optical microscopy. This material had similar features (i.e., consisted of generally spherical and oblique crystalline panicles within a predominantly amorphous matrix) to those of the material formed from beads having diameters between ISO micrometers and 250 micrometers. The crystalline phases, determined by XRD analysis as described in Example 1. consisted of Zro-iCeooOi (cubic) and transitional AI1O3. The average hardness of the as-sprayed material of this example was determined as follows. Sections of the material were mounted in mounting resin (obtained under the trade designation "TRANSOPTIC POWDER" from Buehler, Lake Bluff. IL). The resulting cvlindcr of resin was about 2.5 cm in diameter and about 1.9 cm high. The mounted section was prepared using conventional polishing techniques using a polisher (obtained from Buehler, Lake Bluff, IL under the trade designation "ECOMET 3"). The sample was polished for about 3 minutes with a diamond wheel, followed by 5 minutes of polishing with each of 45, 30, 15, 9, 3, and 1-micrometer slurries. The microhardness measurements were made using a conventional microhardness tester (obtained under the trade designation "MITUTOYO MVK-VL" from Mitutoyo Corporation. Tokyo, Japan) fitted with a Viekers indenter using a 100-gram indent load. The microhardness measurements were made according to the guidelines stated in ASTM Test Method E3S4 Test Methods for Microhardness of Materials (1991). The average microhardness (an average of 20 measurements) of the material of this example was 15 gigapascals (Gpa). Example 3 Feed particles were made as described in Example 1 using the following 50-gram mixture: 27.9 grams of alumina particles (obtained from Alcoa Industrial Chemicals, Bauxite, AR under the trade designation "AI6SG"), 7.8 grams of zirconium oxide particles (obtained from Zirconia Sales, Inc. of Marietta, GA under the trade designation "DK-2"), and 14.3 grams of yttrium oxide particles (obtained from H.C. Stark New ton, MA). The ratio of alumina to zirconia of initial starting materials was 3.5:1 and the alumina and ?.iiconia collectively made up about 72 weight percent. The feed particles were then screened through a 30-mesh screen (600-micromcter opening size) and heat-treated at 1400"C for 2 hours in an electrically heated furnace (obtained from CM Furnaces, Bloomfield. NJ under the trade designation "Rapid Temp Furnace"). The heat-treated panicles were further screened to separate out particles with diameters between 125 micrometers and 180 micrometers, which were then passed through a plasma gun and deposited on stainless steel substrates as described in Example L The 10S0 carbon steel substrate was flexed, thus separating the coating from the substrate resulting in a free-standing bulk material. The resulting bulk material had a z dimension (thickness) of about 700 micrometers, as determined using optical microscopy. The microstructure was observed using optical microscopy. This material consisted of generally crystalline opaque particles (which retained their original angular shapes) within a predominantly transparent, amorphous matrix. The crystalline phases, determined by powder XRD analysis as described in Example 1, consisted of AI5Y3O12 and YQ isZl'ojiiOiqi. Another portion of the free-standing bulk material was crystallized at 1300°C for 1 hour and the fractured surface was sputter coated with a thin layer of gold-palladium and viewed using a JEOLSEM (Model JSM 340A), as described above in Example 1. The tracturcd surface was rough and no crystals coarser than 200 nm were observed (see FIG. 6). A second deposition experiment was earned out using heat-treated particles having diameters less than 125 micrometers. The resulting coating was about 1500 micrometers thick (z dimension). The microstructure was observed using optical microscopy. This material had similar features (consisted of generally opaque, crystalline particles (which retained their original angular shapes) within a predominantly transparent, amorphous matrix) to the material formed from beads having diameters between ISO micrometers and 250 micrometers. The crystalline phases, determined by XRD analysis as described in Example 1, consisted of AI5Y3O12 and Y0.15Z10S5O193. Example 4 A thick coating consisting of various layers of the above three examples was plasma sprayed using feed particles produced in Examples 1-3. The first layer was coated as described in Example 2, the second as described in Example I, and the third as described in Example 3. The substrate was not sandblasted prior to coating sp that it was removed easily by plying it apart by hand, resulting in a free-standing bulk material, approximately 75 millimeters (mm) x 25 mm x 7.5 mm. A cross-section, cutting through each layer, was sectioned from the material using a diamond saw. The sectioned piece was mounted in mounting resin (obtained under the trade designation "TRANSOPTIC POWDER" from Buehler, Lake Bluff, IL) such that the different layers were visible. The resulting cylinder of resin was about 2.5 cm in diameter and about 1.9 cm tall (i.e., high). The mounted section was prepared using conventional polishing techniques using a polisher (obtained from Buehler, Lake Bluff, IL under the trade designation "ECOMET 3"). The sample was polished for about 3 minutes with a diamond wheel, followed by 5 minutes of polishing with each of 45, 30, 15, 9, 3, and 1-micrometer slurries. The first layer had a z dimension (thickness) of approximately 