THERMOSET CERAMIC COMPOSITIONS, INORGANIC POLYMER COATINGS, INORGANIC POLYMER MOLD TOOLING, INORGANIC POLYMER HYDRAULIC FRACKING PROPPANTS, METHODS OF PREPARATION AND APPLICATIONS THEREFORE

Abstract

Thermoset ceramic compositions and a method of preparation of such compositions. The compositions are advanced organic/inorganic hybrid composite polymer ceramic alloys. The material combines strength, hardness and high temperature performance of technical ceramics with the strength, ductility, thermal shock resistance, density, and easy processing of the polymer. Consisting of a branched backbone of silicon, alumina, and carbon, the material undergoes sintering at 7 to 300 centigrade for 2 to 94 hours from water at a pH between 0 to 14, humidity of 0 to 100%, with or without vaporous solvents.

Claims

1.-19. (canceled)

20. A method of manufacturing a solid substrate having a protective coating on the surface thereof, said method comprising: I. providing a first blend of components for forming an organic/inorganic hybrid composite polymer ceramic coating selected from the group consisting of a. dry blends, and b. slurry blends, and; II. providing a second solution blend of components for forming an organic/inorganic hybrid composite polymer ceramic coating; III. blending the blend of I and the blend of II to form a second slurry; IV. coating a predetermined solid substrate with the blend from the second slurry formed in III; V. placing the coated solid substrate from IV. into a chamber to prevent humidity loss; VI. curing the coated solid substrate at a temperature higher than 25 C. for a predetermined period of time to obtain a solid substrate having a coating on the surface.

21. A coating prepared by the method of claim 20.

22. A solid coated substrate when manufactured by the method of claim 20.

23. The coating as claimed in claim 21 wherein the coating has a resistance to acids of pH of 1 to less than 7 with a weight loss of less than twenty percent.

24. The coating as claimed in claim 23 wherein the coating has a resistance to acids selected from the group consisting of sulfuric, hydrochloric, nitric, hydrofluoric, salicylic, formic, acetic, and phosphoric.

25. The coating as claimed in claim 21 wherein the coating has a resistance to bases of pH greater than 7 to 14 with a weight loss of less than one percent.

26. The coating as claimed in claim 25 wherein the coating has a resistance to bases selected from the group consisting of NaOH, KOH, LiOH, and ammonia.

27. The coating as claimed in claim 21 wherein the coating has a resistance to organic solvents with a weight loss of less than one percent.

28. The coating as claimed in claim 27 wherein the organic solvents are selected from the group consisting of methanol, isopropanol, ethanol, ethyl acetate, xylene, methyl ethyl ketone, tetrahydrofuran, dimethylsulfoxide, hydrocarbons, terpenes, mineral oil, acetone and, cellosolve.

29. The coating as claimed in claim 27 that has a thermal resistance up to 400 F.

30. The coating as claimed in claim 21 having a dynamic coefficient of friction of less than 0.3 against steel.

31. The coating as claimed in claim 21 having a static coefficient of friction of less than 0.4 against steel.

32. The coating as claimed in claim 21 having a surface emissivity of less than 0.6.

33. The coating as claimed in claim 21 having a thermal conductivity of less than 1 W/m.sup.2sec.

34. The coating as claimed in claim 21 in which the thermal flux of the coated substrate is less than 50%.

35. The coating as claimed in claim 21 having an electrical resistance of less than 1 ohm.

36. The coating as claimed in claim 21 having an elongation to break greater than 2%.

37.-42. (canceled)

43. In combination, a coating as claimed in claim 21 and an exhaust system wherein the coating is a thermal barrier.

44. The combination as claimed in claim 43 wherein the exhaust system contains a catalytic converter.

45. In combination, a coating as claimed in claim 21, and foam substrates, wherein the foam is coated with said coating.

46. (canceled)

47. A coating as claimed in claim 21 wherein the coating has a thickness in the range of 1 micron to 5 mm.

48. In combination, a coating as claimed in claim 21 an automotive interior engine components, wherein the automobile interior engine components are coated with said coating.

49. The combination as claimed in claim 48 wherein the automotive interior engine component is selected from the group consisting of: pistons, heads, valves, cylinder liners, intake headers, exhaust headers, turbo chargers, turbo compressors, and jet engine turbines.

50. A coating as claimed in claim 21 having high pass or low pass thermal properties having control of thermal conductivity and emissivity in opposition to each other.

51. A well bore liner prepared from the coating as claimed in claim 21.

52. The coating as claimed in claim 21 that is filled with low emissivity filler.

53. The coating as claimed in claim 21 that is filled with low thermal conductivity filler.

54. The coating as claimed in claim 21 that is filled with high thermal conductivity filler.

55. The coating as claimed in claim 21 that is filled with one or more colorants.

56. The coating as claimed in claim 21 that is filled with texturizing agents.

57. The coating as claimed in claim 21 that is filled with fiber fillers.

58. The coating as claimed in claim 21 that is filled with low thermal conductivity filler.

59. The coating as claimed in claim 21 having a porous, oil wetting surface.

60. The coating as claimed in claim 59 having a porosity of 0.05 to 0.9.

61. The coating as claimed in claim 59 having a porosity of less than 7%.

62. The coating as claimed in claim 59 having a porosity greater than 15%.

63. The coating as claimed in claim 21 having open or closed cell foam characteristics.

64. The coating as claimed in claim 21 that self-segregates into a dense region at the surface and porous region in the center.

65. The coating as claimed in claim 21 which is a two part system containing compositions A and B which undergoes a two-step reaction process, wherein part A is mixed metal oxides, selected from alumina oxide, silicon oxide, magnesium oxide, lithium oxide, calcium oxide, metals other metal oxides and carbon; wherein part B is a caustic slurry composed of highly alkaline water and solvent selected from the group consisting of a. methanol, b. ethanol, c. a combination of methanol and ethanol, d. other solvents, e. reactive amorphous carbon, and, f. chloride salts.

66.-121. (canceled)

Description

DETAILED DISCUSSION OF THE INVENTION

[0059] The present invention is unique from existing prior art in both its fundamental composition of matter, and perhaps more notably, its mechanism of synthesis. The reaction pathway by which the material is obtained proceeds through first, the dissolution of the amorphous silicon, alumina, carbon, and alkali metal, in an alkaline solution co-solvated with one or more polar aprotic or protic solvents.

[0060] The resulting solution/slurry rapidly has a viscosity between 1000 and 700,000 centipoise. This solution hardens into a gel-state as a result of silanol condensation complimented by cationic stabilization of the free labile anionic network forming elements (Al, Si, O, C). The physical properties of this gel state, and the states immediately preceding it, are largely a function of the concentration of divalent cations: monovalent cations: to network forming elements (Al, Si, O, C).

