EP2844627A2 - Refractory metal boride ceramics and methods of making thereof - Google Patents
Refractory metal boride ceramics and methods of making thereofInfo
- Publication number
- EP2844627A2 EP2844627A2 EP13806734.3A EP13806734A EP2844627A2 EP 2844627 A2 EP2844627 A2 EP 2844627A2 EP 13806734 A EP13806734 A EP 13806734A EP 2844627 A2 EP2844627 A2 EP 2844627A2
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- EP
- European Patent Office
- Prior art keywords
- metal
- composition
- refractory
- nanoparticles
- carbon
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Definitions
- the present disclosure is generally related to synthesis of refractory-metal borides, such as titanium boride and zirconium boride.
- Refractory transition metal borides have some of the highest known melting points (2600-3900°C) and also outstanding hardness, chemical inertness, thermal conductivity, wear resistance, electrocatalytic activity, and neutron absorption ability. Films, fibers, and powders of these ceramics have been made from polymeric precursors, but large monolithic shapes elude the polymeric method.
- Refractory MBs are typically prepared by powder metallurgy methods such as hot press sintering at temperatures over 2000°C. Ordinarily, metal boride ceramics made by this technique, which is both energy and time intensive, result in brittle materials, owing partly to the large granular structure and the inconsistency in the MB particle sizes.
- thermomechanical For these applications, progress will come when materials are developed that can be easily processed into shaped components with the required thermomechanical and
- the refractory interstitial transition metal borides are extremely hard, inert, and refractory materials.
- metal boride ceramics from metal compounds and boron sources such as boron oxide and boron carbide and metal compounds (oxides and halides) have resulted in either powders or poorly formed films.
- metal compounds and boron sources such as boron oxide and boron carbide and metal compounds (oxides and halides)
- metal compounds and boron sources such as boron oxide and boron carbide and metal compounds (oxides and halides)
- metal borides oxide and boron carbide and metal compounds (oxides and halides)
- metal borides with small particle size and high surface area such as titanium boride, zirconium boride, and hafnium boride due to their potential application as in ballistic armor, electronic and thermal conductivity materials, advanced hypersonic engines, airframe leading edges on sharp-bodied reentry vehicles, and nuclear reactors.
- refractory metal borides for leading edge and nose cap applications which require moderately high temperatures.
- the refractory metal borides have been combined with other ceramics such as silicon carbide to improve the oxidation resistance of these materials in the ultra high temperature region.
- Many of these metal borides also have metallic like conductivity and/or unusual magnetic properties.
- these materials have been prepared by high temperature powder techniques that are limited in their ability to generate homogeneous materials with controlled compositions and macroscopic properties.
- composition comprising nanoparticles of a refractory-metal boride and a carbonaceous matrix.
- the composition is not in the form of a powder.
- composition comprising a metal component, boron, and an organic component.
- the metal component is selected from nanoparticles or particles of a refractory metal and a refractory-metal compound capable of decomposing into refractory-metal nanoparticles.
- the organic component is selected from an organic compound having a char yield of at least 60% by weight and a thermoset made from the organic compound.
- Also disclosed herein is a method comprising combining particles of a refractory metal or a refractory-metal compound capable of reacting or decomposing into refractory-metal nanoparticles, boron, and an organic compound having a char yield of at least 60% by weight to form a precursor mixture.
- Also disclosed herein is a method comprising: providing a precursor mixture of particles of a refractory metal or a refractory-metal compound capable of decomposing into refractory-metal nanoparticles, boron, and an organic compound; heating the precursor mixture in an inert atmosphere at elevated pressure and at a temperature that causes decomposition of the refractory-metal compound to form refractory-metal nanoparticles to form a metal nanoparticle composition; and heating the metal nanoparticle composition in an inert atmosphere, argon, or nitrogen at a temperature that causes formation of a ceramic comprising nanoparticles of a refractory-metal boride in a carbonaceous matrix.
- the organic compound has a char yield of at least 60%) by weight when heated at the elevated pressure.
- composition comprising nanoparticles of a refractory-metal boride.
- the composition is not in the form of a powder.
- composition comprising the above metal component and boron.
- a method comprising: combining particles of a refractory metal or a refractory-metal compound capable of decomposing or reacting into refractory-metal nanoparticles with boron to form a precursor mixture; and heating the precursor mixture in an inert atmosphere or vacuum at a temperature that causes formation of nanoparticles comprising a boride of the refractory metal.
- Fig. 1 schematically illustrates a process for forming the disclosed compositions.
- Fig. 2 schematically illustrates metal nanoparticles 10 embedded in a thermoset matrix
- Fig. 3 schematically illustrates the transfer 40 of boron atoms and carbon atoms from the carbon matrix 30 to the nanoparticles 50.
- Fig. 4 schematically illustrates metal boride nanoparticles 60 in a carbonaceous matrix
- Fig. 5 shows an X-ray diffraction analysis (XRD) of a sample containing TiB 2 and TiC nanoparticles.
- Fig. 6 shows a photograph of a sample containing TiB 2 and TiC nanoparticles.
- Fig. 7 shows an XRD of a sample containing ZrB 2 and ZrC nanoparticles.
- Fig. 8 shows a photograph of a sample containing ZrB 2 and ZrC nanoparticles.
- Fig. 9 shows an XRD of a sample containing HfB 2 and HfC nanoparticles.
- Fig. 10 shows a photograph of a sample containing HfB 2 and HfC nanoparticles.
- Fig. 11 shows an XRD of a sample containing WB 2 and WC nanoparticles.
- Fig. 12 shows an XRD of a sample containing TaB 2 and TaC nanoparticles.
- Fig. 13 shows a photograph of a sample containing TaB 2 and TaC nanoparticles.
- Fig. 14 shows an XRD of a sample containing TiB 2 , TiC, ZrB 2 , and ZrC nanoparticles.
- Fig. 15 shows an XRD of a sample containing TaB 2 , TaC, HfB 2 , and HfC nanoparticles.
- Fig. 16 shows an XRD of a sample containing only ZrB 2 nanoparticles.
- Fig. 17 shows an XRD of a sample containing ZrB 2 , ZrC, and ZrN nanoparticles.
- refractory metal diboride Groups IV- VI ceramics with or without a carbon matrix in one step affording a shaped composition with structural integrity
- various refractory metal nanoparticle-boron-carbon precursor compositions (3) their conversion to shaped thermosets, (4) metal boride and metal boride-metal carbide carbon matrix compositions at multiple stages, (5) the nanoparticle metal boride and nanoparticle metal boride-nanoparticle metal carbide carbon matrix compositions, and
- the synthetic method disclosed herein may result in the formation of nanoparticle metal borides.
- the composition may be consolidated under pressure to remove air pockets and force the reactants into intimate contact at least to the thermoset stage.
