Patent Grant
9852824
The present invention relates to aerogels, and more particularly, to controlling pore morphology in aerogels.
Aerogels are a fascinating class of high surface-area, mechanically-robust materials with a broad range of both commercial and fundamental scientific applications. Owing to its highly porous mass-fractal nanostructure, amorphous silica aerogel has been used as a capture agent in NASA's cometary-dust retrieval missions, to control disorder in 3He-superfluid phase transitions, in the fabrication of targets for laser inertial confinement fusion, in low-k microelectromechanical systems (MEMS), and in Cherenkov nucleonic particle detectors.
In particular, amorphous carbon aerogel has received a considerable amount of attention in recent years owing to its light weight, low cost, electrical conductivity, mechanical strength, and thermal stability. Numerous applications have been explored for this material, including water desalination, electrochemical supercapacitors, and thermal insulation, among others.
Carbon aerogels are furthermore useful for a number of different applications due to their lightweight, conductive, and fairly robust characteristics. In addition, manipulation of a number of their properties, such as pore size, surface area, and density, are well known. However, if pores of a particular orientation are required, for example, to improve mass transport in a particular direction, such a carbon aerogel could not be produced without hard templating, which adds an additional step to the process. Therefore, in order to reduce processing cost, time, and complexity, it would be useful to expand the control of carbon aerogel properties to include pore orientation.
In addition, manipulation of a number of properties of aerogels, and particularly carbon aerogels, such as pore size, surface area, and density, have been performed before and are capable of being reproduced by those skilled in the art. However, currently, there has not been demonstrated any ability to control the orientation of the major pores of a carbon aerogel, for example, to improve mass transport in a particular direction, without hard templating methods, which add one or more additional steps to the aerogel formation process, and are thus time consuming and less efficient.
Furthermore, the current state of the art in the field of target materials for rare isotope production has not taken advantage of the recent advancements in materials science, particularly the tailoring of microstructures and macrostructures for property optimization. Rare isotope beam (RIB) targets are used at accelerator facilities around the world to generate the desired isotope beams for high energy physics experiments and also for rare isotope production used in industrial and medical applications. Typical target assemblies for use in isotope mass separation on-line (ISOL) facilities must be able to withstand extremely high particle flux and extreme operating temperatures.
Due to extreme operating conditions, the typical target lasts only two to four weeks. The down time associated with target replacement using conventional methods, 1-2 weeks, leads to a significant decrease in both isotope production and beam time available for experiments. Therefore, a method for producing such targets quickly, reliably, and inexpensively would confer great benefit to RIB applications.
In one embodiment, an aerogel or xerogel includes column structures including a material, the column structures having minor pores therein and major pores devoid of the material positioned between the column structures, with longitudinal axes of the major pores being substantially parallel to one another.
In another embodiment, a method includes heating a sol including aerogel or xerogel precursor materials to cause gelation thereof to form an aerogel or xerogel and exposing the heated sol to an electric field, wherein the electric field causes orientation of a microstructure of the sol during gelation, which is retained by the aerogel or xerogel.
In still another embodiment, an aerogel or xerogel includes elongated major pores extending between a material arranged in column structures, each column structure having a plurality of minor pores therein, wherein a longitudinal axis of each of the elongated major pores are substantially parallel to a single axis, and wherein the aerogel or xerogel has structural characteristics of being formed from a sol exposed to an electric field that causes orientation of a microstructure of the sol during gelation which is retained by the elongated major pores of the aerogel or xerogel.
Other aspects and embodiments of the present invention will become apparent from the following detailed description, which, when taken in conjunction with the drawings, illustrate by way of example the principles of the invention.
The following description is made for the purpose of illustrating the general principles of the present invention and is not meant to limit the inventive concepts claimed herein. Further, particular features described herein can be used in combination with other described features in each of the various possible combinations and permutations.
Unless otherwise specifically defined herein, all terms are to be given their broadest possible interpretation including meanings implied from the specification as well as meanings understood by those skilled in the art and/or as defined in dictionaries, treatises, etc.
It must also be noted that, as used in the specification and the appended claims, the singular forms “a,” “an,” and “the” include plural referents unless otherwise specified.
In one general embodiment, an aerogel or xerogel, includes column structures including a material, the column structures having minor pores therein and major pores devoid of the material positioned between the column structures, with longitudinal axes of the major pores being substantially parallel to one another.