[0061] This gel is stable for a time period of several minutes to several months, after which it will undergo dehydration-mediated shrinkage and cracking. The gel state can then be subjected to curing at elevated temperatures and humidity, consisting of various pH water and solvents, at various pressures. During this curing, the reactivity of the system increases as solvolysis of the gel system recuperates alkalinity of the system, re-dissolving the silanol condensation product to a greater or lesser extent, and mediating a complete amorphous structure formation of the network forming elements (Al, Si, O, C).

[0062] The added heat of the system overcomes the endothermic barrier preventing the network forming reactions from taking place previously. Al and Si are bound via bridging oxygen generated via hydrolysis, which consumes alkalinity of the gel, and CSi, SiCSi and potentially metastable AlC, bonds are formed. The fundamental monomer of the reaction may be any variation of O, Al, C, and Si, e.g. AlOSiCSiOAlO. More mono-cationic species will lead to a more polymeric and generally weaker structure, whereas divalent cationic species, preferably Li serve to create an even greater degree of crosslinking. Ca++ and Mg++ are less preferable due to their tendencies to rapidly form hydrates which often do not re-dissolve in the second phase of the reaction.

[0063] This material differs from geopolymers, in that, geopolymers consist of AlOSi networks and are generated via a one-step solvent-free method, and produce materials of vastly inferior strength. There is no carbon in the geopolymer matrix.

[0064] Geopolymers have been mixed with latex, acrylates, and ethylene vinyl acetate (hydrophilic hydrocarbon polymers). However, in these situations these polymers interface with the geopolymer only though a bridging O group via reduction of one of the polymer free hydroxyl or other electronegative reactive groups. There is no continuous integration of carbon into the geopolymer matrix itself, and the hydrocarbon polymer very much retains its molecular identity throughout the reaction and serves mainly as a stabilizer of what is a relatively flawed silyl-silanol condensation polymer.

[0065] Some geopolymers have been developed with unique porosity such that hydrocarbon containing or comprised molecules can be retained within them, thereby turning the geopolymer into a drug delivery mechanism. However, these compounds have no structural bonding to the geopolymer matrices, and thus are even farther from the presently disclosed invention than the geopolymer-glue materials previously mentioned. The case of geopolymers used in oilfields is similar in the ab/adsorption of carbon containing compounds onto/into the (porous) geopolymer in a fashion proportional to the surface area of the geopolymer particle.

[0066] Calcium Carbonate stabilized Aluminosilicates are significantly different from the present invention due their lack of a covalent CSi bond formed in-reaction, if in fact they are in fact formed at all rather than simply being mined.

[0067] The instant invention differs from the prior art. The instant invention has a composition including Si, Al, C, O end-capped with a divalent cation such as Mg which is not found in the prior art literature. The instant invention is a two-step process of forming a hydrogel followed by recombination oxygen crosslinking, all of which is not found in the prior art literature.

[0068] The present invention is unique from existing prior art in both its fundamental composition of matter, and perhaps more notable, its mechanism of synthesis. While not bound by any particular theory, the reaction pathway by which the disclosed material is obtained proceeds through (1.) the dissolution of the amorphous silicon, alumina, carbon, and alkali metal, for example, LiOH, NaOH, or KOH, in an alkaline solution co-solvated with one or more polar aprotic or protic solvents. The resulting solution/slurry rapidly has a viscosity between 500 and 700,000 centipoise. (2.) This solution hardens into a gel-state as a result of silanol condensation complimented by cationic stabilization of the free labile anionic network forming elements (Al, Si, O, C).

[0069] The physical properties of this gel state, and the states immediately preceding it, are largely a function of the relative concentration of divalent cations: monovalent cations to network forming elements (Al, Si, O, C). This gel is stable from between several minutes to several months, after which, if allowed to dry, will (3.) undergo dehydration-mediated shrinkage and cracking. The gel state is then (4.) subjected to curing at elevated temperatures and humidity, consisting of various pH water and solvents, at various pressures.

[0070] During this curing, the reactivity of the system increases as solvolysis of the gel system recuperates alkalinity of the system, re-dissolving the silanol condensation product to a greater or lesser extent, and mediating a complete amorphous structure formation of the network forming elements Al, Si, O, and C.

[0071] The added heat of the system overcomes the endothermic barrier preventing the network forming reactions from taking place previously. Al and Si are bound via bridging oxygen generated via hydrolysis, which consumes alkalinity of the gel, and CSi, SiCSi and potentially metastable AlC, bonds are formed. The fundamental monomer of the reaction may be any variation of O, Al, C, and Si, e.g. AlOSiCSiOAlO. More mono-cationic species will lead to a more polymeric and generally weaker structure, whereas divalent cationic species, preferably Li, serve to create an even greater degree of crosslinking. The cations, Ca++ and Mg++ are less preferable due to their tendencies to rapidly form hydrates which often do not re-dissolve in the second phase of the reaction.

[0072] The inventors herein have discovered a method to produce a new class of inorganic polymer ceramic-like materials useful in coatings, and methods to apply them. The polymers and their methods of preparation can be found in U.S. patent application Ser. No. 13/832,328, filed Mar. 15, 2013. The coatings are useful as a corrosion resistant coating, low friction coating, electrically insulating, low heat transfer coating or aesthetic coating. The coating may be applied as a spray, electro spray, dip, brush, rolled on, flow coated or reacted in place. The coating is especially useful as a pipe coating both interior and exterior.

[0073] The inventors herein have developed a family of advanced organic/inorganic hybrid composite polymer ceramics to replace high performance coatings. These polymer materials can be euphonically described as a thermoset ceramics. The material combines strength, hardness and high temperature performance of technical ceramics with the strength, ductility, thermal shock resistance, density, and easy processing of a polymer. The unique chemical structure of the polymer materials provides enhanced strength properties and decreased density with tailored physical, electromagnetic, and thermoconductive properties.

[0074] The inventors herein have discovered a class of materials and methods to coat parts to form controlled porosity, thermal conduction, emissivity, surface hardness, flexibility, toughness, elongation, electrical conduction, density, and electromagnetic properties. Due to the highly tailorable nature of the materials' properties, its compatibility with functional additives, ease of fabrication, and high strength-to-weight ratio, there are many applications to which it can be applied. HCPC formulations can be customized to provide system components that are not only application-tailored in their shape, but in their physiochemical properties as well. In addition to the versatility in terms of manufacturing parts and components from the material itself, the material also has several applications for use in the coating industry.