2.5 mm, as determined using optical microscopy. The microstructure was observed using optical microscopy. This material had similar features to those of the material of Example 2 (i.e., consisted of generally spherical and opaque crystalline particles within a predominantly transparent, amorphous matrix). The second layer had a z dimension (thickness) of approximately 2 mm, as determined using optical microscopy. The micros tincture was also observed using optical microscopy. This material had similar features to those of the material of Example 1 (i.e., was transparent suggesting it was amorphous). The third layer had a z dimension (thickness) of approximately 3 mm, as determined using optical microscopy. The microstructure was also observed using optical microscopy. This material had similar features to those of the material of Example 3 (i.e., it consisted of generally opaque crystalline particles (which mostly retained their original angular shapes) within a predominantly transparent, amorphous matrix). Comparative Example A Feed particles of Yttria-stabilizedZirconia, average size 125 micrometers, (obtained under the trade designation "ZIRSPRAY 9204" from Praxair Surface Technologies, Concord, NH) were passed through a plasma gun and deposited on stainless and carbon steel substrates as described in Example 1. The abrasion wear was measured (in grams) for Examples 1-3 and Comparative Example A according to ASTM standard G65-00el -"Standard Test-Method for Meusmrng-Abrasion Using the Dry Sand/Rubber Wheel Apparatus". The results, Table 1 below, show the abrasion resistance of the coating prepared according to the invention to be greater than three times that of Comparative Example A. Table I Example Mass loss, grams Ex. 1 1.3 Ex.2 1.5 Ex.3 1.2 Comp A 5.1 Example 5 Feed particles were made as described in Example 1 using the following 50-gram mixture: 19.3 grams of alumina particles (obtained from Alcoa Industrial Chemicals, Bauxite, AR under the trade designation "A16SG"), 9.5 grams of zirconium oxide particles (obtained from Zirconia Sales, Inc. of Marietta, GA under the trade designation "DK-2"). and 21.2 grams of lanthanum oxide particles (obtained from Molycorp Inc., Mountain Pass, CA). The feed particles were then screened through a 30-mesh screen (600-micromtcr opening size screen) and heat-treated at 1400°C for 2 hours in an electrically heated furnace (obtained from CM Furnaces, Bloomfield, NJ under the trade designation "Rapid Temp Furnace"). The heat-treated particles were further screened to separate out particles with .. diameters smaller than 100 micrometers, which were then sprayed through a plasma gun.: (obtained under the trade designation "Praxair SG-100 Plasma Gun" from Praxair Surface Technologies, Concord, NH), and into a cylindrical port attached perpendicularly to a cylindrical steel container covered on top with baffles, to collect plasma-sprayed particles. The feed particles were fed (using a Praxair Model 1270 computerized powder feeder obtained from Praxair Surface Technologies, Concord, NH) into the plasma through an orifice in the anode of the plasma gun. The feed orifice was tilted approximately 30 degrees towards the back of the plasma gun to increase the residence time of the particles in the plasma. Nitrogen gas was used as the earner gas to transport the feed into the plasma. The plasma gases of argon, helium (auxiliary gas), and nitrogen (auxiliary and carrier gas) Formed a highly energetic "tri-gas" plasma to uniformly melt the particles. The following conditions were used: Gun current of 1150 Amperes, Potential of 52 Volts, Arc gas (argon at 0.28 MPa (40 psi», Auxiliary gas (helium at 0.28 MPa (40 psi)), Auxiliary gas (nitrogen at 0.28 MPa (40 psi)), Carrier gas (100 volume percent nitrogen at 0.28 MPa (40 psi)). Optical microscopy observation of the resulting plasma-sprayed particles showed a mixture of spherical, elongated, and splat-like shapes, which were predominantly transparent or amorphous. Amorphous material is typically transparent due to the lack of light scattering centers such as crystal boundaries, while the crystalline particles arc opaque due to light scattering effects of the crystal boundaries. The plasma-sprayed particles were crystallized at 1300°C for 1 hour in an electrically heated furnace {obtained from CM Furnaces, Bloomfield, NJ under the trade designation "Rapid Temp Furnace"). The crystalline phases were determined by powder XRD analysis as described in Example i. The resulting crystalline material included LaAlOj, Z1O2 (cubic, tetragonal), LaAInOis, and transitional ANOj phases. Example 6 Plasma-sprayed particles were made according to Example 5, except the "Praxair SG-100 Plasma Gun" was modified using a Miller Thermal 20S9 A extension nozzle (obtained from Praxair Surface Technologies, Concord, NH). This configuration allowed the plasma-sprayed particles to be directed into a water bath for collection. Optical microscopy observation of the resulting plasma-processed particles showed a mixture of shapes, which were predominantly transparent/amorphous. The plasma-sprayed particles were crystallized at 1300X for I hour in an electrically heated furnace (obtained from CM Furnaces, Bloomfieid, NJ under the trade designation "Rapid Temp Furnace")- The crystalline phases were determined by powder XRD analysis as described in Example 1. The resulting crystalline material included LaAIO;, &O2 (cubic, tetragonal), LaAi,|Oia, and transitional Al203 