Patent Application
20210053831
Embodiments of the disclosure relate to methods and systems for forming solid carbon products from carbon nanotubes including mixtures of various types of carbon nanotubes and mixtures of carbon nanotubes with other substances.
The following documents, each published in the name of Dallas B. Noyes, disclose background information hereto, and each is hereby incorporated herein in its entirety by this reference:
Conventional methods of using CNTs (“carbon nanotubes”) or carbon nanofibers in engineering materials generally rely on embedding the CNTs or carbon nanofibers in a matrix material. CNTs are currently processed in a wide variety of composite structures using metals, plastics, thermoset resins, epoxies, and other substances as the matrix to hold the CNTs together, thus creating solid objects. The CNTs act as reinforcing material to improve properties of the materials. Typical objectives of using carbon nanotubes in a matrix are to increase the strength, decrease weight, or to increase electrical and thermal conductivity of the composite.
Methods to make materials composed primarily of carbon nanotubes include spinning the carbon nanotubes into fibers and making “buckyrock.” U.S. Pat. No. 6,899,945, issued May 31, 2005, and entitled “Entangled single-wall carbon nanotube solid material and methods for making same” discloses a method for making buckyrock. Buckyrock is a three-dimensional, solid block material including an entangled network of single-wall CNTs. Buckyrock is mechanically strong, tough, and impact resistant with a bulk density of about 0.72 g/cm3 (see Example 3 of U.S. Pat. No. 6,899,945). The single-wall CNTs in a buckyrock form are present in a random network. The random network of the CNTs appears to be held in place by Van der Waals forces between the CNTs and by physical entanglement or interference of the CNTs. One type of buckyrock is made by forming a slurry of CNTs in water, slowly removing water from the slurry to create a paste, and allowing the paste to dry very slowly, such that the CNT network of the paste is preserved during solvent evaporation. Buckyrock can be used in various applications requiring lightweight material with mechanical strength, toughness, and impact resistance, such as ballistic protection systems.
Though conventional materials including CNTs have interesting and useful properties, the individual CNTs comprising these materials have significantly different properties. It would therefore beneficial to produce materials having properties more comparable to the properties of individual CNTs.
Methods of forming solid carbon products include pressure compaction methods such as extruding, die pressing, roller pressing, injection molding etc. to form solid shapes comprising a plurality of carbon nanotubes. The carbon nanotubes may optionally be mixed with other substances. Such solid shapes may be further processed by heating in an inert atmosphere to temperatures sufficient to sinter at least some of the CNTs so that covalent bonds form between adjacent CNTs. The methods may include forming a plurality of nanotubes, disposing the plurality of nanotubes in a press, and applying heat and pressure to the plurality of carbon nanotubes to form the solid carbon product. When sintered, the resulting material is a novel composition of matter having two or more CNTs with covalent bonding between them.
The solid carbon products, whether sintered or not, include interlocked CNTs that define a plurality of voids throughout the material. The dimension of the interstitial voids may be controlled by a variety of methods including controlling the characteristic diameter of the CNTs comprising the solid carbon products, the inclusion of other materials that may create voids when removed from the solid carbon products, and the pressure and temperatures at which the solid carbon products are formed.
Sintered solid carbon products include a plurality of covalently bonded carbon nanotubes. In some embodiments, the sintered solid carbon products further include amorphous carbon covalently bonded to other carbon atoms, which may be amorphous carbon or crystalline carbon. Some methods include compressing a material comprising carbon nanotubes, heating the compressed material in a non-reactive environment to form chemical bonds between adjacent carbon nanotubes and form a bonded carbon nanotube structure, and cooling the bonded carbon nanotube structure to a temperature at which carbon of the carbon nanotubes does not react with oxygen.
Other methods include first forming a solid carbon product by compressing a material comprising carbon nanotubes and subsequently placing the resulting solid carbon product into sintering conditions. The sintering conditions may include an inert environment, such as a vacuum or inert atmosphere (e.g., argon or helium). The solid carbon product is heated to a desired temperature for a period of time to induce covalent bonding between adjacent CNTs, after which the object is cooled below the oxidation temperature of carbon in air. The product may then be removed from the sintering conditions.
Such methods may include any of a variety of standard industrial processing methods such as extrusion, die pressing, injection molding, isostatic pressing, and roll pressing. The sintering of the solid carbon products can be performed in a variety of apparatus such as are commonly used in sintered powder metallurgy and sintered ceramic processing. The sintering of the solid carbon products may include any of a variety of means including induction heating, plasma arc discharge, high temperature autoclaves and annealing furnaces, and other related devices and methods as are known in the art.
This disclosure includes methods of forming solid carbon products by applying heat and/or pressure to carbon nanotubes, carbon nanofibers, or both. As used herein, the term “solid carbon products” means and includes any material that comprises carbon and may include any material comprising at least one of one or more of carbon nanotubes and one or more carbon nanofibers. Solid carbon products may be useful in various applications, such as filters, reactors, electrical components (e.g., electrodes, wires, batteries), structures (e.g., beams, frames, pipes), fasteners, molded parts (e.g., gears, bushings, pistons, turbines, turbine blades, engine blocks), etc. Such solid carbon products may exhibit enhanced properties (e.g., strength, electrical or thermal conductivity, specific surface area, porosity, etc.) with respect to conventional materials. This disclosure includes a new class of materials that contain a plurality of CNTs, a plurality of carbon nanofibers, or a combination thereof formed into solid shapes under pressure. When such solid shapes are sintered, covalent bonds form between at least some of the CNTs, the carbon nanofibers, or both forming solid shapes. This material has numerous useful properties.