- the invention permits the metal boride-metal carbide carbon composites to be easily shaped by liquid molding procedures (injection molding, infusion molding, vacuum molding, spreading, etc), which is a far less costly and involved process than machining a hot press sintered material.
- metal borides/nitrides may be formed.
- the materials, methods, and conditions are the same as disclosed elsewhere herein except for the absence of the carbon compound.
- a metal and boron precursor composition may be shaped to a form under high pressure and then heated to temperatures necessary as a stand alone (removal from mold) or in the mold to form the metal boride and metal nitride.
- Metal borides would be formed by heating such a composition under argon or helium atmosphere whereas metal boride- metal nitride would form by heating in a nitrogen atmosphere with the metal nitride being formed mainly on the exterior part of a solid component. The method described above does not yield a thermoset since the carbon precursor is not present.
- the methods may produce refractory metal (Ti, W, Nb, Zr, Mo, Cr, V, Ta, and Hf) borides in shaped solid configurations from metal nanoparticles. Mixed phases using multiple metals can also be produced.
- the ceramics are produced as nanoparticles.
- any metal compound capable of forming stable borides or carbides, and which decomposes into highly reactive metal nanoparticles is combined with b) elemental boron, and (c) carbon precursors that melt and only contain carbon and hydrogen
- the combination may be thermally converted to (d) a solid shape containing high yields of both pure metal borides and metal carbides, and possibly some amount of a pure carbon phase.
- the quantity of the metal boride and metal carbide formed depends on the amount of elemental boron and carbon precursor present in the precursor composition (metal nanoparticles, boron, and carbon precursor).
- the appropriate metal nanoparticles are formed in situ from the thermal decompositions of metal compounds (including but not limited to carbonyls and hydrides) within the precursor composition.
- the carbon sources may be melt processable aromatic-containing acetylenes or low molecular weight polymers that exhibit extremely high char yields.
- the carbon precursor may contain only C and H to insure that heteroatoms (such as nitrogen) are not incorporated into the interstitial sites of the metal nanoparticles during the reaction to produce the metal boride and metal carbide carbon matrix composition.
- the metal boride and metal carbide may form between 500-1600°C under inert conditions from reaction of the highly reactive metal nanoparticles with elemental boron and the carbon precursor (degradation above 400°C) with the reaction occurring much faster at the higher temperatures.
- the temperatures at which the synthetic process occurs may be well below those normally associated with the formation of boride and carbide ceramics.
- the carbon precursor is used or is present to glue or bond the individual formed ceramic nanoparticles together as they form within the resulting nanostructured or amorphous elastic carbon.
- the formed carbon behaves as a matrix to afford structural integrity and to ensure a shaped composition for the developing high surface area ceramic nanoparticles. Pressure may be applied to the composition during the heat treatment and conversion to the shaped thermoset to ensure intimate contact of the reactants and to remove any voids or air pockets ensuring a high density ceramic that does not contain defects.
- metal compounds are combined with elemental boron and a carbon precursor that melts.
- the carbon precursors are compounds such as polymers or resins with functional unsaturation to interact with the metal nanoparticles that form from the metal compounds. The unsaturations also permit the carbon precursor to undergo conversion from the melt to form thermosets or crosslinked polymers.
- a typical precursor composition includes the boron, the carbon precursor, and the metal compound or multiple metal compounds. Upon heating this composition, the carbon precursor melts at its melting point and may be thermally converted to a shaped solid thermoset 20 through reaction of the unsaturated sites.
- the carbon precursor can also be partially cured to a B-stage to increase the viscosity but still meltable to enhance the processability and retention of homogeneity within the precursor composition. It is possible that during this step or a subsequent step the metal compound thermally decomposes into metal nanoparticles 10 or the metal powder reacts with the organic component to form nanoparticles which are embedded in the solid thermoset (Fig. 2).
- the formation of the metal nanoparticles may occur later during the next step in the process, which is the extended heat treatment at higher temperatures.
- Thermal treatment of the thermoset above 500°C results in carbonization of the carbon precursor 30 and also reaction 40 between the metal nanoparticles 50 and both the boron source and the now carbonized carbon precursor to form the nanoparticles 60 of the metal boride ceramic (major component) and the metal carbide ceramic (minor component) (Figs. 3-4).
- the resulting solid shaped ceramic can be tailored to contain mainly the metal boride.
- the formation of the reactive metal nanoparticles can occur during the thermal treatment step, instead of the earlier thermosetting step.
- a sufficiently high proportion of carbon precursor is used, an excess of pure solid carbon will remain as a matrix in which the boride and carbide ceramics are embedded.
- the reaction can also be conducted without the thermoset- forming carbon precursor, using only the refractory metal compound and boron to yield the metal boride alone.
- the amount of metal boride, metal carbide, and carbon within the resulting composition can be varied based on the quantity of each individual component (metal compound, boron, and melt processable carbon compound) mixed for usage in the precursor composition.
- the reaction is performed in a nonreactive inert gas such as argon or helium or vacuum.
- metal nitride nanoparticles may also be formed.
- metal boride and both metal nitride and metal carbide may form with the metal carbide and metal boride mainly on the interior part of composition where the nitrogen cannot be in intimate contact.
- Reaction of metal salts and decomposition to metal nanoparticles may occur at lower temperatures with reaction to the ceramics occurring by 1200°C but higher temperatures may be needed at least to 1600°C for metal powders of micron size. Smaller size particles may react faster and be totally consumed at lower temperatures relative to the larger particle size powders.
- the particle size of the metal boride/carbide/nitride can be controlled as a function of the upper temperature treatment with higher exposure temperatures affording larger particle size ceramics.
- the refractory metal boride and metal carbide may form as nanoparticles. This is a highly desirable result, as it is generally accepted that homogeneous nanoparticle composites of ceramics will have better properties than their much more common microparticle counterparts.
- the ceramics are fabricated from micron size powdered particles by sintering techniques at extremely high temperatures. An excess of carbon atoms can be made available for reaction with the metal content and to ensure the formation of a carbon matrix in which the refractory metal borides and carbides are bound, or the reaction can be conducted
- the amount of metal boride, metal carbide, and carbon within the resulting composition can be varied based on the quantity of each individual component (metal compound, boron, and melt processable carbon compound) mixed for usage in the precursor composition.
- the metal nanoparticle When the reaction is performed in a nitrogen atmosphere, the metal nanoparticle may
- Carbon, ceramic, and metal fibers may be incorporated into various mixtures of precursor compositions composed of boron, metal compounds of Groups IV -VI, and the acetylene-containing aromatic compounds or polymers (carbon source) and the resulting fiber- containing mixture is converted to a shaped solid followed by heating to higher temperatures. Following the same heat treatment steps as defined above results in a composition of some proportion of metal boride, metal carbide, carbon, and fibers, which are intended to serve as a reinforcement component.