[0075] The chemical inertness and temperature resistance of the material to 3400 F. allows it to be used to coat both nonferrous and ferrous metals and metal alloys. Due to its high dimensional stability at high temperatures, and low reactivity, the material could allow a disruptive innovation in allowing steel to be made non-corroding, low friction, low electrical and heat conducting. The tailorable thermal conductivity of the material is of especially great interest.

[0076] The polymer material is processed as a reactive two-part material, similar to epoxy, during the fabrication process. The material as mixed can have a viscosity from 500 to 75,000 cPS. The lower viscosity is better for spraying thin films, while the higher viscosity is suitable as a rolled out thin sheet and applied directly. The spray techniques may include air spraying, airless spraying, electro spraying, rotary cone spraying, ultrasonic spraying, and the like.

[0077] The initial reaction is the formation of a semi-solid gel state. The final cure reaction occurs when the gel state part is exposed to temperatures of 160-250 F. for 2-6 hours. Longer curing times yield stronger materials. This cures the polymer to an advanced ceramic-like state. Shrinkage is in the range of less than 0.01%, allowing very fine tolerances. A molecularly-smooth surface allows for low cost high performance, rapid, complex parts manufactured with excellent surface texture. The texture may be smooth and high gloss or may be made with a matt finish as desired. The advanced hybrid is a suitable alternative for critical and strategic coatings.

[0078] The materials have several readily apparent dimensions of appeal. Its composition can be composed of available refined feedstocks and can optionally include various quantities of USA-sourced technical grade postindustrial waste stream materials, offsetting both bulk material costs and decreasing environmental impact of formulations.

[0079] The materials contain no heavy metals, thus mitigating personnel safety risk.

[0080] The materials have multiple end use applications such as, coatings, varnish, veneer, polish, stain, colorant, heat/radiation shields, coatings and sprays; Reflective and ablative; Insulators, Conductors, semiconductors; thermal cycling modules, abrasion resistant wear components; heat radiation substrate; heat/abrasive/caustic/acidic material resistant pipes and linings; thermal and electric insulators; covers; heat shields; can coatings; tank linings; and pipe coatings and linings.

[0081] With regard to the use of the compositions herein as proppants, the inorganic polymers of this invention have demonstrated physical strength properties similar to those of the most widely used ceramic proppants, but with a density of 1.7 g/cc. Using existing pelletizing technologies, spheres with a significantly smoother surface versus today's ceramic proppants can be manufactured in large volumes. The density of the proppant can be reduced by either foaming the polymer or by filling with low density materials. Any desired density, including to 1.0, may be obtained by foaming or filling the polymer to match the fracking fluid density needs.

[0082] In the slickwater fracturing processes adopted by today's industry, it is believed that the combination of lower density and smoother surface will create a proppant that can be transported with greater efficiency and control versus todays ceramics. The result is a proppant of significantly higher value due to the increased conductivity that enables greater production from a given well.

[0083] Raw materials for inorganic polymer proppants are available local to major fields in the form of industrial waste streams and by-products, clays, mineral or metal oxide deposits.

[0084] Possible groundwater contamination has been identified and/or reported in communities proximate to water tables with fracking-compromised aquatard formations. Due to the unique chemical composition and controlled porosity achievable by the inorganic polymer material, there is the potential to engineer inorganic polymer proppants so that they are able to absorb at least some of the reactive aromatic hydrocarbons, which could otherwise leak through fracking-disrupted aquatards.

[0085] Ceramic proppants exhibit brittle failure when crushed shattering resulting in a large fraction of fines. Inorganic polymers can be designed to include significant flexibility. There are several ways to increase flexibility of the inorganic polymer proppant. Plasticizers, reduced polymer branching, inclusion of fibers all significantly increase the flexibility of the inorganic polymer.

[0086] The resulting proppants can deform to resist fracture. Also, when fracture does occur, they break into large pieces with few, if any, fines. Conductivity of the formation is maintained and not blinded by the fines. Adding of fibers to ceramic proppants is known (Schlumberger).

[0087] Polymers can be formed by any known granulation processes. Nominally spherical proppants are desired; however, different shapes have value for specific applications. Elliptical proppants have been shown to increase conductivity in a given formation (Baker Hughes). Cylindrical proppants are desired as proppant pillars for high compression resistance (Halliburton). The curing conditions of less than 200 F. is very low energy compared to traditional ceramic proppants.

EXAMPLES

[0088] The carbon compound(s), solvents, and alkaline solutions, with waterglass, are blended under agitator-level mixing conditions until a uniform solution is achieved. The dissolution of the carbon at room temperature is negligible, and as such the solution will be pitch black and gently roiling due to evaporative convection. As such, a lid should be placed on the vessel. As this stage, oligomerizing metallorganic materials may be added in trace quantities. These compounds, such as vinytrimethoxysilane serve to seed oligomeric structures which produce materials with differing strength, thermal, conductivity, and other properties. The solution may be heated in a pressure-sealed vessel to ensure dissolution of the materials. Upon cooling, remaining pressure may be released and excess solvent may need to be added. This breaching step is of importance to mention only since certain metallorganics evolve gasses in the presence of alkaline water. Organic polymer precursors, such as phenol and furan containing compounds, can be added at this step. The solution is best kept at cool temperatures.

[0089] The metal salt powder blend is prepared through the addition of Alumina as amorphous Al.sub.2O.sub.3 anhydrous, amorphous alkali silicoaluminate source such as low-calcined Kaolin clay or Spogumene, amorphous SiO.sub.2 in the form of glass flour or fumed silica. It is also advantageous to add powdered LiOH or KOH to this powder mix to compensate for any neutralization of the solution previously disclosed through absorption of CO.sub.2 into the solution. Once all powders have been combined, they must be put through a blending and de-agglomeration step, due to the anhydrous material's tendency to clump together. Once de-agglomerated and thoroughly blended, it should be sealed such that no moisture can access it.

[0090] Alternatively, recycled waste stream material may be added: aluminosilicate sources such coal combustion products (e.g. Fly Ash) or metal refining by products (ground blast furnace slag, silica fume), rice husk ash, municipal sludge ash, etc. In this case, the relative cationic concentrations must be carefully monitored and calculated and balanced. Alternatively, the Al.sub.2O.sub.3 can be introduced to the liquid material.

[0091] According to these examples, approximately 90-95 grams of liquid is combined with 170-190 grams of the reactive powder mixture. The powder must be added to the liquid gradually or under very high shear to ensure forced reaction constituent proximity necessary to engage the first step of the reaction. If this directive is not followed, insufficient wetting-out of the powder will occur, and the reaction will be ruined. If the mixing is occurring in a sealed kettle, the liquid component may be heated up to 60 degrees centigrade to aid in rapid dissolution and therefor hasten system throughput. Powdered caustic potash or LiOH will be of benefit as they will dissolve into the mixture as the hydrolysis of the amorphous reactive constituents consume the alkalinity of the system, maintaining a critical level of free C, Si, and Al ions.