In other embodiments, solid carbon products may be formed by additive manufacturing. The solid carbon products may be formed to include carbon-carbon covalent bonds between at least some adjacent CNTs and/or carbon nanofibers between at least some of their contact points. In some embodiments, at least some of the carbon of the solid carbon products include amorphous carbon.
As used herein, the term “sintering” means and includes annealing or pyrolizing solid carbon products (e.g., CNTs and/or carbon nanofibers) at temperatures and pressures sufficient to induce carbon-carbon covalent bonding between at least some of the adjacent CNTs and/or carbon nanofibers between at least some of their contact points.
As used herein, the term “catalyst residual” means and includes any non-carbon elements associated with a CNT and/or a carbon nanofiber. Such non-carbon elements may include a nanoparticle of a metal catalyst in the growth tip of CNTs, and metal atoms or groups of atoms randomly or otherwise distributed throughout and on the surfaces of CNTs and/or carbon nanofibers.
As used herein, the term “green” means and includes any solid carbon product that has not been sintered.
CNTs may be created through any method known to the art, including arc discharge, laser ablation, hydrocarbon pyrolysis, the Boudouard reaction, the Bosch reaction and related carbon oxide reduction reactions, or wet chemistry methods (e.g., the Diels-Alder reaction). The methods described herein are applicable to carbon nanotubes regardless of the method of manufacture or synthesis. Carbon nanofibers may be formed through any method known in the art, including deposition from carbon vapor, such as by catalytic chemical vapor deposition (CCVD) wherein carbon is deposited in the presence of a transition metal catalyst on a substrate, or other method of forming carbon nanofibers known in the art.
CNTs may occur as single-wall and multi-wall carbon nanotubes of various diameters ranging from a few nanometers to 100 nanometers in diameter or more. CNTs may have a wide variety of lengths and morphologies, and may occur as substantially parallel “forests,” randomly tangled masses, or “pillows” of structured agglomerations. CNTs may also form or be compounded to form many different mixtures of CNTs with various combinations and distribution of the above characteristics (number of walls, diameters, lengths, morphology, orientation, etc.). Various mixtures, when compounded and used to form the solid carbon products described herein, may result in products with specifically engineered properties. For example, the median void size of interstitial spaces between CNTs comprising solid carbon products typically is approximately proportional to the characteristic diameters of the CNTs used in forming the solid carbon products. The median void size influences the overall porosity and density of the solid carbon products.
Various CNT features and configurations are illustrated in
The CNT 100 has an inside diameter related to the number of carbon atoms 102 in a circumferential cross section. The CNT 100 depicted in
CNTs having more than one wall are called multi-walled CNTs.
Carbon nanotubes are typically formed in such a way that a nanoparticle of catalyst is embedded in the growth tip of the carbon nanotube. This catalyst may optionally be removed by mild washing (e.g., by an acid wash). Without being bound to a particular theory, it is believed that if the catalyst is left in place, catalyst atoms become mobilized during the sintering process, and may migrate to the surface or within the pores of the carbon nanotubes. This process may disperse the catalyst atoms randomly, uniformly, or otherwise throughout the solid carbon product mass and may have a significant influence on the properties of the solid carbon product. For example, catalyst material may affect electrical conductivity or the ability to catalyze other chemical reactions.
The catalyst particles may be selected to catalyze other reactions in addition to the formation of solid carbon. Catalyst particles may be any material, such as a transition metal or any compound or alloy thereof. For example, catalyst particles may include nickel, vanadium oxide, palladium, platinum, gold, ruthenium, rhodium, iridium, etc. Because the catalyst particles are attached to or otherwise associated with CNTs, each catalyst particle may be physically separated from other catalyst particles. Thus, the catalyst particles may collectively have a much higher surface area than a bulk material having the same mass of catalyst. Catalyst particles attached to CNTs may therefore be particularly beneficial for decreasing the amount of catalyst material needed to catalyze a reaction and reducing the cost of catalysts. Compressed solid carbon products used as catalysts may, in many applications, benefit from the catalytic activity of both the CNT and the metal catalyst particles embedded in the growth tip of the CNTs.
The CNTs used in the processes herein may be single-walled CNTs, multi-walled CNTs, or combinations thereof, including bi-modally sized combinations of CNTs, mixtures of single-walled and multi-walled CNTs, mixtures of various sizes of single-walled CNTs, mixtures of various sizes of multi-walled CNTs, etc.
The CNTs and the carbon nanofibers may be in forms such as a sheet-molded compound, a pressure-molded compound, or as a pourable liquid. The CNTs and/or the carbon nanofibers may be disposed within a press any other device structured and configured to provide pressure to the material. The press may include an extrusion die, a mold, a cavity, etc. In other embodiments, the CNTs and/or the carbon nanofibers, may be incorporated into a structure comprising the CNTs and/or the carbon nanofibers by additive manufacturing.