- the precursor composition (metal salt, boron, and carbon precursor) described above are mixed with continuous fibers or chopped fibers and heated until conversion to the shaped thermoset forms.
- the tough, solid shaped composite can be used for structural applications in excess of 3000°C.
- the composite may be exposed to an upper temperature for which it is going to be used so that the physical properties may remain intact and not change.
- the precursor composition can contain a combination of different refractory metal compounds that will lead to a mixture of ceramics in the composite, which could be beneficial for specific applications.
- metal nitride-containing ceramics may form with a direct incorporation of nitrogen into the lattices of the metal atoms/nanoparticles.
- metal boride/metal carbide/carbon-matrix composition or a metal boride/metal nitride/metal carbide carbon-matrix composition or combination thereof.
- the composite may have outstanding oxidative stability and temperature capabilities in excess of 3000°C.
- Shaped solid precursor compositions can be fabricated from the precursor metal component, boron, and carbon source or metal component and boron compositions under pressure.
- the various precursor compositions may be formulated and milled to convert to very small particle sizes, such as, for example, up to 100 ⁇ or up to 10 ⁇ .
- Shaped pellets or other shaped components can be formed under pressure to consolidate the small milled particles into intimate contact and with structural integrity for removal from the pressure system followed by thermal conversion to the ceramic.
- the heating of the shaped precursors occurs from ambient conditions at a very slow rate (such as up to 10, 5, 3, or 2°C/min) to control the rate of decomposition of the metal hydride into the atomic-to-nanoparticle size metal, which is very reactive and will commence to react with the boron and/or carbon source as the nanoparticles form.
- the heating can occur in vacuum or under inert atmospheres such as argon or nitrogen.
- the atoms of each reactants can readily move across the boundaries to ensure strong bonding between the nanoparticle metal borides being formed.
- the ceramic nanoparticles show strong interaction within the solid ceramic and the formed solid shaped ceramics exhibit toughness, hardness and structural integrity.
- the process is outlined in Fig. 1 and schematically illustrated in Figs. 2-4. Any reactions described are not limiting of the presently claimed methods and compositions. It is speculated that the nanoparticle form of the refractory metal is highly reactive with the elemental boron and the carbon source, thereby lowering the temperature of the formation of metal borides and metal carbides. Moreover, at least a stoichiometric amount of metal nanoparticles and boron and perhaps a slight excess of boron and a minimum amount of carbon precursor may be included in the precursor composition. Any excess boron would react with the carbon to form boron carbide, which would reduce the amount of metal carbide that can potentially form.
- the metal boride and metal carbide carbon-matrix composites are expected to show enhanced toughness, owing to the presence of the relatively elastic carbon, which would exist in forms ranging from amorphous to nanotube to graphitic carbon.
- the native presence of an "elastic" carbon matrix may allow for toughening of the inherently brittle sintered ceramics.
- the carbon may permit operation of the toughened ceramic at extremely high temperatures, owing to carbon's high melting point (>3000°C).
- Ceramic/carbon-matrix compositions are currently sought for these reasons, and the present method may permit straightforward preparation of these composites in a single step for the first time, in contrast to the traditional means of first forming the ceramic powder and then preparing the metal boride shaped composition under sintering conditions. Only trace or very small amounts of carbon may be needed to achieve the effect. Also, the ratio of ceramic to carbon is easily tuned based on the ratio of metal-compound or metal powder to elemental boron to carbon-precursor.
- Fiber-reinforced refractory metal boride carbon matrix composites may exhibit outstanding mechanical properties for usage under extreme environmental high temperature conditions. Finely divided fiber reinforced refractory nanoparticle metal boride carbon composites can allow the consolidation of fully dense shaped solid components with extreme fracture resistance for uses in high stress and temperature applications such as advanced engine components for hypersonic vehicles and automobiles, and for nuclear reactors and fuel cells, where increased operation temperature and mechanical integrity could translate into tremendous economic advantages.
- the fiber reinforced ceramic composites could be beneficial in the construction of manufacturing facilities needing the high temperature properties and structural integrity of the composites such as in steel mills and coal burning electrical facilities.
- Such tough, easily shaped ceramic composites are critical to the next generation of jet engines and engines for hypersonic vehicles, which are being designed to operate at higher internal temperatures and stresses than those in current service, in advanced automobile engines and supporting components, and in the design of advanced engine components and supporting structural components.
- High temperature ship deck plates could be readily fabricated for aircraft carriers needing the superior heat resistant properties of the metal boride/metal carbide ceramic- carbon composites.
- lightweight, tough, and hard ceramics easily made in controllable forms could be very important for the fabrication of superior military armor; again fabricated in a reactor or mold in a shaped structure.
- the ability to fabricate tough, shaped refractory metal boride components in one step enhances their importance due to the economic advantages and the elimination of machining to a shaped component.
- the disclosed methods can create nanosized metal borides from already well-formed metal nanoparticles within a relatively narrow size range.
- the process appears to be largely mediated by the high reactivity of the metal nanoparticles toward the boron in excess and the carbon source, above which the kinetics may be determined by the rate of boron and carbon insertion into the metal lattice, and subsequent localization in the appropriate crystallographic positions for formation of the ceramic, implying straightforward control of the rate of the process by temperature.
- a metal component which may be a refractory-metal compound capable of decomposing into refractory metal nanoparticles or particles of a refractory metal.
- Any refractory metal may be used, including but not limited to a group IV- VI transition metal, titanium, zirconium, hafnium, tungsten, niobium, molybdenum, chromium, tantalum, or vanadium.
- a pure metal it may be in the form of nanoparticles or other particles such as a powder.
- the metal may directly react with the boron or organic component. Suitable powders include, but are not limited to, tungsten and tantalum.
- a compound containing the metal atom may be used. Such compounds decompose at elevated temperatures, releasing the metal atoms so that they may react with the boron or organic component. Suitable such compounds include, but are not limited to, a salt, a hydride, a carbonyl compound, or a halide of the refractory metal. Examples include titanium hydride, zirconium hydride, and hafnium hydride. Other examples and embodiments of types of compounds which may be used with the metals disclosed herein may be disclosed in US Patent Nos. 6,673,953; 6,770,583; 6,846,345; 6,884,861; 7,722,851; 7,819,938; 8,277,534.
- the second component is boron in elemental form. Suitable boron is readily available in powder form. A 95-97 % boron is suitable with a higher pure boron powder (99%) being preferred. The boron powder may be milled to reduce its particle size.
- the third component is an organic compound that has a char yield of at least 60% by weight.
- the char yield may also be as high as at least 70%>, 80%>, 90%>, or 95% by weight.
- the char yield of a potential compound may be determined by comparing the weight of a sample before and after heating to at least 1000°C for at least 1 hr in an inert atmosphere such as nitrogen or argon. Any such compounds with high char yields may be used as the charring may play a role in the mechanism of the reactions. This char yield may be measured at an elevated pressure to be used when a heating step is also performed at such pressure.