In another general embodiment, a method includes heating a sol including aerogel or xerogel precursor materials to cause gelation thereof to form an aerogel or xerogel and exposing the heated sol to an electric field, wherein the electric field causes orientation of a microstructure of the sol during gelation, which is retained by the aerogel or xerogel.
In still another general embodiment, an aerogel or xerogel includes elongated major pores extending between a material arranged in column structures, each column structure having a plurality of minor pores therein, wherein a longitudinal axis of each of the elongated major pores are substantially parallel to a single axis, and wherein the aerogel or xerogel has structural characteristics of being formed from a sol exposed to an electric field that causes orientation of a microstructure of the sol during gelation which is retained by the elongated major pores of the aerogel or xerogel.
In operation 102, a sol, including aerogel or xerogel precursor materials is heated in order to cause gelation thereof and form and aerogel or xerogel. Any precursor materials may be used as would be known to one of skill in the art.
In one embodiment, the aerogel or xerogel precursor materials may include a mixture of resorcinol, formaldehyde, and a base or acid catalyst to facilitate a reaction between the resorcinol and the formaldehyde. Alternatively, the aerogel or xerogel precursor materials may include a mixture of alcohol, tetramethyl orthosilicate (TMOS), tetraethyl orthosilicate (TEOS), and an acid or base catalyst to facilitate a reaction between the alcohol and the TEOS and/or TMOS.
In another embodiment, the sol may comprise a plurality of particles, such as fluoroapatite, which in some embodiments may be electrically conductive. The plurality of particles may have a length of between about 1 μm and about 3 μm, and a width of between about 150 nm and about 500 nm, in one approach.
Subsequently, in operation 104, the heated sol is exposed to an electric field, causing orientation of a microstructure of the sol during gelation, which is retained by the aerogel or xerogel after gelation of the sol. The sol may be exposed to the electric field prior to being heated, while being heated, after being heated, and/or during all periods, in various embodiments, as understood by one having ordinary skill in the art upon reading the present descriptions.
In some embodiments, the plurality of particles, as described above, may remain in the aerogel or xerogel after gelation of the sol. In an alternate embodiment, the method 100 may comprise removing the plurality of particles from the aerogel or xerogel, such as through burning, purging, washing, or any other method of removal as would be understood by one of skill in the art.
According to some embodiments, major pores of the aerogel or xerogel may be aligned along a single axis consistent with the electric field, as described in more detail later.
In more embodiments, the microstructure of the aerogel or xerogel may comprise column structures having minor pores therein, the column structures being separated by major pores aligned with the electric field, as described in more detail later.
In some approaches, the electric field may include an alternating current (AC) field having an electric field strength of between about 100 V/cm and about 500 V/cm, such as a field strength of about 300 V/cm. Of course, other strengths and types of electric fields may be used as would be understood by one of skill in the art upon reading the present descriptions.
In more approaches, the electric field may alternatively or additionally include a bias direct current (DC) electric field having an electric field strength of between about 0.5 V/cm and about 10 V/cm, which may be applied during gelation of the sol. Of course, other strengths and types of electric fields may be used as would be understood by one of skill in the art upon reading the present descriptions.
For example, in one approach, an organic sol may, be formed by combining 1.5 g water, 1.25 g resorcinol, 1.8 g formaldehyde, and 44 μl acetic acid in solution. This solution may be simultaneously heated and subjected to an electric field of 300 V/cm until gelation completes. After gelation, the sample may be washed in acetone and dried in air at room temperature to obtain a finalized organic aerogel material with controlled pore morphology.
Although the final aerogel product may be obtained without supercritical drying, in ambient air, alternative approaches may additionally include converting the organic aerogel product to a carbon aerogel by pyrolization at temperatures exceeding about 600° C. in an inert, supercritical pressure environment. For example, carbonization of an aerogel formed using the process described immediately above may be accomplished by pyrolizing the organic aerogel at 1050° C. in a nitrogen environment.
While the preceding examples describe an organic aerogel comprising resorcinol-formaldehyde and, upon pyrolization, a carbon aerogel, other suitable materials such as silica, alumina, titania, or any other metal-oxide or material capable of carrying an electrostatic charge may also serve as the material of which the aerogel may be based.