For example, in the press 200 shown in
In some embodiments and as shown in the press 220 of
In other embodiments and as shown in the press 240 of
In an embodiment as shown in the press 260 of
Pressure is applied to form the carbon-containing material into a cohesive “green” body. For example, the screw mechanisms 210, 230 shown in
The pistons 266, 268 shown in
Heat is applied to green bodies to link the carbon-containing material together into a more cohesive body in which at least some of the adjacent CNTs and/or carbon nanofibers form covalent bonds between other CNTs and/or carbon nanofibers. For example, the carbon-containing material may be heated at a heating rate from about 1° C./min to about 50° C./min to a temperature of at least 1500° C., 1800° C., 2100° C., 2400° C., 2500° C., 2700° C. or even to just below the sublimation temperature of carbon (approximately 3600° C.). Pressure may also be applied concurrently with, before, or after heat is applied. For example, the carbon-containing material may be pressed at 10 to 1000 MPa, such as 30 MPa, 60 MPa, 250 MPa, 500 MPa, or 750 MPa. The green bodies may be subjected to a heated inert environment, such as helium or argon, in an annealing furnace. Sintering the carbon-containing material (i.e., subjecting CNTs and/or carbon nanofibers to heat in an oxygen-free environment) apparently creates covalent bonds between the CNTs and/or carbon nanofibers at points of contact. The sintering of the carbon-containing material typically occurs in a non-oxidizing environment, such as a vacuum or inert atmosphere so that the CNTs and/or carbon nanofibers are not oxidized during the sintering. Sintering the carbon-containing material to induce chemical bonding at the contact surfaces may improve desirable material properties such as strength, toughness, impact resistance, electrical conductivity, or thermal conductivity in the solid structure product when compared to the green material. The carbon-containing material may also be sintered in the presence of additional constituents such as metals or ceramics to form composite structures, lubricants to aid processing, or binders (e.g., water, ethanol, polyvinyl alcohol, coal, tar pitch etc.). Materials may be introduced as powders, shavings, liquids, etc. Suitable metals may include, for example, iron, aluminum, titanium, antimony, Babbitt metals, etc. Suitable ceramics may include materials such as oxides (e.g., alumina, beryllia, ceria, zirconia, etc.), carbides, boride, nitrides, silicides, etc. In embodiments in which materials other than CNTs and/or carbon nanotubes are present, covalent bonding occurs between at least some of the CNTs and/or carbon nanofibers, and the additional materials may become locked into a matrix of CNTs and/or carbon nanofibers.
The carbon-containing material in the sintered body may comprise chemical bonds connecting CNTs and/or carbon nanofibers with each other. Chemical bonds, which are generally stronger than physical bonds, impart different properties on the collection of the carbon-containing material than physical bonds. That is, the sintered body may have higher strength, thermal conductivity, electrical conductivity, or other properties than the green body from which it was formed.
When single-walled CNTs are covalently bonded to adjacent single-walled CNTs, holes can form on the surface of the CNTs as some of the carbon-carbon bonds break, thus modifying the mechanical and electrical properties of each single-walled CNT. Sintered single-walled CNTs, however, may still typically exceed non-sintered single-walled CNTs in such properties as strength, toughness, impact resistance, electrical conductivity, and thermal conductivity. With multi-walled CNTs, typically only the wall of the outer tube is modified; the internal walls remain intact. Thus, using multi-walled and bi-modally sized CNTs in, for example, extrusion and molding processes, may yield solid structures with properties that, in many respects, exceed practical limitations of single-walled CNTs. Similarly, using carbon nanofibers in, for example, extrusion and molding processes, may yield solid carbon products with properties that, in many respects, exceed practical limitations of carbon nanofiber bound together, such as in a tow or carbon nanofibers.
Sintering appears to cause covalent bonds to form between the walls of CNTs at their contact points and between outer surfaces of carbon nanofibers at their contact points. That is, any given CNT or carbon nanofiber may “cross-link” with an adjacent CNT or carbon nanofiber at the physical point of contact of the two structures. Any given CNT or carbon nanofiber having undergone sintering may be covalently bound to numerous other CNTs (both single-walled CNTs and multi-walled CNTs) and/or carbon nanofibers. This increases the strength of the resulting structure because the CNTs and/or carbon nanofibers do not slide or slip at the bonding points. Unsintered, CNTs (e.g., in buckyrock) and/or carbon nanofibers may slide with respect to each other. Because the covalent bonding caused by sintering may occur at numerous sites in the mass of CNTs and/or carbon nanofibers, the sintered body has significantly increased strength, toughness, impact resistance, and conductivity over convention agglomerations of CNTs and/or carbon nanofibers.
In another embodiment, a mixture comprising one or more CNTs, one or more carbon nanofibers, or both, is heated in a reactive environment (e.g., in the presence of oxygen, hydrogen, a hydrocarbon, and/or another material). In this embodiment, heat and pressure are maintained as needed until the reactants in the reactive environment have reacted with one another or with the CNTs and/or carbon nanofibers. The product is then cooled. In such a process, the reactants may form additional holes or pores in the CNTs and/or carbon nanofibers, increasing the specific surface area of the sintered body. Alternatively, the reactants may deposit materials on the surface of the CNTs and/or carbon nanofibers without affecting the underlying CNT and/or carbon nanofiber structure.
In another embodiment, the mixture comprising one or more CNTs and/or one or more carbon nanofibers is initially heated and sintered in a nonreactive environment (e.g., in a vacuum, in the presence of helium, or in the presence of argon). Subsequent to sintering, the heat and pressure are changed to suitable reaction conditions and reactants are added to the environment. Such reactants may include a variety of metals (as liquid or vapor), metal carbonyls, silanes, or hydrocarbons. The reaction of the reactants with one another or with the carbon of the one or more CNTs and/or one or more carbon nanofibers may fill some or all of the interstices of the solid carbon product lattice (e.g., the CNT lattice) with products of the reactions. Such processing with additional reactants may in some cases be conducted during sintering, but may also be performed separately. The heat and pressure are maintained until the desired level of reaction (both cross-linking within the CNTs and/or carbon nanofibers, and the reaction between the CNTs and/or carbon nanofibers and the reactant) has occurred. The reacted mixture is then cooled and removed from the reaction environment for further processing, storage, packaging, shipment, sale, etc.