- a compound having a low char yield at atmospheric pressure but having a high char yield under external pressure or the conditions that the disclosed methods are performed may be suitable for producing metal borides, carbides, and nitrides.
- the organic compound may be omitted to form pure metal boride and optionally metal nitride.
- Certain organic compounds may exhibit any of the following characteristics, including mutually consistent combinations of characteristics: containing only carbon and hydrogen;
- containing aromatic and acetylene groups containing only carbon, hydrogen, and nitrogen or oxygen; containing no oxygen; and containing a heteroatom other than oxygen. It may have a melting point of at most 400°C, 350°C, 300°C, 250°C, 200°C or 150°C and the melting may occur before polymerization or degradation of the compound.
- organic compounds include, but are not limited to, l,2,4,5-tetrakis(phenylethynyl)benzene (TPEB), 4,4'- diethynylbiphenyl (DEBP), N, N'-(l,4-phenylenedimethylidyne)-bis(3-ethynylaniline) (PDEA), N,N'-(1 ,4-phenylenedimethylidyne)-bis(3,4-dicyanoaniline) (dianilphthalonitrile), and l,3-bis(3,4-dicyanophenoxy)benzene (resorcinol phthalonitrile) or a prepolymer thereof.
- TPEB l,2,4,5-tetrakis(phenylethynyl)benzene
- DEBP 4,4'- diethynylbiphenyl
- PDEA N, N'-(l,4-phenylenedimethylidy
- Prepolymers may also be used, such as a prepolymer of TPEB or other suitable organic compounds. Different compounds can be blended together and/or reacted to a prepolymer stage before usage as the organic compound of the precursor composition. The presence of nitrogen atoms in the organic compound may produce metal nitrides in the ceramic without the use of a nitrogen atmosphere.
- More than one metal, metal compound, and/or organic compound may be used. Two or more different metals may be used to produce two different metal borides, carbides, and/or nitrides in the ceramic. Also, in some cases only one compound may be used when the metal component and the organic component are the same compound. Such compounds may be high in carbon and hydrogen to produce a high char yield, but also have a refractory metal bound to the compound.
- An optional component in the precursor materials is a plurality of fibers or other fillers.
- fibers include, but are not limited to, carbon fibers, ceramic fibers, and metal fibers.
- the fibers may be of any dimension that can be incorporated into the mixture and may be cut or chopped to shorter dimensions.
- the precursor mixture which may be mixed in a melt stage and/or consolidated under pressure, then undergoes a heating step to form a metal nanoparticle composition.
- a heating step to form a metal nanoparticle composition.
- This may be performed while the mixture is in a mold. This will allow the final product to have the same shape as the mold, as the organic component of the mixture will melt if not already liquid and the mixture will fill the mold during the heating, and retain its shape when the ceramic is formed.
- the precursor mixture is heated in an inert atmosphere at a temperature that causes decomposition of the refractory-metal compound to form refractory-metal nanoparticles. If the organic compound is volatile, the heating may be performed under pressure to avoid evaporation of the organic compound.
- this heating step includes the formation of nanoparticles from a metal powder. As the reaction proceeds from the metal powder, the metal particles will become smaller. It is not necessary to verify that the nanoparticles are formed in order to continue with the method. However, any known technique for detecting nanoparticles such as SEM, TEM, or x-ray diffraction analysis (XRD) may be used if desired to verify that the metal component suitably produces nanoparticles. Suitable heating temperatures include, but are not limited to, 150-500 or 700°C.
- Heating the precursor may also cause the polymerization of the organic compound to a thermoset.
- the metal nanoparticles 10 would then be dispersed throughout the thermoset 20 as shown in Fig. 2.
- the organic compound may also polymerize before the nanoparticles are formed.
- thermoset may also be machined to a desired shape, followed by heating to form a ceramic as described below. The thermoset is not formed if the organic compound is omitted.
- the metal source may be homogeneously distributed or embedded in the thermoset as an intermediate shaped solid.
- the composition may have a shape that it will retain upon further heating and conversion to the ceramic from reaction of the metal source with the developing carbon matrix.
- the precursor mixture may be consolidated to a shaped solid component under pressure to promote intimate contact of the reactants to provide a very dense ceramic solid or to density the final product.
- the precursor mixture may be compacted under exterior pressure, removed from the pressure, and then heated to a thermoset followed by conversion to the ceramic.
- the precursor mixture may be compacted under exterior pressure and the pressure maintained while heating to the thermoset and ceramic.
- the metal nanoparticle composition is heated to form a ceramic.
- the heating is performed at a temperature that causes formation of nanoparticles of a refractory-metal boride 60 and a refractory-metal carbide in a carbonaceous matrix 70 (Fig. 4).
- the carbonaceous matrix may comprise graphitic carbon, carbon nanotubes, and/or amorphous carbon. There is no carbonaceous matrix if the organic compound is omitted. If nitrogen is present, metal nitride nanoparticles may be formed. There may be a higher concentration of nitrides on the surface than in the interior. Suitable heating temperatures include, but are not limited to 500-1900°C.
- Nanoparticles that may be formed include, but are not limited to, titanium boride, titanium carbide, zirconium boride, zirconium carbide, hafnium boride, hafnium carbide, tungsten boride, tungsten carbide, tantalum boride, tantalum carbide, and Hf aC 2 .
- the presence and composition of the metal boride or carbide particles may be verified by any known technique for detecting nanoparticles such as SEM, TEM, or XRD.
- the nanoparticles may have an average diameter of less than 100 nm, 50 nm, or 30 nm. They may be generally spherical in shape or may be non-spherical, such as nanorods.
- the ceramic may include any amount of nanoparticles, including but not limited to, at least 5%, 10%, 20%, 30%, 40%, 50%, 60%, 70%, 80%, 90%, 95%, or 99% by weight of nanoparticles.
- the percentage of nanoparticles may be in part determined by the molar ratio of metal to boron and carbon atoms in the precursor mixture. At a 1 : 1 ratio, nearly all of the boron and carbon may be incorporated into the nanoparticles, leaving a small amount or trace of carbonaceous matrix. Higher amounts of boron may result in a higher ratio of metal boride to metal carbide nanoparticles. With higher amounts of organic compound, the fraction of metal carbide nanoparticles is lower and the fraction of carbonaceous matrix is higher.
- variations in the ratio of metal to boron to organic may be used, affording a mixture of metal boron and metal carbide when performed in an inert atmosphere such as argon and metal boron, metal carbide, and metal nitride when performed in a nitrogen atmosphere.
- an inert atmosphere such as argon and metal boron, metal carbide, and metal nitride when performed in a nitrogen atmosphere.
