Patent Application
20060100088
The invention relates to a method of making a multi-cation ceramic. The invention also relates to a method of making a transparent multi-cation ceramic. More particularly, the invention relates to a method of making a transparent and grain-size engineered multi-cation ceramic through the use of nanopowders and their enhanced sintering ability.
Multi-cation ceramics—specifically transparent multi-cation ceramics—are widely used in lighting, medical, industrial, homeland security, and defense applications. For example, transparent ceramic scintillators, such as yttrium aluminium garnet (YAG) with dopants find applications in imaging, non-destructive evaluation, and sensors. Alumina, yttria, YAG, Aluminum oxynitride, and magnesium aluminate spinel are good candidates for lighting, automotive, and harsh environment windows. Consequently, efforts have been directed towards producing transparent ceramics of these and other materials. For many of these applications it is desirable to have high strength and machinablity.
Transparent ceramics are typically made by pressure sintering micron and sub-micron size powders. Generally, micron-size ceramic powders of the desired phase are synthesized by solid-state routes, compacted, and sintered to form transparent ceramic articles. It is difficult to limit or control the grain size during high pressure sintering processes. Alternatively, synthesis of ceramic nanopowders may be achieved by wet chemical routes, followed by compaction and sintering. In both of these two step-processing methods, controlling grain growth is difficult, and only limited success in obtaining dense, fine-grained ceramics has been achieved.
In single step-processes, it is difficult to achieve both phase formation and sintering while limiting grain growth during processing, due to the inherent problems associated with nanopowders. One such problem is the strong agglomeration of the nanocrystallites within the nanoparticles. Another problem is the tendency of nanopowders to resist compaction due to electrostatic repulsion between nanoparticles. These effects lead to loose packing of particles, low density, and high levels of porosity in a green body. In a single step process, achieving dense compaction is even more challenging, as a suitable combination of surfactants to enable simultaneous surface modification of different reactants may be needed to achieve uniform and homogeneous packing of the green body. Another challenge is controlling rapid grain growth associated with the enhanced reactivity of nano materials. Generally, grain growth inhibitors are used to overcome this problem, but they may have adverse effects on the optical and mechanical properties of the final product. In addition, pores tend to be trapped within the nanoparticles during sintering, yielding ceramic bodies with high scattering coefficients and poor mechanical properties.
The approaches in the prior art to these problems have produced only limited success. Therefore, what is needed is a versatile and simple processing technique to fabricate transparent and grain-size engineered ceramics.
The present invention meets these and other needs by providing a transparent multi-cation ceramic material and a method for making a multi-cation ceramic material in a single step process.
Accordingly, one aspect of the invention is to provide a method of making a multi-cation ceramic material. The method comprises the steps of: providing at least a first material and a second material, wherein the first material comprises a first cation and the second material comprises a second cation, and wherein the first cation and the second cation are different from each other and each of the first material and the second material are nanopowders; forming a mixture comprising the first material and the second material; forming a green body from the mixture; and forming a dense multi-cation ceramic material comprising the first cation and the second cation, wherein the dense multi-cation ceramic material comprises a major phase that is different from the first material and the second material and has an average grain size of less than 1 micron.
A second aspect of the invention is to provide a method of making an article comprising a multi-cation ceramic material. The method comprises the steps of: providing at least a first material and a second material, wherein the first material comprises a first cation and the second material comprises a second cation, wherein the first cation and the second cation are different from each other and each of the first material and the second material are nanopowders; forming a slurry comprising the first material, the second material, at least one dispersant, and a solvent; mixing the slurry to form a mixture comprising the first material and the second material; drying the slurry to form a powder; forming a green body from the powder; sintering the green body at a controlled pressure to form a sintered body; and finishing the sintered body to form the article, wherein the article comprises a major phase comprising the first cation and the second cation, and wherein the major phase is different from the first material and the second material and has an average grain size of less than 1 micron.