During the sintering process, the green body may shrink, corresponding with a decrease in the size of voids among the CNTs and/or carbon nanofibers. However, the sintered body may remain porous due to the porosity of each CNT (i.e., the center of the CNT) and due to voids between and among CNTs and/or carbon nanofibers. The sintered body may have pores or voids having a median minimum dimension of less than about 1 μm, less than about 500 nm, less than about 100 nm, less than about 50 nm, or even less than about 10 nm. That is, each void may have two or more dimensions (e.g., a length, a width, and a height, each perpendicular to the others, or a diameter and a length), measured in different directions. The voids need not be regularly shaped. The “minimum dimension” is defined as the minimum of the two or more dimensions of a single void. The “median minimum dimension” is defined as the median of these minimum dimensions for a group of voids.
A sintered body as described herein may have a high specific surface area, due to voids between CNTs and/or carbon nanofibers and within CNTs (i.e., because the CNTs are hollow). For example, a sintered body may have a specific surface area of at least about 100 m2/g, at least about 500 m2/g, at least about 750 m2/g, at least about 900 m2/g, or even at least about 1000 m2/g. The specific surface area can be controlled by the characteristic diameters or mixture of diameters of the CNTs and/or carbon nanofibers used in forming the solid carbon product. For example, small-diameter single-walled CNTs have specific surface areas up to approximately 3000 m2/g, while large-diameter multi-walled CNTs have specific surface areas of approximately 100 m2/g. In some embodiments, the sintered body may be formed from CNTs having at least one property (e.g., a diameter, a density, a specific surface area, a length, etc.) different than an analogous property of at least some carbon nanofibers used to form the sintered body.
A sintered body may have a high electrical conductivity. For example, a sintered body may have an electrical conductivity of at least about 1×105 S/m (Siemens per meter), at least about 1×106 S/m, at least about 1×107 S/m, or even at least about 1×108 S/m. The electrical conductivity can be controlled by the types of carbon-containing materials (e.g., CNTs and/or carbon nanofibers) used, the chirality of the carbon-containing materials (e.g., CNTs and/or carbon nanofibers) used, the sintering conditions, and the quantity of resulting covalent bonds in the solid carbon product. For example, single-walled CNTs with a metallic chirality have a much higher electrical conductivity than multi-walled CNTs. As a further example, an increase in the number of covalent bonds appears to correlate with an increase in conductivity.
A sintered body may also have a high thermal conductivity. For example, a sintered body may have a thermal conductivity of at least about 400 W/m·K (watts per meter per Kelvin), at least about 1000 W/m·K, at least about 2000 W/m·K, or even at least about 4000 W/m·K. The thermal conductivity of the resulting solid carbon product may be controlled by the types of carbon-containing material (e.g., CNTs and/or carbon nanofibers) used and the chirality of the carbon-containing material (e.g., CNTs and/or carbon nanofibers used). For example, single-walled CNTs with a metallic chirality have much high thermal conductivity than large multi-walled CNTs.
CNTs and/or nanofibers may alternatively be pressed after the sintering process by, for example, extrusion or molding, as described above with respect to
In some embodiments, an incremental manufacturing method may be employed wherein, CNTs (either compressed or not) and/or carbon nanofibers are placed in a nonreactive environment, such as in an inert gas autoclave. The CNTs and/or carbon nanofibers are sintered to form covalent bonds between the CNTs and/or carbon nanofibers in the surface layer and the underlying layer. For example, a laser may irradiate a portion of the CNTs and/or carbon nanofibers in a pattern. Additional CNTs and/or carbon nanofibers are deposited over the sintered CNTs and/or carbon nanofibers, and in turn sintered. The sintering process is repeated as many times as necessary to achieve a selected thickness of sintered structure comprising CNTs and/or carbon nanofibers. The sintered CNTs and/or carbon nanofibers are then cooled to a temperature below which the CNTs and/or carbon nanofibers do not react with oxygen or other atmospheric gases. The sintered CNTs and/or carbon nanofibers may then be removed from the nonreactive environment without contaminating the sintered CNTs and/or carbon nanofibers. In some embodiments, the sintered CNTs and/or carbon nanofibers are cooled and removed from the nonreactive environment before deposition of each additional portion of CNTs and/or carbon nanofibers.
In some embodiments, a structure comprising CNTs and/or carbon nanofibers may be formed by additive manufacturing, such as by, for example, selective laser sintering (SLS), laser engineered net shaping, or other 3D printing or additive manufacturing process. In some embodiments, the structure may be formed one layer at a time.
The tool 400 may include one or more powder delivery nozzles 404. The powder delivery nozzles 404 may be configured to provide a powder material over a surface of the structure 450 on the movable stage 410 to form a powder layer 420 thereon. In some embodiments, the powder delivery nozzles 404 may be configured to provide the powder layer 420 to the structure 450 coaxially with the laser radiation from the laser 402. Each of the powder delivery nozzles 404 may be configured to provide a powder material having a different composition than that provided by the other powder delivery nozzles 404. In some embodiments, the powder may be provided from the powder delivery nozzles 404 to the surface of the structure 450 or the substrate by gravity. In other embodiments, the powder may be fed with an inert carrier gas, such as, for example, nitrogen, argon, helium, another inert carrier gas, or combinations thereof. Although
The laser 402 may be configured to direct electromagnetic radiation (e.g., laser radiation) through a lens 408 and to the powder layer 420 over the structure 450. Responsive to exposure to heat provided by the laser radiation, individual particles of the powder layer 420 may form inter-granular bonds with each other and with previously formed layers of the structure 450 previously exposed to the laser radiation.