- the ceramic is not formed as a powder and may be in the form of a solid, unbroken mass. It may contain less than 20%> by volume of voids or as low as 10%>, 5%, or 1%. It may have the same shape as the precursor mixture (if solid) or it may take on the shape of a mold it was placed in during the heating. The ceramic may retain its shape in that it does not crumble when handled and may not change shape or break without the use of extreme force.
- the ceramic composition may be tough, hard, and have structural integrity. The degree of such properties may depend on the amount of ceramic to carbon in the solid ceramic composition. Any shape may be formed to make an article useful for incorporation into an apparatus. The article may be large enough to have a minimum size of at least 1 cm in all dimensions.
- the entire surface of the article is at least 5 mm from the center of mass of the article. Larger articles may be made, such as having a minimum size of at least 10 cm in all dimensions. Also, the composition may have smaller sizes, such as 1 mm, 2 mm, or 5 mm.
- a third heating step may also be performed, where the ceramic is heated in an oxygen- containing atmosphere to form an oxide of the refractory metal on the surface of the ceramic. For example, titanium oxide may be formed on the surface. Such surface oxidation may protect the interior of the ceramic from further oxidation.
- Preliminary TGA-DSC thermal analysis study to determine the conditions for formation of refractory TiB 2 ceramic solid in one step by heating at 10°C/min to 1400°C under an argon atmosphere -
- a sample (16.8960 mg) of the precursor composition prepared in Example 1 was weighed into a TGA ceramic pan, flushed for 15 min in a flow (110 cc/min) of argon, and then heated in a TGA chamber at 10°C/min to 1400°C using a Q600 TGA-DSC TA Instrument yielding a solid ceramic material.
- the DSC thermogram showed a small melting point endotherm at about 194°C (TPEB) and an exothermic transition peaking at about 282°C (reaction/cure of ethynyl groups of TPEB to form shaped thermoset polymer). As the heating was continued, the DSC thermogram showed a combination of transitions (endotherms and exotherms) commencing above 480°C with an endotherm at about 533°C followed by an exotherm peaking at about 590°C. During the thermal treatment to 1400°C, the sample lost only a small amount of weight with retention of 96.78% weight at 1400°C. The ceramic carbon solid composition was formed in one step and exhibited structural integrity.
- a sample (88.8430 mg) of the precursor composition prepared in Example 1 was weighed into a TGA ceramic pan, packed with a flat surface, and heated in a TGA chamber under an argon atmosphere at 10°C/min to and at 250°C for 2 hr to consolidate to a shaped solid thermoset polymer.
- the sample showed an endothermic transition at about 195°C attributed to the melting point of TPEB.
- the isothermal heat treatment at 250°C resulted in the reaction of the ethynyl units in the TPEB and conversion to the shaped thermoset polymer.
- the solid polymeric sample composed of TiH 2 and boron embedded in the polymeric thermoset was then slowly heated at 3°C/min to and at 1300°C for 3 hr affording a solid ceramic material with weight retention of 96.06%. Above 400°C, degradation of the TiH 2 occurred to Ti nanoparticles and H 2 ; the H 2 vaporized from the sample. Further heating above 500°C to 1300°C resulted in the reaction of the highly reactive Ti nanoparticles with the developing carbon atoms being formed from the carbonization of TPEB during the heat treatment resulting in the formation of high yields of TiB 2 nanoparticles and a small amount of TiC nanoparticles embedded in the excess carbon formed during the simple carbonization process.
- the nanoparticle refractory ceramic carbon matrix composite was formed in one step.
- XRD analysis (Fig. 5) of the solid sample showed a clean reaction with the formation of TiB 2 (87%) and TiC (13%).
- the particle size for the TiB 2 was 21.5 nm and for TiC it was 12.4 nm.
- Fig. 6 shows a photograph of a typical sample.
- refractory ZrB 2 solid ceramic composition in one step by heating at 10°C/min to 1400°C under an argon atmosphere -
- a sample (12.1180 mg) of the precursor composition prepared in Example 4 was weighed into a TGA ceramic pan, packed with a flat surface, and heated in a TGA chamber at 10°C under a flow (110 cc/min) of argon to 1400°C yielding a solid material with a weight retention of 98.03%.
- the sample melted at about 194°C (endothermic transition; TPEB) and exhibited an exothermic transition peaking at about 292°C attributed to the cure to a shaped solid thermoset polymer.
- TPEB endothermic transition
- the solid ceramic composition was removed from the TGA pan.
- the shaped solid ceramic refractory ZrB 2 ceramic carbon composite was formed in one step, appeared hard, and exhibited structural integrity.
- a sample (115.7420 mg) of the powdered composition prepared as in Example 4 was weighed into a TGA ceramic pan, packed with a flat surface, and heated in a TGA chamber under a flow (110 cc/min) of argon at 5°C/min to and at 250°C for 1 hr to consolidate to a shaped solid thermoset polymer.
- the sample showed an endothermic transition at about 195°C attributed to the melting point of TPEB.
- thermoset polymer sample was slowly heated at 3°C/min to 1300°C and held at this temperature for 3 hr affording a solid ceramic material with a weight retention of 93.27%. Heating from 500°C to 1300°C resulted in the reaction of the highly reactive Zr nanoparticles with the boron and the developing carbon atoms being formed from degradation of TPEB during the simple
- TPEB tetramethyl methacrylate
- boron 0.233 g, 21.5 mmol
- ZrH 2 1.50 g; 10.7 mmol
- the ratio of the three reactants can be readily varied by the described formulation method.
- nanoparticle in solid ceramic produced in one step by controlled heating at 3°C/min to 1400°C under an argon atmosphere using stoichiometric amount of boron -
- a sample (115.7420 mg) of the powdered composition prepared as in Example 7 was weighed into a TGA ceramic pan, packed with a flat surface, and heated in a TGA chamber under a flow (110 cc/min) of argon at 5°C/min to and at 250°C for 1 hr to consolidate to a shaped solid thermoset polymer.
- the sample showed an endothermic transition at about 195°C attributed to the melting point of TPEB.
- thermoset polymer sample was slowly heated at 3°C/min to 1400°C and held at this temperature for 3 hr affording weight retention of 97.27% of a ceramic solid with structural integrity.
- Heating from 500°C to 1400°C resulted in the reaction of the highly reactive Zr nanoparticles with the boron and the developing carbon atoms being formed from degradation of TPEB during the simple carbonization process resulting in the formation of ZrB 2 and ZrC nanoparticles embedded in excess carbon.
- the refractory metal ceramic carbon matrix composition was formed in one step.
- XRD analysis (Fig. 7) showed a high yield of pure ZrB 2 nanoparticles relative to ZrC nanoparticles embedded in an amorphous carbon matrix as the products formed during the heat treatment.