[0092] This solution should be cooled and then undergo ultrahigh shear mixing, such as a rotostator pump or mixer, to ensure all reactive species have reacted. The more homogenous the solution/nanoslurry, and the less metallorganic oligomerizing agents present, the more amorphous the structure eventually formed will be. It is suggested that this step be cooled due to the excessive heat often generated by high shear systems. If a high shear mixer is lacking, a twin auger mortar mixer could suffice, though the mixing vessel ought to be bathed in an ice bath.

[0093] Following high shear mixing, the solution/nanoslurry can have fibers and or other bulking and or functional additives placed into it. Due to the preference of the material for amorphous structures, glass fibers and carbon fibers may be added and expectedly produce a much stronger material than neat. Steel fibers are also an excellent choice due to their potential to be oxidized and form strong oxygen bridges with Al and Si, and rarely, oxycarbide groups. Alternatively, the slurry may be used to wet out a continuous fiber matrix. Any particulates added must be pre-wetted with an alkaline solution or they will destroy the viscosity of the material. Viscosity of the neat material can be altered through increasing the concentration of divalent cations over any monovalent cations present; the former form ionic stabilized gel that can reach the consistency of clay if so desired (e.g. extrusion). The recipes provided have roughly the consistency of cake batter and may be injection cast or molded with ease. It manifests thixotropic behavior such that in-line vibration-aided de-airing would remove bubbles left in the matrix.

[0094] The material will take between 5 and 20 minutes to reach a demoldable state if left at the presumptively cooled state it was injected in. If the mold is heated, the demolding time can be decreased by a scale of magnitude, but care must be taken to ensure that proper solvent-moisture level is maintained in the matrix. This is not a difficult task, as the nano-porous nature of these particular mixtures makes them resilient to dry out.

[0095] Once demolded, the gel-state material is stable for 3 hours at room temperature at 20% humidity and 72 F. If refrigerated at 40 degrees, placed inside a non-porous/reactive plastic bag with water between pH 8 and 9, the gel state is stable for several days. At any point during this time, the material can be milled, tooled, etc. If the mixture is sufficiently de-aired, there will be minimal, though potentially noticeable under microscopic scrutiny, differences between the cast and the milled surfaces. This is largely determined by the tool used to mill the material.

[0096] The provided formulations are such that they are to be cured at saturated humidity between pH 2 and 10, 165 F., for 6 hours at least, preferably 6 hours or more. Following that, the material should be allowed time to breathe for as long as possible before being put under maximum stress loads. This allows the remaining reaction solution to crystalize within the pores, creating a silicaceous polished surface appearance on the surface of the material. Depending on the solvent used and the level of dissolution of carbon compounds, this layer may or may not have different conductive properties than the primary matrices. Should the material be destined for metal casting applications, desiccation of the material would be advantageous to prevent the production of supercritical steam when the molten metal hits an improperly breathed patch of the material.

[0097] It is noteworthy that the material does not seem to ever stop gaining strength, though the rate of strength gain does seem attenuate at a logarithmic rate. Nonetheless, several month-old samples are significantly stronger than their younger counterparts. Materials of unprecedented strength could likely be obtained through curing regimes of several months.

[0098] First table below is example 1 and second table below is example 2.