The lens 408 may comprise a focusing lens and may be positioned to focus laser radiation from the laser 402 a predetermined distance from the laser 402.
The movable stage 410, on which the structure 450 may be disposed, may be configured to move in one or more directions. By way of nonlimiting example, the movable stage 410 may be configured to move in one or more of a z-direction (e.g., up and down in the cross-sectional view of
In other embodiments, the laser 402 may be configured to move in one or more directions, such as, for example, one or more of the z-direction, the y-direction, and the x-direction. Accordingly, the laser 402 may be configured to move relative to the structure 450 and the movable stage 410.
In use and operation, the powder layer 420 may be formed over an uppermost surface of the structure 450. The powder layer 420 may be exposed to laser radiation from bonds between the powder and the structure 450 (e.g., such as by sintering). Exposing the powder layer 420 to laser radiation may form another layer on the structure 450. As described above, at least one of the laser 402 or the movable stage 410 may be coupled to a suitable drive assembly to move in a horizontal plane (e.g., the x-direction, the y-direction, or both) in a designated pattern and speed to expose selected portions of the powder layer 420 to the laser radiation. After formation of the layer of the structure, the structure 450 may be moved away from the laser 402 (such as by moving the laser 402, moving the movable stage 410, or both) a predetermined distance, which may correspond to a thickness of the previously formed layer of the structure 450. By way of nonlimiting example, the movable stage 410 may be moved away from the laser 402 after forming a layer of the structure 450. Movement of the structure 450 relative to the laser 402 may form a cavity defined by the previously formed layer and the sidewall structures 412. Powder may be deposited within the cavity and over the structure 450 by one or more of the powder delivery nozzles 404 to form another powder layer 420 over the previously formed layer of the structure 450. The powder layer 420 may be compacted and subsequently exposed to laser radiation to form another layer of the structure 450. Accordingly, the structure 450 may be formed layer-by-layer.
In some embodiments, the tool 400 may be substantially enclosed, such as with an enclosure 440. The interior of the enclosure 440 may be substantially free of oxygen or other gases that may oxidize or otherwise react with the powders that form the structure 450 during exposure of the powders to the laser radiation. In some embodiments, the interior of the enclosure 440 includes one or more of the shield gases (e.g., argon). In some embodiments, a concentration of oxygen in the enclosure 440 may be less than about 70 ppm, such as less than about 50 ppm, less than about 40 ppm, less than about 20 ppm, or less than about 10 ppm.
Although the tool 400 has been described as including powder delivery nozzles 404, the disclosure is not so limited. In other embodiments, the tool 400 may include a different powder delivery system. By way of nonlimiting example, the tool 400 may include a powder delivery piston located adjacent the movable stage 410 such as in a selective laser sintering (SLS) tool. The powder delivery piston may be configured to introduce one or more powders to a location coplanar with an uppermost surface of the structure 450. A roller may be configured to roll powder from the powder delivery system to a location on the uppermost surface of the structure 450.
Act 502 includes forming one or more mixtures of a powder that will be used to additively manufacture at least one structure. In some embodiments, a first powder material is mixed with at least a second, different powder material to form a powder mixture including particles of the first powder material substantially homogeneously dispersed throughout particles of the second powder material.
The first powder material may comprise CNTs, carbon nanofibers, a combination thereof. By way of nonlimiting example, the powder material may comprise single-walled CNTs and multi-walled CNTs, such as the single-walled and multi-walled CNTs described above. A diameter of particles of the first powder material may be between about 1 nm and about 100 μm, such as between about 1 nm and about 10 nm, between about 10 nm and about 50 nm, between about 50 nm and about 100 nm, between about 100 nm and about 500 nm, between about 500 nm and about 1 μm, between about 1 μm and about 5 μm, between about 5 μm and about 10 μm, between about 10 μm and about 50 μm, or between about 50 μm and about 100 μm. In some embodiments, the diameter of the particles of the first powder material is between about 1 μm and about 5 μm.
The second powder material may comprise one or more materials that may be incorporated into the structure being formed. In some embodiments, the second powder material comprises at least one material selected from the group consisting of at least one metal, at least one ceramic (e.g., a carbide, a nitride, a silicide, an oxide), and at least one other material. By way of nonlimiting example, the second powder material may comprise one or more of aluminum, silicon, phosphorus, sulfur, titanium, vanadium, chromium, manganese, iron, cobalt, nickel, copper, zinc, zirconium, palladium, silver, cadmium, tin, tantalum, tungsten, platinum, and gold, a ceramic (e.g., a carbide (e.g., aluminum carbide, tungsten carbide, cementite, silicon carbide, titanium carbide, boron carbide, etc.), an oxide (e.g., alumina (Al2O3), beryllia, ceria, zirconia, etc.) a nitride (e.g., silicon nitride), a silicide (e.g., ferrosilicon (Fe5Si2), manganese silicide (MnSi2), titanium disilicide (TiSi2), silicon boride (SiB4, SiB6), etc.), borides (such as, for example, aluminum diboride (AlB2), cobalt boride (CoB, CO2B), nickel boride (NiB), tantalum boride (TaB, TaB2), titanium boride (TiB2), tungsten boride (WB), etc.), or combinations thereof.
The first powder material may constitute between about 1 weight percent (1 wt. %) and about 50 weight percent of the powder mixture, such as between about 1 weight percent and about 5 weight percent, between about 5 weight percent and about 10 weight percent, between about 10 weight percent and about 20 weight percent, between about 20 weight percent and about 30 weight percent, between about 30 weight percent and about 40 weight percent, or between about 40 weight percent and about 50 weight percent of the powder mixture.