- TPEB 0.033 g; 0.069 mmol
- boron (0.233 g, 21.5 mmol
- ZrH 2 (1.00 g; 10.7 mmol)
- nanoparticle in ceramic solid produced in one step by controlled heating at 3°C/min to 1300°C under an argon atmosphere using stoichiometric amount of boron and smaller amount of TPEB -
- a sample (114.8850 mg) of the powdered composition prepared as in Example 9 was weighed into a TGA pan, packed with a flat surface, and heated in a TGA chamber under a flow (110 cc/min) of argon at 10°C/min to and at 250°C for 1 hr to consolidate to a shaped solid thermoset polymer.
- the isothermal heat treatment at 250°C resulted in the reaction of the ethynyl units in the TPEB and conversion to the shaped solid thermoset polymer.
- thermoset polymer contained a homogeneous distribution of ZrH 2 and boron embedded in the domain of the polymer.
- the solid thermoset polymer sample was slowly heated at 3°C/min to 1300°C and held at this temperature for 3 hr affording weight retention of 98.01% of a ceramic solid with structural integrity. Heating from 500°C to 1300°C resulted in the reaction of the highly reactive Zr nanoparticles with the boron and the developing carbon atoms being formed from degradation of TPEB presence in a smaller quantity compared to precursor compositions of Examples 4 and 7.
- the refractory metal ceramic carbon matrix composition was formed in one step.
- XRD analysis showed a high yield of pure ZrB 2 nanoparticles relative to ZrC nanoparticles embedded in an amorphous carbon matrix as the products formed during the heat treatment.
- the XRD studies showed about an 85% yield of ZrB 2 nanoparticles and 15% yield of ZrC nanoparticles with average particle sizes of 29.3 nm and 27.9 nm for ZrB 2 and ZrC, respectively.
- Preliminary TGA-DSC thermal analysis study to determine the conditions for formation of refractory HfB 2 ceramic solid in one step by heating at 10°C/min to 1400°C under an argon atmosphere -
- a sample (30.9100 mg) of the precursor composition prepared in Example 11 was weighed into a ceramic pan, packed with a flat surface, flushed for 15 min in a flow (110 cc/min) of argon, and then heated in a TGA chamber at 10°C/min to 1400°C using a Q600 TGA-DSC TA Instrument yielding a solid ceramic material with a weight retention of 98.47%.
- the DSC thermogram showed a small melting point endotherm at about 194°C (TPEB) and an exothermic transition peaking at about 282°C (reaction/cure of ethynyl groups of TPEB to form shaped thermoset polymer).
- the DSC thermogram showed two exothermic transitions peaking at about 535°C and 728 °C. As the heating was continued, the DSC thermogram was flat until about 1142 °C but started to exhibit an exothermic transition, which continued to the final temperature of 1400°C. During the thermal treatment to 1400°C, the sample lost only a small amount of weight with retention of 98.47% at 1400°C.
- the ceramic carbon solid composition was formed in one step and exhibited structural integrity.
- a sample (115.7420 mg) of the powdered composition prepared as in Example 11 was weighed into a ceramic pan, packed with a flat surface, and heated in a TGA chamber under a flow (110 cc/min) of argon at 10°C/min to and at 250°C for 1 hr to consolidate to a shaped solid thermoset polymer.
- the sample showed an endothermic transition at about 195°C attributed to the melting point of TPEB.
- thermoset polymer contained a homogeneous distribution of HfH 2 and boron embedded in the domain of the polymer. Further heating above 500°C resulted in the degradation of the HfH 2 to Hf nanoparticles and H 2 ; the H 2 vaporized from the sample as formed whereas the highly reactive Hf nanoparticles interact with the elemental boron and carbon atoms being formed from carbonization of the TPEB.
- the solid thermoset polymer sample was slowly heated at 3°C/min to and at 1300°C for 3 hr affording weight retention of 98.49% of a ceramic solid with structural integrity.
- the novel refractory metal ceramic carbon matrix composition was formed in one step.
- XRD analysis (Fig. 9) showed high yield of pure HfB 2 (87%) and HfC (13%) nanoparticles embedded in an amorphous carbon matrix as the products formed during the heat treatment.
- the XRD studies showed average particle sizes of 31.3 nm and 30.5 nm for HfB 2 and HfC, respectively.
- Fig. 10 shows a photograph of a typical sample.
- TPEB 0.018 g; 0.038 mmol
- boron 0.035 g, 3.24 mmol
- tungsten 0.500 g; 2.72 mmol
- Preliminary TGA-DSC thermal analysis study to determine the conditions for formation of refractory WB ceramic solid in one step by heating at 10°C/min to 1400°C under an argon atmosphere -
- a sample (16.8960 mg) of the precursor composition prepared in Example 14 was weighed into a ceramic pan, packed with a flat surface, flushed for 15 min in a flow (110 cc/min) of argon, and then heated in a TGA chamber at 10°C/min to 1400°C using a Q600 TGA-DSC TA Instrument yielding a solid ceramic material with a weight retention of 97.03%.
- the sample exhibited a small exotherm peaking at about 1100°C and a more intense exotherm commencing at about 1188°C.
- the ceramic carbon solid composition exhibited structural integrity.
- a sample (115.7420 mg) of the powdered composition prepared as in Example 14 was weighed into a ceramic pan, packed with a flat surface, flushed with argon for 15 min, and then heated in a TGA chamber under a flow (110 cc/min) of argon at 10°C/min to and at 250°C for 1 hr to consolidate to a solid shaped thermoset polymer.
- the sample showed an endothermic transition at about 195°C attributed to the melting point of TPEB.
- thermoset polymer contained a homogeneous distribution of tungsten powder and elemental boron embedded in the domain of the polymer. Further heating of the thermoset polymer composition resulted in the microsized tungsten particles interacting with the elemental boron and the carbon atoms being formed from carbonization of the TPEB.
- the solid thermoset polymer sample was slowly heated at 2°C/min to and at 1300°C for 3 hr affording weight retention of 97.31% of a carbon ceramic solid.
- the refractory metal ceramic carbon matrix composition was formed in one step and retained its structural integrity.
- XRD analysis (Fig. 11) showed a high yield of pure predominately WB nanoparticles with an average particle size of 24 nm along with a small amount of WC nanoparticle embedded in an amorphous carbon matrix.
- a sample (100.3100 mg) of precursor composition prepared as in Example 17 was weighed into a ceramic pan, packed with a flat surface, flushed for 15 min in a flow (110 cc/min) of argon, and then heated in a TGA chamber at 10°C/min to and at 250°C for 1 hr.
- the resulting solid thermoset polymer was then heated at 2°C/min to and at 1300°C for 3 hr followed by heating at l°C/min to and at 1400°C for 1 hr.
- XRD analysis Fig.
- Fig. 13 shows a photograph of a typical sample.