TABLE-US-00002 Carmen 1 Pure Feedstock When de-aired a bit, this is one that hit the demonstrated strength area MW g/mol 60 102 159.7 80 56 62 $/kg amt (g) SiO2 Al2O3 Fe2O3 SO3 CaO Na2O Ericson Coal Ash $0.030 38.8% 20.1% 6.3% 1.2% 22.0% 2.3% mass contribution 0 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0.000 0.00 0.00 Recyc Amorphous C $0.800 10.0 0% 0.00% 0.0% 0.02% 0.0% 0% mass contribution 0 0 0 0.002 0 0 molar contribution 0 0 0 0.000025 0 0 Monroe Coal Ash $0.030 .sup.42% .sup.22% .sup.8% .sup.1% 16% 1% mass contribution 0 0 0 0 0 0 molar contribution 0 0 0 0 0 0 China Twp. Ash $0.030 37.90% 19.8% 5.9% 2.60% 16.30% 7.75% mass contribution 0 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0.00 0.00 0.00 Steek Slag $0.088 35.83% 10.8% 0.5% 3.06% 40.43% 0.25% mass contribution 0 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0.00 0.00 0.00 LF Steel Slag $0.088 10.0 35.83% 10.8% 0.5% 3.06% 40.43% 0.25% mass contribution 3.583 1.075 0.05 0.306 4.043 0.025 molar contribution 0.06 0.01 0.00 0.00 0.07 0.00 Clay Ash $0.600 50.0 .sup.53% .sup.45% .sup.0% 0.1% 0.1% 0.1% mass contribution 26.4 22.3 0.2 0.05 0.05 0.05 molar contribution 0.44 0.2186 0.0013 0.0006 0.0009 0.0008 Alumina (anhydrous) $0.540 20.0 0.5% 99.8% 0.5% 0.5% 0.5% 0.5% mass contribution 0.1 20.0 0.1 0.1 0.1 0.1 molar contribution 0.0 0.2 0.0 0.0 0.0 0.0 Fume $0.240 80.0 99.8% 0% .sup.0% .sup.0% .sup.0% 0% mass contribution 79.8 0.0 0.0 0.0 0.0 0.0 molar contribution 1.3 0.0 0.0 0.0 0.0 0.0 G solid NaSiO2 $1.736 61.8% 0% .sup.0% .sup.0% .sup.0% 19.1% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 0.0 PQ SOLID LithSil 25 $4.400 19.5% 0% .sup.0% 0.0% 0.0% 0.0% mass contribution 0 0 0 0 0 0 molar contribution 0.00 0.00 0.0 0.00 0.00 0.00 LiOH monohydrate $5.540 10.0 0.0% 0% .sup.0% .sup.0% .sup.0% 1% mass contribution 0.0 0.0 0.0 0.0 0.0 0.1 molar contribution 0.0 0.00 0.0 0.00 0.00 50% NaOH solution $0.500 0.0% 0.0% 0.0% 0.0% 0.0% 38.8% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 0.0 48% KOH solution $0.640 47.0 0.0% 0.0% 0.0% 0.0% 0.0% 0.0% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.00 0.00 0.00 PQ KSIL6 soln $1.660 26.6% 0% .sup.0% .sup.0% .sup.0% 0% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.00 0.0 0.00 0.00 0.00 PQ NaSil D soln $0.592 29.8% 0% .sup.0% .sup.0% .sup.0% 14.7% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.00 0.0 0.00 0.00 0.00 PQ NaSil STAR soln $0.544 32.0 26.51% 0.0% 0.0% 0.00% 0.00% 10.58% mass contribution 8.4832 0 0 0 0 3.3856 molar contribution 0.1 0.00 0.0 0.00 0.00 0.05 PQ NaSil M soln $0.552 32.0% 0.0% 0.0% 0.0% 0.0% 12.3% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.00 0.0 0.00 0.00 0.00 PQ D soln $0.592 29.8% 0.0% 0.0% 0.0% 0.0% 14.9% MW g/mol 29.8 40.3 94 18 16.04 % solids Li2O MgO K2O H2O CH4 % ret. on 325 Ericson Coal Ash .sup.0% .sup.0% 0% 0.1% 0.0% 6.75 mass contribution 0 0 0 0 0 molar contribution 0 0 0 0.000 0.000 Recyc Amorphous C .sup.0% .sup.0% 0% 0.1% 99.0% 10.37 mass contribution 0 0 0 0.01 9.9 molar contribution 0 0 0 0.0005556 0.617207 Monroe Coal Ash 0.0% .sup.0% 0% 0% .sup.0% 15.66 mass contribution 0 0 0 0 0 molar contribution 0 0 0 0 0 China Twp. Ash 0.0% 4.0% 0.98% 0.10% 0.00% mass contribution 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0.00 0.00 Steek Slag 0.0% 10.5% 0.36% 1.75% 0.00% mass contribution 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0.00 0.00 LF Steel Slag 0.0% 10.5% 0.36% 1.75% 0.00% mass contribution 0 1.051 0.036 0.175 0 molar contribution 0.00 0.03 0.00 0.01 0.00 Clay Ash 0.0% 0.1% 1% 1% .sup.0% mass contribution 0 0.05 0.5 0.5 0 molar contribution 0.0000 0.0012 0.0053 0.0278 0 Alumina (anhydrous) 0.0% 0.5% 0.5%.sup. 0.5% 0.0% mass contribution 0.0 0.1 0.1 0.1 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 Fume 0.0% .sup.0% 0% 0% .sup.0% mass contribution 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 G solid NaSiO2 0.0% .sup.0% 0% 18.5% 0.0% 80.9% mass contribution 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 PQ SOLID LithSil 25 2.3% 0.0% 0% 0% .sup.0% mass contribution 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0 0 LiOH monohydrate 65.0% .sup.1% 0.5%.sup. 32.0% 0.0% mass contribution 6.5 0.1 0.1 3.2 0.0 molar contribution 0.22 0.00 0.00 0.1777778 0 50% NaOH solution 0.0% 0.0% 0.0%.sup. 61.2% 0.0% 38.80% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 48% KOH solution 0.0% 0.0% 37.2% 62.8% 0.0% 37.24% mass contribution 0.0 0.0 17.5 29.5 0.0 17.5 molar contribution 0.00 0.00 0.19 1.6387333 0 PQ KSIL6 soln 0.0% .sup.0% 12.7% 60.7% 0.0% 39.30% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.00 0.00 0.00 0 0 PQ NaSil D soln 0.0% .sup.0% 0% 55.5% 0.0% 44.54% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.00 0.00 0.00 0 0 PQ NaSil STAR soln 0.0% 0.0% 0.00% 62.9% 0.0% 37.09% mass contribution 0 0 0 20.1312 0 11.9 molar contribution 0.00 0.00 0.00 1.1184 0 PQ NaSil M soln 0.0% 0.0% 0.0%.sup. 55.6% 0.0% 44.37% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.00 0.00 0.00 0 0 PQ D soln 0.0% 0.0% 0.0%.sup. 55.3% 0.0% 44.69%