The second powder material may constitute between about 50 weight percent and about 99 weight percent of the powder mixture, such as between about 50 weight percent and about 60 weight percent, between about 60 weight percent and about 70 weight percent, between about 70 weight percent and about 80 weight percent, between about 80 weight percent and about 90 weight percent, or between about 90 weight percent and about 99 weight percent of the powder mixture.
In some embodiments, particles of the powder mixture may comprise coated particles. One of the first powder material and the second powder material may be coated with the other of the first powder material and the second powder material. By way of nonlimiting example, particles of one or more CNTs and/or carbon nanofibers may be coated with one or more materials of the second powder material (e.g., at least one of one or more of metals and one or more ceramics). In other embodiments, one or more particles of the second powder material may be coated with one or more of CNTs and/or carbon nanofibers. The particles of the powder material may be coated by one or more of atomic layer deposition (ALD), chemical vapor deposition (CVD), or other suitable method. In some such embodiments, forming the one or more powder mixtures may include forming a powder mixture comprising one or more of CNTs and/or carbon nanofibers coated with a second material or a second material coated with one or more of CNTs and/or carbon nanofibers.
Act 504 includes introducing the one or more powder mixtures over a substrate to form a powder layer over the substrate. In some embodiments the first powder material and the second powder material may be disposed over the substrate separately, such as through separate powder delivery nozzles 404 (
Sufficient powder may be provided over the surface of the substrate to form a layer having a thickness between about 10 nm and about 100 μm, such as between about 10 nm and about 50 nm, between about 50 nm and about 100 nm, between about 100 nm and about 500 nm, between about 500 nm and about 1 μm, between about 1 μm and about 5 μm, or between about 5 μm and about 10 μm.
The powder may be provided to the selected locations over the substrate such that a cross-sectional profile of the powder layer exhibits a selected cross-sectional shape and composition of the structure. By way of nonlimiting example, where the structure being formed comprises, for example, an I-beam, the cross-sectional profile of the powder layer formed over the structure may exhibit a cross-sectional profile of the I-beam.
The powder delivery nozzles 404 (
Act 506 includes selectively exposing at least a portion of the powder layer to laser radiation, such as portions of the powder layer that are desired to be in the final structure, to form a layer of a structure. Exposing the powder layer to the laser radiation may form inter-granular bonds between adjacent particles of the powder layer and underlying layers of the structure previously formed. In some embodiments, exposing the powder layer to the laser radiation forms carbon-carbon bonds between particles of the powder layer and between particles of the powder layer and underlying particles of the structure previously formed. In some embodiments, such as where the second powder material comprises carbon (e.g., a carbide material), exposing the powder layer to the laser radiation may form carbon-carbon bonds between at least some particles of the first powder material and at least some particles of the second powder material. Exposing the powder layer to the laser radiation may further form metal-metal bonds between particles of the second powder material in the same layer and between particles of the second powder material in adjacent layers.
As described above, at least one of the movable stage 410 (
The laser 402 may be any suitable laser configured to provide energy in the form of electromagnetic radiation (e.g., laser radiation) to the powder layer. In some embodiments, the laser 402 is configured to provide electromagnetic radiation having a substantially monochromatic wavelength to the powder layer. By way of nonlimiting example, the laser 402 may comprise a helium-neon laser (having a wavelength of about 632.8 nm), an argon laser (having a wavelength of about 454.6 nm, about 488.0 nm, or about 514.5 nm), a krypton laser (having a wavelength between about 416 nm, about 530.9 nm, about 568.2 nm, 647.1 nm, about 676.4 nm, about 752.5 nm, or about 799.3 nm, a xenon ion laser, a nitrogen laser (having a wavelength of about 337.1 nm), a carbon dioxide laser (having a wavelength of about 10.6 μm), a carbon monoxide laser (having a wavelength between about 2.6 μm and about 4.0 μm or between about 4.8 μm and about 8.3 μm), an excimer laser (having a wavelength of about 193 nm, about 248 nm, about 308 nm, or about 353 nm), a fiber laser, or combinations thereof. However, the laser is not so limited and may comprise any suitable laser to provide sufficient energy to the powder layer to form bonds therein. The laser 402 may be configured to provide electromagnetic radiation having a power between about 10 W and about 1 kW, such as between about 10 W and about 50 W, between about 50 W and about 100 W, between about 100 W and about 500 W, or between 500 W and about 1 kW. However, the laser 402 may have a different power and the disclosure is not limited by laser type or power.
Exposing the powder layer to the laser radiation may locally heat the powder layer at regions that are exposed to the laser radiation. In some embodiments, the powder layer may be locally heated to temperatures sufficient to melt at least the second powder material. In some embodiments, the temperature may be between a melting temperature of the second powder material and a melting temperature of carbon (e.g., of carbon nanotube and of carbon nanofibers). In some such embodiments, the temperature may be less than about 3,500° C. By way of nonlimiting example, the temperature may be between about 500° C. and about 3,500° C., such as between about 500° C. and about 1,000° C., between about 1,000° C. and about 1,500° C., between about 1,500° C. and about 2,000° C., between about 2,000° C. and about 2,500° C., between about 2,500° C. and about 3,000° C., or between about 3,000° C. and about 3,500° C. In some embodiments, the temperature may be between about 1,400° C. and the sublimation temperature of carbon. In other embodiments, the temperature may be at least about 2,100° C.