A third aspect of the invention is to provide a method of making an article comprising a multi-cation ceramic material. The method comprises the steps of: providing at least a first material and a second material, wherein the first material comprises a first cation and the second material comprises a second cation, wherein the first cation and the second cation are different from each other and each of the first material and the second material are nanopowders; forming a slurry comprising the first material, the second material, at least one dispersant, and a solvent; mixing the slurry to form a mixture comprising the first material and the second material; drying the slurry to form a powder; forming a green body from the powder; sintering the green body at a controlled pressure to form a sintered body; and finishing the sintered body to form the article, wherein the article comprises a major phase comprising the first cation and the second cation, wherein the major phase is different from the first material and the second material and has an average grain size of less than 1 micron and is transparent, and wherein the article has a specular transmission of at least 50% normalized to a 1 mm thick specimen. A fourth aspect of the invention is to provide a ceramic material. The ceramic material comprises a major phase. The major phase comprises at least a first cation and a second cation, wherein the first cation and the second cation are different from each other, and has an average grain size of less than 1 micron. The ceramic material is transparent and has a specular transmission of at least 50% normalized to a 1 mm thick specimen. Yet another aspect of the invention is to provide a ceramic article. The ceramic article comprises a major phase. The major phase comprises at least a first cation and a second cation, wherein the first cation and the second cation are different from each other, and has an average grain size of less than 1 micron, wherein the ceramic article is formed by a method including the following steps: providing at least a first material and a second material, wherein the first material comprises a first cation and the second material comprises a second cation, wherein the first cation and the second cation are different form each other and wherein each of the first material and the second material are nanopowders; forming a slurry comprising the first material, the second material, at least one dispersant, and a solvent; mixing the slurry to form a mixture comprising the first material and the second material; drying the slurry to form a powder; forming a green body from the powder; sintering the green body at controlled pressure to form a sintered body; and finishing the sintered body to form the ceramic article.
These and other aspects, advantages, and salient features of the present invention will become apparent from the following detailed description, the accompanying drawings, and the appended claims.
In the following description, like reference characters designate like or corresponding parts throughout the several views shown in the figures. It is also understood that terms such as “top,” “bottom,” “outward,” “inward,” and the like are words of convenience and are not to be construed as limiting terms. Furthermore, whenever a particular aspect of the invention is said to comprise or consist of at least one of a number of elements of a group and combinations thereof, it is understood that the aspect may comprise or consist of any of the elements of the group, either individually or in combination with any of the other elements of that group.
In the following discussion, for simplicity Y3Al15O12 is denoted as YAG, YAG with neodymium doping is denoted as YAG:Nd, YAG with ytterbium doping is denoted as YAG:Yb, and YAG with neodymium doping and magnesium additive is denoted as YAG:Nd, Mg. For the purposes of understanding the invention, a nanopowder is understood to be a powder in which the primary crystallite size is less than 500 nm and the average particle size is below 1 micron. In one embodiment, the primary crystallite size is less than 100 nm and, in another embodiment, the primary crystallite size is less than 60 nm. In one embodiment, the average particle size is less than 500 nm, and, in another embodiment, less than 100 nm.
There is a large demand for transparent materials across a range of technological and industrial applications. Traditionally, single crystals are used for this purpose. Transparent polycrystalline ceramics are highly desirable for these applications because, when compared to single crystals, they allow the use of lower concentrations of dopants, higher concentrations and uniformity of optical activators, and have lower processing temperatures. In addition, polycrystalline ceramics allow near-net or net shape fabrication and molding of articles. This cannot be achieved using single crystals. However, preparing polycrystalline ceramics having high transparency is a challenging task, as polycrystalline ceramics have a large number of scattering centers, such as pores, possible multiple second phases, and defects at grain boundaries. A high degree of transparency can be achieved either in a high-density ceramic having an extremely low residual porosity, or in a ceramic where the length scale of at least one of the porosity and any second phases present are below the scattering regime considered. In recent years, efforts to synthesize high density, transparent ceramics of high transparency and to develop versatile methods for making transparent ceramics have been made. Hot pressing techniques have been used to obtain transparent ceramics. However, the operations involved in producing transparent ceramic articles using such a method are very complex and potentially costly.
Pressureless sintering can be used to make transparent ceramics by considerably increasing the specific surface area and decreasing the particle size of the starting reactant particles. Even though this method may provide transparency, it tends to yield ceramic bodies having large grain sizes, which adversely affect mechanical strength. Despite such efforts, there is no method to easily produce high-density transparent ceramics having engineered fine grain sizes on an industrial scale. Disclosed herein is a versatile method for making transparent, high-density multi-cation ceramics with controlled grain size.