phases. Various modifications and alterations of this invention will become apparent to those skilled in the art without departing from the scope and spirit of this invention, and it should be understood that this invention is not to be unduly limited to the illustrative embodiments set forth herein. WE CLAIM : 1. A method for making amoiphous matenal, the method comprising: feeding particles into a pliismu to provide a melt, the particles comprising ai least 35 percent by weight AI203, based on the total weight of the particles, and a metal oxide other than AliOs, wherein the particles contain not more than 10 percent by weight collectively ASiOj, B2O3, GeO;. P2O5, SiO^, Te02, and V2O5, based on the total weight of the particles, with the proviso that if the metal oxide other than AI2O3 is ZrOz, then the particles comprise a metal oxide other than AI203 and ZrO:; and spraying and cooling the melt to provide amorphous material, the amorphous material comprising at least 35 percent by weight AI2O3, based on the total weight of the amoiphous material, and the metal oxide other than AI2O3, wherein the amorphous material contains not more than 10 percent by weight collectively AS2O3, B2O3, Ge02, P2O5, SiOi, TeOi.and VjOs, based on the total weight of the amorphous material, wherein the amorphous material has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and 2 dimensions is at least 25 micrometers, with the proviso that if the metal oxide other than AI2O3 is Zr02, then the particles comprise a metal oxide other than AI2O3 und ZiO^ at least a portion of which forms at least one distinct crystalline phase when the amorphous material is crystallized. 2. The method according to claim 1 wherein spraying and cooling the melt includes spraying the melt onto a substrate and cooling to provide the amorphous material. 3. The method according to claim 1 wherein spraying and cooling the melt includes spraying the melt into a liquid to cool the melt and provide particles comprising the amorphous material. 4. The method according to claim 1 wherein the particles each comprise at least 35 percent by weight AI2O3, based on the total weight of the particle, and wherein the amorphous material comprises at least 35 percent by weight AI3O3, based on the total weight of the amorphous material. 5. The method according to claim 1 wherein spraying and cooling the melt provides ceramic comprising the amoq>hous material. 6. A composite material comprising discrete crystalline regions within an amoiphous matrix, wherein the crystalline regions and the amorphous matrix each independently comprise at least 35 pcvcent by weight AI2O3, based on the total weight of the crystalline regions and the amoi-phous matrix, respectively, and a metal oxide other than AI2O3, wherein the crystalline regions and the amorphous matrix each contain not more than 10 percent by weight collectively AS2O3, B2O3, GeOz, P2O5, SiOj, TeO^, and V2OS. based on the total weight of the crystalline regions and the amorphous matrix, respectively, and wherein the composite material has x, y, and z dimensions each perpendicular to each other, and wherein each of the x, y, and z dimensions is at least 150 micrometers. 7- The composite material according to claim 6 wherein the amorphous matrix does not have a T^. 8. The composite material according to claim 6 wherein the amorphous matrix is glass. 9. A layer of the composite material according to claim, 6. 10- A composite layer comprising an amorphous layer and a layer of the composite materia! according to claim, 6. 11. The composiie material according to claim 6 comprising a first portion and a second portion, wherein the first portion has an average number of the discrete crystalline regions per mm\ wherein the second portion has an average number of the discrete crystalline regions per mm , and u-herein the average number of the discrete crystalline regions permm3 of the first portion is greater than the average number of the discrete crystalline regions per mm3 of the second portion. 12. The composite material according to claim 11 "comprising a third portion disposed between the first and second portions, wherein the third portion has an average number of the discrete crystalline regions per mm"*, and wherein the average number of the discrete crystalline regions per mm' of the third portion is greater than the average number of the discrete crystalline regions per mm3 of the second portion, and less than the average number of the discreve crystalline regions per mm3 of the first portion. 13. The composite material according to claim 11 wherein the average number of the discrete crystalline regions per mm3 for the first portion is at least 50 percent larger than the average number of the discrete crystalline regions per mm" for the second portion. 14. A layer of the composite material according to claim 11.

Documents:

108-chenp-2005 abstract duplicate.pdf

108-chenp-2005 abstract.pdf

108-chenp-2005 assignment.pdf

108-chenp-2005 claims duplicate.pdf

108-chenp-2005 claims.pdf

108-chenp-2005 correspondence others.pdf

108-chenp-2005 correspondence po.pdf

108-chenp-2005 description (complete) duplicate.pdf

108-chenp-2005 description (complete).pdf

108-chenp-2005 drawings duplicate.pdf

108-chenp-2005 drawings.pdf

108-chenp-2005 form-1.pdf

108-chenp-2005 form-18.pdf

108-chenp-2005 form-26.pdf

108-chenp-2005 form-3.pdf

108-chenp-2005 form-5.pdf

108-chenp-2005 others.pdf

108-chenp-2005 pct.pdf

108-chenp-2005 petition.pdf