In some embodiments, the second powder material may be selected to exhibit a greater thermal expansion that the first powder material. In some such embodiments, particles of the second powder material may condense or shrink onto particles of the first powder material responsive to cooling after exposure to the laser radiation. Such differences in thermal expansion and cooling of particles of the second powder material may form a physical (e.g., mechanical) bond between particles of the first powder material and particles of the second powder material in the same layer of the structure and in adjacent layers of the structure.
Act 508 includes repeating cycles of act 504 and act 506 until a net shape (i.e., a near final shape) of the structure is formed. After exposing the powder layer to laser radiation to form a layer of the structure, the structure may be moved a predetermined distance from the laser 402 (
The structure may be formed layer-by-layer to form a structure exhibiting a net shape of a final structure. Each layer of the structure may exhibit a different cross-sectional shape than other layers of the structure.
In some embodiments, the structure may be machined, heat treated, or a combination thereof, to a final shape after the additive manufacturing process.
The structure formed according to the method 500 may include one or more of structural members (e.g., beams), fasteners (e.g., screws), moving parts (e.g., propellers, crankshafts, etc.), tubes, channels, plates, electrically conductive members (e.g., electrodes, wires, etc.), a stage of a scanning electron microscope (SEM), or any other structure.
In certain embodiments, sintered solid carbon products are formed in a belt-casting operation. A layer of CNTs and/or carbon nanofibers is placed on a moveable belt. The belt moves the CNTs and/or carbon nanofibers into a chamber containing a nonreactive environment. The CNTs and/or carbon nanofibers are sintered in the chamber, then cooled (e.g., in a portion of the chamber), and removed from the chamber. The process may be operated continuously, such as to form a sheet of sintered CNTs and/or carbon nanofibers.
In some embodiments, solid carbon products are further treated by electrodeposition to fill interstices in the solid carbon products with another material. A solution having materials to be deposited is prepared. The solvent of the solution may be water, an organic solvent, or an inorganic solvent. The solute may include a material such as a metal salt, an organic salt, a metalorganic salt, etc. Electroplating solutions are known in the art and not described in detail herein. The solid carbon product to be treated is contacted with the solution, such as by immersing the body in the solution. An electric potential (a direct-current voltage or an alternating-current voltage) is applied to the body to induce electrodeposition of one or more components of the solution. The composition, potential, temperature, and/or pressure are maintained until a selected amount of the material is deposited onto the solid carbon product. The solid carbon product is then removed from the solution and rinsed to remove excess solution.
Solid carbon products formed as described herein each include a plurality of cross-linked CNTs and/or carbon nanofibers. The CNTs define a plurality of voids, which may have a median minimum dimension of less than about 1 μm, less than about 500 nm, less than about 100 nm, less than about 50 nm, or even less than about 10 nm. Some or all of the carbon-containing material (e.g., the CNTs and/or the carbon nanofibers) may include a metal, such as a metal particle from which the CNTs and/or carbon nanofibers were formed, or a metal coating on the CNTs and/or carbon nanofibers. The solid carbon products may be structural members (e.g., beams), fasteners (e.g., screws), moving parts (e.g., propellers, crankshafts, etc.), electrically conductive members (e.g., electrodes, wires, etc.), or any other form. The solid carbon product may include another material dispersed in a continuous matrix surrounding and in contact with the CNTs and/or carbon nanofibers. The solid carbon products may have improved strength, toughness, impact resistance, and electrical and thermal conductivity in comparison to conventional materials.
In some embodiments, the solid carbon products also include other morphologies of carbon, interspersed with or otherwise secured to the CNTs and/or carbon nanofibers. For example, buckyballs may be connected to some of the CNTs and/or carbon nanofibers. As another example, one or more graphene sheets may be formed over all or a portion of a solid carbon product.
Both the compressed solid carbon products and the sintered solid carbon products described herein have a wide variety of potentially useful applications. For example, the compressed solid carbon products may be used as filters, molecular sieves, catalysts, and electrodes in applications where the additional mechanical integrity achieved through sintering is not necessary. The sintered solid carbon products can be used in the applications in which compressed solid carbon products can be used and in a wide variety of additional applications requiring additional mechanical integrity, electrical properties, and other material-property enhancements achieved through sintering.
Sintered solid carbon products may be useful components of armor because of their mechanical integrity, ability to absorb compressive loads with a high spring constant, and ability to dissipate heat. That is, sintered solid carbon products may be used to form projectile-resistant materials, such as armor plates, bullet-proof vests, etc. The light weight of the solid carbon products could improve mission payloads, increase vehicle range, and alter the center of gravity. For example, armor materials including sintered solid carbon products may be beneficial in preventing injury and death of occupants of vehicles such as Mine Resistant Ambush Protected vehicles (“MRAPs”), which are prone to tipping. Sintered solid carbon products as described herein may be effective in light-weight armament systems such as mortar tubes, gun barrels, cannon barrels, and other components. Sintered solid carbon products may also be beneficial in aerial vehicles, such as aircraft, spacecraft, missiles, etc.
CNTs were formed as described in U.S. Patent Publication No. 2012/0034150 A1. Samples of approximately 1.0 grams to 1.25 grams of CNTs each were pressed in 15-mm diameter dies using a 100-ton (890-kN) press. The pressed samples were placed in an inert gas furnace (Model 1000-3060-FP20, available from Thermal Technology, LLC, of Santa Rosa, Calif.) and heated under vacuum at a rate of 25° C. until the samples reached 400° C. This temperature was maintained for 30 minutes to allow the samples to outgas any oxygen, water, or other materials present. The furnace was then filled with inert gas (argon or helium) at 3-5 psi (21 to 34 kPa) above atmospheric pressure. The furnace was heated at a rate of 20° C./min until the sample reached 1500° C. This temperature was maintained for 30 minutes. Heating continued at 5° C./min to a sintering temperature, which was maintained for a dwell time of 60 minutes. The samples were then cooled at 50° C./min to 1000° C., after which the furnace was shut down until the samples reached ambient temperature. The sample masses, compaction pressures, and sintering temperatures for the samples are shown in Table 1 below. The inert gas was helium for the samples sintered at 2400° C. and was argon for the other samples.