In some specific embodiments, the aerogel or xerogel may comprise at least one of: a carbon aerogel or xerogel, a silica aerogel or xerogel, an alumina aerogel or xerogel, and a titania aerogel or xerogel.
According to one embodiment, an aerogel or xerogel 200 comprises column structures 202 comprising a material. Each of the column structures 202 have minor pores therein (too small to be seen in
For ease of understanding, in some embodiments, the minor pores may be defined as having a smaller median volume than the median volume of the major pores 204, e.g., the aerogel or xerogel 200 exhibits hierarchical porosity where two different dominant pore sizes exist, minor pores and major pores 204. Furthermore, the major pores 204 may be those pores in-between the column structures 202, and the minor pores may be those pores within each column structure 202, as would be understood by one of skill in the art. In some approaches, the longitudinal axis of each major pore 204 may be aligned along a single axis consistent with the electric field, e.g., each column structure 202 is aligned in a single direction.
According to one embodiment, the material may comprise at least one of: carbon, silica, alumina, and titania, or any other suitable material for use in an aerogel or xerogel, as would be understood by one of skill in the art.
In another embodiment, the aerogel or xerogel 200 may have structural characteristics of being formed from a sol exposed to an electric field that causes orientation of a microstructure of the sol during gelation which is retained by the aerogel or xerogel 200. This orientation of the microstructure, in some embodiments, is the column structures 202 and major pores 204 therebetween. In a further embodiment, the aerogel or xerogel 200 may have structural characteristics of being formed from a sol having a plurality of particles therein which are caused to move in a direction consistent with the electric field. This is described in more detail later.
In further embodiments, the material may retain the plurality of particles after formation thereof. In one embodiment, the plurality of particles may include fluoroapatite, e.g., Ca5(PO4)3F, and in some embodiments may be electrically conductive. Of course, other sizes and/or types of particles may be used as would be understood by one of skill in the art upon reading the present descriptions.
In another embodiment, the particles may have a length of between about 1 μm and about 3 μm, and a width of between about 150 nm and about 500 nm. This particle size range may provide for well defined column structures, and may prevent the column structures from clumping, exceeding a useable width, or forming in contact with each other, which would degrade or otherwise ruin or destroy the product formed, as the porosity of the final product would not be representative of an aerogel or xerogel.
In another approach, the aerogel or xerogel 200 may have structural characteristics of being formed in a process that does not use templating. As described previously, templating adds a cumbersome step to the process of aerogel or xerogel formation, and therefore any way of eliminating this step is beneficial.
SEM analysis of carbon aerogels formed using the techniques described herein according to various embodiments shows that the microstructure of the aerogel cured in the electric field may be very different from that of the aerogel cured without any electric field present. In particular, without the use of any template, the pores in the aerogel cured in the electric field are all aligned along a single axis, while the microstructure of a traditional aerogel is random in nature unless applied using a template. These properties may be referred to as structural characteristics of the aerogel or xerogel being formed in an electric field, which may be accomplished without the use of templating.
According to one embodiment, these characteristics may include escaping the limitations of a templating material's shape and/or structure. In other embodiments, these structural characteristics may include elongated major pores devoid of material between column structures of the material, where the longitudinal axes of the major pores are substantially parallel to the longitudinal axes of the column structures.
In one embodiment, an aerogel or xerogel comprises elongated major pores extending between a material arranged in column structures, each column structure having a plurality of minor pores therein. A longitudinal axis of each of the elongated major pores are substantially parallel to a single axis, and the aerogel or xerogel has structural characteristics of being formed from a sol exposed to an electric field that causes orientation of a microstructure of the sol during gelation which is retained by the elongated major pores of the aerogel or xerogel.
According to one approach, the material comprises at least one of: carbon, silica, alumina, and titania, or any other suitable material.
In another approach, the material may comprise a plurality of particles having a length of between about 1 μm and about 3 μm, and a width of between about 150 nm and about 500 nm, such as particles of fluoroapatite. In more approaches, the plurality of particles may be electrically conductive.
In yet another approach, the aerogel or xerogel may have structural characteristics of being formed from a sol having a plurality of particles therein which are caused to move in a direction consistent with the electric field. In a specific approach, the aerogel or xerogel may have structural characteristics of being formed in a process that does not use templating.
In particular, in some embodiments, the microscale interconnecting pore network may be comprised of the gaps between the column structures, with the nanoscale porosity being primarily comprised within the column or trabecular microstructure of the aerogel or xerogel, according to some embodiments.