- the solid thermoset polymer was then heated at 2°C/min to and at 1300°C for 3 hr resulting in weight retention of 97.24% of a shaped solid ceramic solid.
- the carbon ceramic solid was removed and found to exhibit structural integrity.
- XRD analysis (Fig. 14) showed a very complex mixture of ceramic nanoparticle materials being formed including ZrB 2 (74%, particle size of 19.3 nm), TiB 2 (12.3%), TiC (-3.5%), and ZrC (-10%), all of which were embedded in a carbon matrix. The percentages shown are the crystalline materials in the sample.
- the XRD was so complex that it was not possible to determine the nanoparticle sizes for some of the ceramics.
- the solid thermoset polymer was then heated at 2°C/min to and at 1300°C for 3 hr followed by heating at l°C/min to and at 1400°C for 1 hr resulting in weight retention of 98.36% of a shaped ceramic solid.
- the carbon ceramic solid was removed and found to exhibit structural integrity.
- XRD analysis (Fig. 15) showed a complex mixture of ceramic nanoparticle materials being formed including TaB 2 (61.8%, particle size of 26.5 nm), HfB 2 (26.5%), TiC (8.2%), and HaTaC (2.4%). The percentages shown are the crystalline materials in the sample. The XRD was so complex that it was not possible to determine the nanoparticle sizes for some of the ceramics.
- thermoset polymer contained a homogeneous distribution of titanium hydride (TiH 2 ) and elemental boron embedded in the domain of the polymer.
- Formulation of TiH 2 , boron, and TPEB carbon fiber polymeric composite Into a 0.5 in diameter mold formed from aluminum foil was placed the precursor composition (1.8567 g of the TiH 2 , boron, and TPEB mixture) prepared as in Example 1 and a small amount of chopped carbon fibers was added and mixed. The mixture was heated to 240°C to melt the TPEB and the melted composition was pressed with a flat surface to consolidate to a flat surface.
- the resulting carbon fiber-precursor composition was then heated under a flow of argon at 260-270°C for 1 hr resulting in solidification to a shaped carbon fiber-containing polymeric thermoset in which the TiH 2 and boron were embedded within the fiber-reinforced polymer thermoset composite.
- the shaped solid carbon fiber polymeric composite was removed from the mold.
- Example 27 Conversion of the ZrH 2 and boron carbon fiber polymeric composite to ZrB 2 carbon fiber ceramic composite -
- the solid shaped carbon fiber polymeric composite prepared in Example 25 was placed in an oven and heated under a flow of argon at 3°C/min to 1200°C and held at the temperature for 3 hr.
- the resulting ceramic-carbon fiber reinforced composite was cooled at 3°C/min back to room temperature.
- Example 27
- HfH 2 , boron, and TPEB carbon fiber polymeric composite Into a 0.5 in diameter mold fabricated from aluminum foil was placed a precursor composition (2.8558 g of HfH 2 , boron, and TPEB mixture) prepared as in Example 11 and a small amount of chopped carbon fibers was added and mixed. The composition was heated to 240°C to melt the TPEB and the melted composition was pressed with a flat surface to consolidate to a flat surface. The resulting carbon fiber-precursor composition was heated under a flow of argon at 260-270°C for 1 hr resulting in solidification to a shaped carbon fiber-containing polymeric thermoset. The solid shaped carbon fiber polymeric composite with a homogeneous distribution of the HfH 2 and boron was removed from the mold.
- the shaped polymeric thermoset solid (1.55 g) from Example 31 was placed in a 3" tube furnace, heated at 2°C/min under a flow (100 cc/min) of argon to 1400°C, and held at 1400°C for 2 hr yielding a solid dense ceramic with weight retention of 97.8%.
- the solid ceramic was removed from the furnace, characterized XRD, and found to form nanoparticle sized TiB 2 along with a small amount of TiC in an excess of carbon as the matrix.
- the TiB 2 -TiC carbon solid composition was formed in one step and exhibited great structural integrity, hardness, and toughness.
- the pellet was then placed in a furnace, heated at 20°C /min under an argon atmosphere to 250°C, and held at this temperature for 30 minutes followed by heating at 2°C/min under a flow (100 cc/min) of argon to 1200°C and holding at 1200°C for 3 hr yielding a solid dense ceramic with weight retention of 97.1%.
- the solid ceramic was removed from the furnace, characterized by XRD, and found to form nanoparticle sized TiB 2 along with a small amount of TiC in an excess of carbon as the matrix.
- the TiB 2 -TiC carbon solid composition was formed in one step and exhibited great structural integrity, hardness, and toughness.
- Example 37 Conversion of precursor composition of tungsten powder, boron, and TPEB prepolymer to solid shaped thermoset -
- the pellet from Example 35 was placed in a furnace, heated at 20°C/min under an argon atmosphere to 215°C, and held at this temperature for 10 hr (overnight) resulting in the formation of a tough shaped polymeric solid.
- the tungsten and boron powders were homogeneous dispersed in the solid thermoset.
- refractory WB solid ceramic in one step by heating at 2°C/min to 1500°C under an argon atmosphere -
- the cured thermoset pellet (0.525 g) from Example 36 was placed in a 3" tube furnace, heated at 2°C/min under a flow (100 cc/min) of argon to 1500°C, and held at 1500°C for 2 hr yielding a solid dense ceramic with weight retention of 99.5%.
- the solid ceramic was removed from the furnace, characterized by XRD, and found to form nanoparticle sized pure WB and a small amount of nanoparticle sized WC in an excess of carbon as the matrix. All of the tungsten had reacted.
- the WB-WC carbon solid composition was formed in one step and exhibited structural integrity, hardness, and toughness.
- TPEB prepolymer (0.070 g; 0.146 mmol) from Example 29, boron (0.252 g, 23.3 mmol), and hafnium hydride (2.00 g; 11.1 mmol) were ball milled for 5 minutes resulting in a deep red-black fine powder. The powder was placed in a 13 mm pellet press and pressed at 10,000 pounds for 10 sec.
- Example 40 20°C/min under an argon atmosphere to 210°C, and held at this temperature for 10 hr (overnight) resulting in the formation of a tough shaped polymeric solid.
- the hafnium hydride and boron powders were homogeneous dispersed in the solid thermoset.
- TPEB prepolymer (0.050 g; 0.105 mmol) from Example 29, boron (0.116 g, 10.7 mmol), and zirconium hydride (0.500 g; 5.36 mmol) were ball milled for 5 minutes resulting in a deep red- black fine powder. The powder was placed in a 13 mm pellet press and pressed at 8,000 pounds for 10 sec.
- refractory ZrB 2 solid ceramic in one step by heating at 2°C/min to 1400°C under an argon atmosphere -
- the cured thermoset pellet (0.625 g) from Example 42 was placed in a 3" tube furnace, heated at 2°C/min under a flow (100 cc/min) of argon to 1400°C, and held at 1400°C for 2 hr yielding a solid dense ceramic with weight retention of 98.5%.