Samples 1 through 18 were harder and more robust than were the samples before the heating process. At the highest sintering temperature of 2400° C. (samples 7 through 9), the sintered pellets are flakier than the other sintered samples. All the samples prepared in Example 1 were qualitatively observed to be hard.
Pycnometry tests show that the skeletal density decreases from 2.2 g/cm3 for raw powders and raw compactions to 2.1 g/cm3, 2.08 g/cm3, and 2.05 g/cm3 for the samples sintered at 1800° C., 2100° C., and 2400° C., respectively. Bulk density also decreased after sintering, in almost every case to less than 1.0 g/cm3. Pellet thickness increased 5% to 9% during sintering, with the higher pressure compactions expanding more than the lower pressure compactions. The bulk densities of Samples 1 through 9 are shown in Table 2 and in
CNTs were formed as described in U.S. Patent Publication No. 2012/0034150 A1. Graphite foil (available from Mineral Seal Corp., of Tucson, Ariz.) was lined into 20-mm diameter dies, and 2.0 g to 4.0 g of CNTs were placed over the foil. The samples were placed in a spark plasma sintering (SPS) system (model SPS 25-10, available from Thermal Technology, LLC, of Santa Rosa, Calif.). An axial pressure of approximately 5 MPa was applied to the CNT samples, and the SPS system was then evacuated to less than 3 mTorr (0.4 Pa). The sample was heated at 150° C./min to 650° C., and this temperature was maintained for one minute to allow the vacuum pump to re-evacuate any materials out-gassed. The pressure was increased to the compaction pressure of 30 MPa or 57 MPa, while simultaneously increasing the temperature at a rate of 50° C./min to 1500° C. The temperature and pressure were maintained for one minute. The temperature was then increased at 50° C./min to the sintering temperature, and maintained for 10 min or 20 min. After the dwell, the pressure was reduced to 5 MPa, and the sample allowed to cool at 150° C./min to 1000° C., after which the furnace was shut off until the samples reached ambient temperature.
The sample masses, compaction pressures, compaction rates, sintering temperatures, and dwell times for the samples are shown in Table 2 below.
The SPS-sintered pellets formed in Example 2 were about 10 mm thick and had bulk densities between 1.3 g/cm3 and 1.5 g/cm3. To illustrate the strength of these samples, sample #20 was planned to be sintered 2100° C., but at about 1900° C., the die broke. The ram traveled significantly, crushing the graphite die. After the test was completed, the die was broken away from the sample. The sample remained visibly intact, though slightly thinner than expected. This would indicate that the sintering occurs at temperatures less than 1900° C., that the strength of SPS-sintered pellets is high, even at extreme temperatures, and that the sintered samples are strong enough to resist an applied force without fracturing.
The bulk densities of the samples with the graphite foil still attached were determined. For the samples weighing about 4 g (i.e., samples #21, #22, and #23), bulk densities were between 1.35 g/cm3 and 1.50 g/cm3. The volume resistivity and electrical conductivity of the samples were also measured. These data are shown in Table 4. The samples are more conductive than amorphous carbon, and nearly as conductive as graphite.
Although the foregoing description contains many specifics, these are not to be construed as limiting the scope of the present invention, but merely as providing certain embodiments. Similarly, other embodiments of the invention may be devised which do not depart from the scope of the present invention. For example, features described herein with reference to one embodiment also may be provided in others of the embodiments described herein. The scope of the invention is, therefore, indicated and limited only by the appended claims and their legal equivalents, rather than by the foregoing description. All additions, deletions, and modifications to the invention, as disclosed herein, which fall within the meaning and scope of the claims, are encompassed by the present invention.
This application is a divisional of U.S. patent application Ser. No. 15/663,392, filed Jul. 28, 2017, which will issue as U.S. Pat. No. 10,815,124 on Oct. 27, 2020, and is a continuation-in-part of U.S. patent application Ser. No. 15/470,587, filed Mar. 27, 2017, which is a divisional of U.S. patent application Ser. No. 14/414,232, filed Jan. 12, 2015, now U.S. Pat. No. 9,604,848, issued Mar. 28, 2017, which is a national phase entry under 35 U.S.C. § 371 of International Patent Application PCT/US2013/049719, filed Jul. 9, 2013, designating the United States of America and published in English as International Patent Publication WO 2014/011631 A1 on Jan. 16, 2014, which claims the benefit under Article 8 of the Patent Cooperation Treaty to U.S. Provisional Patent Application Ser. No. 61/671,022, filed Jul. 12, 2012, for “Solid Carbon Products Comprising Carbon Nanotubes and Methods of Forming Same,” the disclosure of each of which is hereby incorporated herein in its entirety by this reference.
| Number | Date | Country | |
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| 61671022 | Jul 2012 | US |
| Number | Date | Country | |
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| Parent | 15663392 | Jul 2017 | US |
| Child | 17080566 | US | |
| Parent | 14414232 | Jan 2015 | US |
| Child | 15470587 | US |
| Number | Date | Country | |
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| Parent | 15470587 | Mar 2017 | US |
| Child | 15663392 | US |