TABLE-US-00003 Claus2.Beta.1 When de-aired, this is the somewhere between basic and demonstrated strength mix This is the formulation used to cast 2000f+ molten glass MW g/mol 60 102 159.7 80 56 62 66-86% Recycled Content $/kg amt (g) SiO2 Al2O3 Fe2O3 SO3 CaO Na2O Ericson Coal Ash $0.030 15.0 38.8% 20.1% 6.3% 1.2% 22.0% 2.3% mass contribution 5.82 3.015 0.939 0.18 3.3 0.345 molar contribution 0.10 0.03 0.01 0.002 0.06 0.01 Recyc Amorphous C $0.240 15.0 0% 0.00% 0.0% 0.02% 0.0% 0% mass contribution 0 0 0 0.003 0 0 molar contribution 0 0 0 3.75E05 0 0 Monroe Coal Ash $0.030 .sup.42% .sup.22% .sup.8% .sup.1% 16% 1% mass contribution 0 0 0 0 0 0 molar contribution 0 0 0 0 0 0 China Twp. Ash $0.030 100.0 37.90% 19.8% 5.9% 2.60% 16.30% 7.75% mass contribution 37.9 19.8 5.9 2.6 16.3 7.75 molar contribution 0.63 0.19 0.04 0.03 0.29 0.13 Steek Slag $0.088 35.83% 10.8% 0.5% 3.06% 40.43% 0.25% mass contribution 0 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0.00 0.00 0.00 LF Steel Slag $0.088 10.0 35.83% 10.8% 0.5% 3.06% 40.43% 0.25% mass contribution 3.583 1.075 0.05 0.306 4.043 0.025 molar contribution 0.06 0.01 0.00 0.00 0.07 0.00 Clay Ash $0.600 5.0 .sup.53% .sup.45% .sup.0% 0.1% 0.1% 0.1% mass contribution 2.64 2.23 0.02 0.005 0.005 0.005 molar contribution 0.044 0.0219 0.0001 0.0001 0.0001 0.0001 Alumina (anhydrous) $0.340 30.0 0.5% 99.8% 0.5% 0.5% 0.5% 0.5% mass contribution 0.2 29.9 0.2 0.2 0.2 0.2 molar contribution 0.0 0.3 0.0 0.0 0.0 0.0 Fume $0.160 2.0 99.8% 0% .sup.0% .sup.0% .sup.0% 0% mass contribution 2.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 0.0 G solid NaSiO2 $1.736 61.8% 0% .sup.0% .sup.0% .sup.0% 19.1% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 0.0 PQ SOLID LithSil 25 $4.400 19.5% 0% .sup.0% 0.0% 0.0% 0.0% mass contribution 0 0 0 0 0 0 molar contribution 0.00 0.00 0.0 0.00 0.00 0.00 LiOH monohydrate $5.540 10.0 0.0% 0% .sup.0% .sup.0% .sup.0% 1% mass contribution 0.0 0.0 0.0 0.0 0.0 0.1 molar contribution 0.0 0.00 0.0 0.00 0.00 50% NaOH solution $0.500 45.0 0.0% 0.0% 0.0% 0.0% 0.0% 38.8% mass contribution 0.0 0.0 0.0 0.0 0.0 17.5 molar contribution 0.0 0.0 0.0 0.0 0.0 0.3 48% KOH solution $0.640 0.0% 0.0% 0.0% 0.0% 0.0% 0.0% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.00 0.00 0.00 PQ KSIL6 soln $1.660 26.6% 0% .sup.0% .sup.0% .sup.0% 0% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.00 0.0 0.00 0.00 0.00 PQ NaSil D soln $0.592 45.0 29.8% 0% .sup.0% .sup.0% .sup.0% 14.7% mass contribution 13.4 0.0 0.0 0.0 0.0 6.6 molar contribution 0.2 0.00 0.0 0.00 0.00 0.11 PQ NaSil STAR soln $0.544 26.51% 0.0% 0.0% 0.00% 0.00% 10.58% mass contribution 0 0 0 0 0 0 molar contribution 0.0 0.00 0.0 0.00 0.00 0.00 PQ NaSil M soln $0.552 32.0% 0.0% 0.0% 0.0% 0.0% 12.3% mass contribution 0.0 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.00 0.0 0.00 0.00 0.00 MW g/mol 29.8 40.3 94 18 16.04 66-86% Recycled Content Li2O MgO K2O H2O CH4 Ericson Coal Ash .sup.0% .sup.0% 0% 0.1% 0.0% mass contribution 0 0 0 0.015 0 molar contribution 0 0 0 0.001 0.000 Recyc Amorphous C .sup.0% .sup.0% 0% 0.1% 99.0% mass contribution 0 0 0 0.015 14.85 molar contribution 0 0 0 0.0008333 0.9258105 Monroe Coal Ash 0.0% .sup.0% 0% 0% .sup.0% mass contribution 0 0 0 0 0 molar contribution 0 0 0 0 0 China Twp. Ash 0.0% 4.0% 0.98% 0.10% 0.00% mass contribution 0 4 0.98 0.1 0 molar contribution 0.00 0.10 0.01 0.01 0.00 Steek Slag 0.0% 10.5% 0.36% 1.75% 0.00% mass contribution 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0.00 0.00 LF Steel Slag 0.0% 10.5% 0.36% 1.75% 0.00% mass contribution 0 1.051 0.036 0.175 0 molar contribution 0.00 0.03 0.00 0.01 0.00 Clay Ash 0.0% 0.1% 1% 1% .sup.0% mass contribution 0 0.005 0.05 0.05 0 molar contribution 0.0000 0.0001 0.0005 0.0028 0 Alumina (anhydrous) 0.0% 0.5% 0.5%.sup. 0.5% 0.0% mass contribution 0.0 0.2 0.2 0.2 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 Fume 0.0% .sup.0% 0% 0% .sup.0% mass contribution 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 0.0 G solid NaSiO2 0.0% .sup.0% 0% 18.5% 0.0% mass contribution 0.0 0.0 0.0 0.0 0.0 molar contribution 0.0 0.0 0.0 0.0 PQ SOLID LithSil 25 2.3% 0.0% 0% 0% .sup.0% mass contribution 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0 0 LiOH monohydrate 65.0% .sup.1% 0.5%.sup. 32.0% 0.0% mass contribution 6.5 0.1 0.1 3.2 0.0 molar contribution 0.22 0.00 0.00 0.1777778 0 50% NaOH solution 0.0% 0.0% 0.0%.sup. 61.2% 0.0% mass contribution 0.0 0.0 0.0 27.5 0.0 molar contribution 0.0 0.0 0.0 1.5 0.0 48% KOH solution 0.0% 0.0% 37.2% 62.8% 0.0% mass contribution 0.0 0.0 0.0 0.0 0.0 molar contribution 0.00 0.00 0.00 0 0 PQ KSIL6 soln 0.0% .sup.0% 12.7% 60.7% 0.0% mass contribution 0.0 0.0 0.0 0.0 0.0 molar contribution 0.00 0.00 0.00 0 0 PQ NaSil D soln 0.0% .sup.0% 0% 55.5% 0.0% mass contribution 0.0 0.0 0.0 25.0 0.0 molar contribution 0.00 0.00 0.00 1.3865 0 PQ NaSil STAR soln 0.0% 0.0% 0.00% 62.9% 0.0% mass contribution 0 0 0 0 0 molar contribution 0.00 0.00 0.00 0 0 PQ NaSil M soln 0.0% 0.0% 0.0%.sup. 55.6% 0.0% mass contribution 0.0 0.0 0.0 0.0 0.0 molar contribution 0.00 0.00 0.00 0 0

[0099] The composition formed is an amorphous polymer of silicon and aluminum with carbon and oxygen bonds. Raman spectroscopy is one way to measure the amorphous nature and observe the bonds present. Crystalline materials exhibit relatively shape bands and harmonic repetition of bands. The inventive materials are characterized by wide diffuse bands with a lack of harmonics. The silicon oxygen bridge between 1300 and 1400 wave numbers in the instant samples have a full width half height normalized ration from 0.12 to 0.16.

Example 3

[0100] Proppants are materials that are injected into hydraulically fractured oil and gas wells to prop open the fissures that are created during fracturing. Proppants must be transportable through injection media to the fissures, deposit appropriately throughout the fissure, and be strong enough not to crush under pressure from the walls of the fissure. They must also have a spherical geometry that creates a porous bed for the released oil and gas to permeate through the proppant (called conductance) and be collected at the well's surface. Today's proppants are typically sand, coated sand, clay-based ceramics (intermediate grades are the vast portion of the market), or sintered bauxite (high-value proppants).