In further embodiments, additional benefits of the sol-gel production methods as described herein may include improved nanostructure resistance to radiation damage since damage sites within materials can easily and quickly migrate to surfaces and thus relieve stresses and gas build up in the matrix. Nanostructures may thus have tailored porosities and densities that enable optimization of radionuclide production and/or release rates.
Additionally, the ability to template sol-gel produced materials around micro- to macro-scale removable templates has been developed. In one exemplary embodiment, as shown in
Upon removing the scaffolding material, according to one embodiment, the aerogel or xerogel may exhibit a highly organized porous architecture, as depicted in
Alternatively, the scaffolding material may be a dopant or catalyst capable of interacting with compositions of matter coming into proximity or contact with the aerogel or xerogel. In these embodiments, the scaffolding material may remain embedded within the aerogel or xerogel structure in order to facilitate subsequent interactions.
In some embodiments, the aerogels and/or xerogels may be expanded to more complicated macro-scale geometries, for example using a removable template with a fractal structure such as those typical in bronchiolar passages.
Furthermore, application of an electric field during the gelation step of the sol-gel process may induce textured porosity aligned with the field, according to other embodiments. This alignment may be utilized to create anisotropic transport rates to optimize radionuclide release.
The methods and systems described herein are particularly useful in a variety of fields and applications. In one exemplary application, an aerogel or xerogel exhibiting controlled pore morphology may serve as a scaffold for biofunctionalization applications. For example, labeled nanoparticles, such as fluorescent or dye-doped nanoparticles and luminescent quantum dots, may be deposited along the porous microstructure and serve as probes for detecting biomolecules or organisms, with high resolution and specificity.
In another application, an aerogel or xerogel may facilitate culturing of microorganisms by depositing microorganisms along, for example, a carbon aerogel electrode exhibiting the presently described columnar structures with microporous channels existing therebetween. Researchers may then facilitate the growth, metabolism, reproduction, or other similar biological processes of the deposited organisms by providing desired substances thereto along the microporous channels with the assistance of electric fields. Similarly, researchers may employ the same channels and fields to collect biomolecules and other metabolites produced and/or secreted by organisms deposited on the porous latticework.
In some embodiments, microporosity between columnar and/or trabecular structures along the longitudinal axis of the aerogel or xerogel may facilitate mass transport along the same axis, resulting from decreased collision rates along the micropore structure. In addition, these structures permit mass transport at decreased pressures relative to structures exhibiting random porosity. Similarly, other mass transport applications may include facilitating movement of fluids capacitors, batteries, for filtration, etc.
In some embodiments, a column structure may be controlled at multiple length scales, concurrently optimizing surface area for nucleation sites, reaction sites, and bulk mass transport.
According to more uses, rare isotope beam (RIB) targets must withstand extreme operating conditions, and current methods produce crystals typically capable of withstanding such conditions for only a limited duration of approximately one to two weeks, frustrating efficient and smooth research operations in many isotope mass separation online (ISOL) facilities. By using the material production methods disclosed herein to engineer both the microstructure and macrostructure of targets, researchers may improve the performance of ISOL facilities with carbo-thermal reduction of composite monolith targets, leading to high surface area carbide foams with high temperature stability capable of outperforming current RIB targets.
In additional embodiments, the materials produced using the methods described herein may be tested for temperature stability and thermal conductivity prior to online testing at various ISOL facilities, while optimizing radionuclide release rates due to the ability to tailor the microstructures and macrostructures of the targets.
While various embodiments have been described above, it should be understood that they have been presented by way of example only, and not limitation. Thus, the breadth and scope of a preferred embodiment should not be limited by any of the above-described exemplary embodiments, but should be defined only in accordance with the following claims and their equivalents.
This application claims priority to U.S. Provisional Patent Application No. 61/376,484 filed on Aug. 24, 2010, and which is herein incorporated by reference.
The United States Government has rights in this invention pursuant to Contract No. DE-AC52-07NA27344 between the United States Department of Energy and Lawrence Livermore National Security, LLC for the operation of Lawrence Livermore National Laboratory.
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| Number | Date | Country | |
|---|---|---|---|
| 20120052511 A1 | Mar 2012 | US |
| Number | Date | Country | |
|---|---|---|---|
| 61376484 | Aug 2010 | US |