- the solid ceramic was removed from the furnace, characterized by XRD, and found to form nanoparticle sized pure ZrB 2 and a smaller amount of nanoparticle sized ZrC in an excess of carbon as the matrix.
- the ZrB 2 -ZrC carbon solid composition was formed in one step and exhibited structural integrity, hardness, and toughness.
- thermoset - Conversion of precursor composition of TiH 2 , boron, and TPEB prepolymer containing chopped fibers to thermoset -
- the 21 ⁇ 2" pellet from Example 44 was placed in a furnace, heated at 20°C/min under an argon atmosphere to 210°C, and held at this temperature for 10 hr (overnight) resulting in the formation of a tough shaped polymeric carbon fiber reinforced thermoset solid.
- the titanium hydride and boron powders were homogeneous dispersed in the solid thermoset-carbon fiber composite.
- the carbon fiber-containing shaped polymeric thermoset pellet (15.7 g) from Example 45 was placed in a 3" tube furnace and heated at 2°C/min under a flow (100 cc/min) of argon to 1400°C yielding a solid dense carbon fiber reinforced ceramic with weight retention of 97.2%.
- the solid carbon fiber reinforced ceramic was removed from the furnace, characterized by XRD, and found to form nanoparticle sized TiB 2 and nanoparticle sized TiC in the carbon-carbon fiber composite.
- the TiB 2 -TiC carbon-carbon fiber solid composition exhibited great structural integrity with the inclusion of the fiber reinforcement.
- thermoset - Conversion of precursor composition of TiH 2 , boron, and TPEB prepolymer containing chopped fibers to thermoset -
- the 21 ⁇ 2" pellet from Example 47 was placed in a furnace, heated at 20°C/min under an argon atmosphere to 210°C, and held at this temperature for 10 hr (overnight) resulting in the formation of a tough shaped carbon fiber reinforced polymeric solid.
- the zirconium hydride and boron powders were homogeneous dispersed in the solid thermoset-carbon fiber composite.
- the carbon fiber-containing shaped polymeric thermoset pellet (12.5 g) from Example 48 was placed in a 3" tube furnace and heated at 2°C/min under a flow (100 cc/min) of argon to 1500°C yielding a solid dense carbon fiber reinforced ceramic with weight retention of 97.5%.
- the solid carbon fiber reinforced ceramic was removed from the furnace, characterized by XRD, and found to form nanoparticle sized ZrB 2 and nanoparticle sized ZrC in the carbon-carbon fiber composite.
- the ZrB 2 -ZrC carbon-carbon fiber solid composition exhibited great structural integrity with the inclusion of the fiber reinforcement.
- a ZrH 2 -boron pellet (133.187 mg) prepared as in Example 50 was placed a TGA chamber and heated at 5°C/min to 250°C followed by heating at 3°C/min to 1300°C and holding at 1300°C for 3 hr under a flow of argon at 100 cc/min affording solid ceramic material (pure ZrB 2 ) with a weight retention of 97.77%.
- Example 29 Formulation of precursor composition of TiH 2 , boron, and TPEB prepolymer and formation of shaped pellet - TPEB prepolymer form
- Example 29 (0.129 g; 0.270 mmol), boron (0.455 g, 42.1 mmol), and TiH 2 (1.00 g; 42.1 mmol) were ball milled for 1 minute resulting in a deep red-black fine powder. The powder was placed in a 6 mm pellet press and pressed to 4,000 pounds for 1 sec.
- the pellet (198.992 mg) prepared in Example 52 was placed in a TGA chamber and heated under a 100 cc/min flow of nitrogen at 5°C/min to 250°C and held at 250°C for 1 hr to consolidate to a shaped solid thermoset polymer.
- the isothermal heat treatment at 250°C resulted in the reaction of the ethynyl units in the TPEB and conversion to the shaped thermoset polymer.
- the solid polymeric sample composed of TiH 2 and boron embedded in the polymeric thermoset was then slowly heated at 3°C/min to 1300°C and held at 1300°C for 3 hr affording a solid ceramic material, which had taken on about 12% wt relative to the initial weight. Above 400°C, degradation of the TiH 2 occurred to Ti nanoparticles and H 2 ; the H 2 vaporized from the sample. Further heating above 500°C to 1300°C resulted in the reaction of the highly reactive Ti nanoparticles with the boron, with nitrogen, and with the developing carbon atoms being formed from the carbonization of TPEB during the heat treatment.
- the solid ceramic Upon cooling, the solid ceramic was removed from the furnace, characterized by XRD, and found to contain a large amount of TiN nanoparticles along with smaller portions of TiB 2 and TiC nanoparticles embedded in the excess carbon formed during the simple carbonization process.
- the TiB 2 -TiN-TiC carbon solid composition was formed in one step and exhibited great structural integrity, hardness, and toughness.
- TPEB prepolymer (0.050 g; 0.105 mmol), boron (0.116 g, 10.7 mmol), and zirconium hydride (0.500 g; 5.36 mmol) were ball milled for 1 minute resulting in a deep red-black fine powder. The powder was placed in a 6 mm pellet press and pressed to 4,000 pounds for 10 sec.
- the ZrB 2 -ZrN-ZrC carbon solid composition was formed in one step and exhibited great structural integrity, hardness, and toughness.
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Abstract
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US201261693930P | 2012-08-28 | 2012-08-28 | |
US13/749,794 US8822023B2 (en) | 2012-01-26 | 2013-01-25 | Refractory metal ceramics and methods of making thereof |
US13/768,219 US8865301B2 (en) | 2012-01-26 | 2013-02-15 | Refractory metal boride ceramics and methods of making thereof |
PCT/US2013/037559 WO2013191804A2 (en) | 2012-05-01 | 2013-04-22 | Refractory metal boride ceramics and methods of making thereof |
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NO822739L (en) * | 1981-08-31 | 1983-03-01 | Battelle Memorial Institute | SINTERIZATION COMPOSITION ON TITANBORIDE BASIS AND ITS USE FOR PREPARING SINTERED GOODS |
US4512946A (en) * | 1983-09-06 | 1985-04-23 | General Electric Company | Microcomposite of metal boride and ceramic particles |
US4582553A (en) * | 1984-02-03 | 1986-04-15 | Commonwealth Aluminum Corporation | Process for manufacture of refractory hard metal containing plates for aluminum cell cathodes |
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US4937101A (en) * | 1988-11-07 | 1990-06-26 | Rohr Industries, Inc. | Prereacted inhibitor powder for carbon-carbon composites |
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US5320717A (en) * | 1993-03-09 | 1994-06-14 | Moltech Invent S.A. | Bonding of bodies of refractory hard materials to carbonaceous supports |
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