Examples were made according to the method of example 1 with the starting materials:

TABLE-US-00004 Grams Grams Grams Carbon Grams Grams Part Al (OH) 3 SiO2 Black MgO B (pH 13.4) 33.43 42.78 3.86 1.66 43.3
Part B is a solution of 20 g KOH 112 grams water glass, 20 g amorphous silicon, 12.5 grams methanol, 12.5 grams methylene glycol, and 4 grams formic acid. The Al(OH)3, SiO2, Carbon and MgO were mixed as dry powder, then added with mixing to part B solution. The slurry was allowed to green set for 30 minutes, followed by curing in a 160-degree Fahrenheit oven for 12 hours. The cure step for example 3 being in air at 30% humidity and the cure step for example 4 in air at 100% humidity. Example 3 Raman peak at 1349 wave numbers (cm.sup.1) has a full width half height ratio of 0.12. (See FIG. 1) Example 4 Raman peak at 1323 wave numbers (cm.sup.1) full width half height ratio is 0.16. (See FIG. 2)

Example 4

[0101] Emissivity measurements were made as follows. Three-inch diameter by inch thick cylindrical disks were cast and cured. The disks were painted with known emissivity flat black 0.95 emissivity, reflective metallic 0.30 emissivity and white 0.92. One quarter was left uncoated to measure native emissivity. The disk was heated with a 250 watt heat light 12 inches from the disk for 5 minutes. An NBS calibrated IR thermometer was then used to measure the heat emitted from all four sections. The known emissivity measurements were linearized and used to calculate the emissivity of the native disk.

[0102] Thermal conductivity was measured by first, casting one-inch diameter cylinders two inches long. The cylinders ends were polished. Standard materials of known thermal conductivity were similarly prepared. Standards included Aluminum, 1054 steel, borosilicate glass, graphite, and mullite. Thermocouples were attached to the top center and bottom outside edge of the cylinder. The thermocouples were attached to a data logger. The cylinder was placed on a hot plate set at 150 degrees C. The heating rate and differential from top to bottom of sample was measured. The known materials differential vs conductivity was fitted to an exponential decay and the thermal conductivity of the sample was calculated.

Delta T Watt/mK

[0103] ANSI A137.1, is called the DCOF AcuTest for dynamic coefficient of friction of ceramics. The formula is =f/N, where is the coefficient of friction, f is the amount of force that resists motion, and N is the normal force. Static friction is below 0.30 and dynamic below 0.15.

[0104] Acid, base and solvent resistance was measured by soaking samples of the thermal set ceramic in one-inch cubes in concentrated acid base or solvent for one month then drying and measuring any weight gain or loss.

TABLE-US-00005 Dry blend solid materials part A 40 g calcium alumina silicate 22 g alumina silicate 22 g flyash Mix with solution part B 5 g methanol 14 g sodium hydroxide 0.25 ethylene glycol 2.7 g borax 1.9 g formalin 55.6 g 40% sodium silicate solution

[0105] Mixed part A and B into a well dispersed solution. Slurry was applied as coating on substrates or cast into disks for thermal testing, then placed in enclosure to prevent humidity loss and cured overnight in a 77 C. oven. Measured emissivity 0.42.

Example 5

[0106]

TABLE-US-00006 Dry blend solid materials part A 15 g magnesium oxide 86 g alumina silicate 64 g flyash 18 g aluminum tri hydrate 13 g sodium naphthalene sulfate 14 g ceramic nanospheres Mix solution part B 7.9 g methanol 22 g Potassium hydroxide 2 ethylene glycol 4.1 g borax 3.8 g formalin 111 g 40% sodium silicate solution

[0107] Mixed part A and B into a well dispersed slurry. Slurry was applied as coating on substrates or cast into disks for thermal testing, then placed in an enclosure to prevent humidity loss and cured overnight in a 77 C. oven. Measured emissivity=0.82. Thermal conductivity=0.54 W/M2/sec.

Example 6

[0108]

TABLE-US-00007 Dry blend solid materials part A 15 g magnesium oxide 86 g alumina silicate 64 g flyash 18 g aluminum tri hydrate 13 g sodium naphthalene sulfate 14 g ceramic nanospheres 40 g titanium dioxide Mix solution part B 7.9 g methanol 22 g potassium hydroxide 2 g ethylene glycol 4.1 g borax 3.8 g formalin 111 g 40% sodium silicate solution

[0109] Mixed part A and B into a well dispersed slurry. Slurry was applied as coating on substrates or cast into disks for thermal testing. Placed in enclosure to prevent humidity loss and cured overnight in 77 C. oven. Measured emissivity=0.54. Thermal conductivity=0.59 W/M2/sec.

TABLE-US-00008 Example 5 32.90 0.54 Example 6 31.10 0.59 Graphite 5.32 33.7 Borosilicate 28.78 1.12 Aluminum 2.63 220 Mullite 11.86 2.5 Steel 5.23 51.9

Example 7

[0110]

TABLE-US-00009 Part A: Fly Ash 370 g Ground Glass Flour 400 g Metakaolin 290 g Sodium Naphthalene 8.5 g Sulfonate Magnesium Oxide 12.6 g Part B: 40% Sodium Silicate 556 g Potassium Hydroxide 98.2 g Ethylene Glycol 11 g Methanol 20 g Methylene Glycol (37%) 19 g

Example 8

[0111]

TABLE-US-00010 Part A: Fly Ash 370 g Ground Glass Flour 400 g Metakaolin 290 g Magnesium Oxide 12.6 g Part B: 40% Sodium Silicate 556 g Potassium Hydroxide 98.2 g Ethylene Glycol 11 g Methanol 20 g Methylene Glycol (37%) 19 g

Example 9

[0112]

TABLE-US-00011 Part A: Fly Ash 370 g Ground Glass Flour 400 g Metakaolin 290 g Sodium Naphthalene 8.5 g Sulfonate Magnesium Oxide 12.6 g Part B: 40% Sodium Silicate 556 g Potassium Hydroxide 98.2 g Ethylene Glycol 11 g Methanol 20 g Methylene Glycol (37%) 19 g 3 mm glass fiber 8 g 300 micron carbon fiber 50 g inch aramid fiber 150 g

Example 10

[0113]

TABLE-US-00012 Part A: Fly Ash 370 g Ground Glass Flour 400 g Metakaolin 290 g Sodium Naphthalene 8.5 g Sulfonate Magnesium Oxide 12.6 g Part B: 40% Sodium Silicate 556 g Potassium Hydroxide 98.2 g Ethylene Glycol 11 g Methanol 20 g Methylene Glycol (37%) 19 g sodium borate (5 H2O) 129 g 3 mm glass fiber 8 g 300 micron carbon fiber 50 g

[0114] For all examples:

[0115] Part A: all components are added and dry blended until uniform.

[0116] Part B is added sequentially with stirring each component one at a time in order, slowly to maintain a clear single-phase solution. Fiber was dispersed in the solution after all the other ingredients dissolved into a single phase.

[0117] Part A and B are added in a mixing cup at a ratio of 1:0.72 in a gyro mixer until well blended. The resulting slurry is then cast into a variety of useful shapes. The slurry cast was then placed in a container to prevent evaporation of the solvents and allowed to green set into the hydrogel at room temperature for two hours. The green set inorganic polymer was then removed from the mold. The green set inorganic polymer was then placed in a humidity-controlled oven at 180 F. for 12 hours for final cure.

[0118] The slurry was cast as a by inch disk for diametrical compression tensile strength measurement. Tensile strength of example 1 was 1029 psi with 7.9% elongation prior to fracture. Tensile strength of example 2, made without the plasticizer, was 1091 psi with 2.7% elongation prior to fracture. Tensile strength of example 3 with fiber was 1201 psi with 32% elongation prior to fracture.

[0119] The slurry of example 10 was cast as an injection mold halves into two 8 inches by 8 inches frame by 3-inch boxes with a wine cork mold half in each part and cured as above. The two mold halves were fit into a MUD frame and used on a plastic injection mold machine and thermoplastic urethane (TPU) parts made. Mold closing pressure was 110 tons, 3000 psi injection pressure.

[0120] In addition to the HCPC's versatility in terms of manufacturing parts and components from the material itself, the material also has several applications for use in the metal casting industry. The chemical inertness and temperature resistance of the material to 3400 F. allows it to be used to cast both nonferrous and ferrous metals and metal alloys. Due to its high dimensional stability at high temperatures and low reactivity, the material could allow a disruptive innovation in allowing steel to be die cast, currently impossible by conventional means. The tailorable thermal conductivity of the material is of especially great interest for aluminum casting; the faster the aluminum cools from molten to glassy state, the more amorphous the structure and the harder the resulting part. The quickest entry into the market is somewhat less glamorous: pattern casting material for medium to high-volume sand-casting operations. In these operations, sand is blown and/or pressed against a urethane pattern which are typically cast off of metal master. There is a need for a pattern casting material with higher abrasion resistance than urethane, and that can withstand the heat of hot sand mold making, rather than the cold sand required by the thermally labile urethanes. Hot sand making of molds allows considerably more rapid mold creation than cold sand methods.

[0121] The HCPC has several readily apparent dimensions of appeal: Its composition can be composed of available refined feedstocks and can optionally include various quantities of USA-sourced technical grade postindustrial waste stream materials, offsetting both bulk material costs and decreasing environmental impact of formulation. It contains no formaldehyde, VOC's, or heavy metals, thus mitigating personnel safety risk. It is potentially amenable to 3D-printing based rapid prototyping and fabrication methodologies; applications include rapid production of both part and molds. When used as a mold, the HCPC material can be tooled quickly in gel state, thereby minimizing machine time and labor expenses. If used as a mold, its high temperature stability and thermal conductivity allows for fast demold times of both cast metals, and sequentially, thermoset/plastics. The same mold can be used to cast multiple material types, including LiAl alloys, Steel, and as well as organic polymers.

[0122] These properties will allow the HCPC material to fulfill several material needs, which include high temperature structural component requirements that do not delaminate or crack, the need for fast turn-around time production methodologies and cross-material scalable design process, the need for low-cost high precision components at medium production scale, the need for ablative/reusable heat shielding, the need for advancements in cast metal process and associated materials, among others. Due to high dimensional stability, the HCPC material can also be used to make molds for casting titanium, steel, as well as lithium-aluminum alloys, and more.

[0123] When used as a viscous coating and patch-cured, our HCPC provides a highly temperature resistant, dimensionally stable, hydrophobic, thermal shock resistant coating with tunable electromagnetic absorption/conduction properties and high substrate bond strength. This coating can be applied at room temperature, contains no VOC's, and is environmentally friendly. Low deployment cost and increased durability decreases cost of production and sustainment for current and future LO material coated systems.

[0124] The materials of this invention have a lot of potential uses, including: dental implants and plating; speaker housings, bracings, passive/active absorbing interfaces, braces mounts, transducer component; synthetic decking, flooring, and tiling; ceramic preforms for investment casting; metal casting molds, cored, dies, patterns, and forms; precast building elements, load bearing and decorative; disc brakes, brake pads, bearings, rotary gaskets; glassblowing molds, pads, handles, tongs, forms, and others; dishware, drinking glasses/cups, plates, platters, bowls; adhesives, coatings, varnish, veneer, polish, stain, colorant; refractory cauldrons, kiln walls, molds, flooring; watch housings, belt buckles, buttons, cufflinks; building compound/binder (cement), bricks, highway sleepers, sidewalk slabs; grills, griddles, smokehouses, cookers, autoclaves; resistive heating elements, thermoelectric components; cast metal tooling and substrate; interleaved metal/ceramic products; cermets; solid surfaces such as countertops, bathroom sinks/basins, hot tubs, pools; performance flooring, roofing (continuous), tiles, extruded roofing plates; drivetrains: transaxle, engine components, front drive axle, drive shaft, rear drive axle, rear differential, and engine components; gears, sprockets, bolts, nuts, brackets, pins, bearings, cuffs; engine blocks, fly wheels, turbo fans, compression housings, fuel line connectors; turbine vanes, blades, rotary cores, ignition chambers, exit valves, guide nozzles; drilling shafts, well shield/walls, drill bits; aerospace interiors, arm rests walls, shelves, brackets and more; valves, pump housings, rotors; preforms for glass-to-metal seal; deep drilling rig, teeth, pylons, shaft, related equipment components; bricks, cinderblocks, speed bumps, flooring tiles; battery anode, cathode, housing; plug-in hybrid electric vehicle components, EMF shielding; wheel hubs and components; artificial limb and joint apparatus components; lighting housing, filament, base, bulb components; marine system components and hulls; biological sample gathering and treatment; basins, bowls, and vessels; heat radiation substrate; boats and boat parts; car and car parts; heat/abrasive/caustic/acidic material resistant pipes and linings; fluid and gas tanks; nozzles, bell jars, magnets, blades and abrasives, telecommunications relays, magnetrons, circuits; rings; general health care applications not otherwise mentioned; thermal and electric insulators; covers; microelectronic applications not otherwise mentioned, precast building elements, cast in place building elements, and structural elements applications not otherwise mentioned. Appliance housings, autobody interior and exterior paneling, bridge building and other distance spanning structural components. 3D printed components, structures, process, and elements. Electrical discharge machining heads and other components. appliance as in consumer appliance housings, bridge, and autobody for paneling.

[0125] Other possible applications are for prostheses, medical implants, countertops and labtops, consumer electronic housings, industrial and commercial flooring, can coatings, tank linings, pipe coatings and linings, re-bar, EDM milling electrode, and EDM milled parts. The materials of this invention can be used as coatings for various substrates, such as, for example, metals.