Referring to the drawings in general and to
One aspect of the present invention is to provide a method of making an article comprising a multi-cation ceramic material. The method of making a multi-cationic ceramic is shown as a flow diagram in
The method 100 summarized in
In step 120, a mixture comprising the first material and the second material is formed. The step of forming a mixture comprising the first material and the second material may comprise either wet mixing or dry mixing. Wet mixing comprises forming a slurry comprising the first material, the second material, and a solvent. Either aqueous or nonaqueous solvents may be used. Nonaqueous solvents may be either polar or nonpolar solvents. In one embodiment, the polar solvent is an alcohol. Nonpolar solvents such as alkanes and alkenes may also be used. Non-limiting examples of nonpolar solvents include hexane, toluene, carbon tetrachloride and the like. Liquids having low surface tension are preferred solvents, as high surface tension promotes agglomeration. Strong agglomerates lead to poor packing of the particles in the green body, which in turn produces low density and porosity in the in the final sintered body.
In another embodiment, the step of forming a slurry comprises adding a dispersant to the slurry. The dispersant effectively disperses the reactant powders in the slurry and has no significant deleterious effect on the sintered product. Non-limiting examples of dispersants include, but are not limited to, sodium polyacrylates, ammonium polyacrylates, ammonium polymethacrylates, polyvinyl alcohols, alkyl stearates, organo-phosphates, alkyl ammonium bromide salts, block copolymers, combinations thereof, and the like. Generally, from about 1.0 to 10.0 pph (parts per hundred parts solvent) of dispersants are provided.
If dry mixing is involved, any of the dry mixing methods known in the art such as fluid energy mixing, vibratory mixing, static mixing, jet milling, ball milling and the like may be used. Alumina, zirconia, yttria stabilized zirconia, agate, nylon, silicon nitride, or Teflon® may serve as the milling media.
If wet mixing is used, the mixture is dried to form a dried mixture. Non-limiting examples of drying methods that may be used include, but are not limited to, temperature-assisted drying, spray drying, freeze drying, and reduced pressure drying of the mixture. The drying method is chosen so as to produce a dried mixture. In step 130, a green body is formed from the dried mixture. A number of techniques can be used to form the green body, such as, but not limited to, compacting under uniaxial pressure, biaxial pressure or isostatic pressure. Net-shape or near net-shape fabrication by techniques such as extrusion, injection molding, slip casting, and gel casting may also be used. In one embodiment, the green body has a density of at least about 40% of the theoretical density of the major phase of the multi-cation ceramic material and, in another embodiment, at least about 50% of the theoretical density to promote further densification during sintering and achieve the desired optical transmission.
In step 140, a dense ceramic body is prepared by densifying the green body. In one embodiment, the green body is sintered in a controlled -atmosphere and under a controlled pressure. In another embodiment, the green body is pre-fired in an oxygen-containing atmosphere at a temperature below about 1000° C. Pre-firing is generally carried out at a temperature in a range from about 500° C. to about 1000° C. to burn off organic binders and surfactants. The pre-firing temperature and time cycle that are actually used depend on the level of organic impurities present and the thickness of the ceramic samples. Following the pre-sintering step, the sintering process is carried out. Sintering may be conducted in or under reduced pressure (vacuum), ambient air, inert gas, reducing gas, oxidizing gas, or mixtures of such gases. Non-limiting examples of inert gases include, but are not limited to, argon and helium. Reducing gases include but are not limited to, dry or wet H2, N2, and CO/CO2 mixtures. Oxidizing gases include, but are not limited to, O2 and O3. Generally, sintering is conducted at a temperature in a range from about 1000° C. to about 2100° C. for a time ranging from 0.5 h to 24 h. The rate of heating to the sintering temperature may vary and should have no significant deleterious effect on the green body. Generally, heating rates are in a range from about 1° C./min to about 10° C./min. The controlled pressure used for sintering is in a range from about 10−8 torr to about 1.6×106 torr. Sintering in an ambient atmosphere with high diffusivity in the ceramic matrix is preferred to achieve high density. Sintering conditions are chosen to achieve a desired density and grain size, and depend on the particular materials system and thickness of the samples. Sintering conditions are also chosen to achieve complete pore filling, densification to a desired density value, and to confine the final grain size.
Sintering is optimized to enable simultaneous formation and sintering of the multi-cation ceramic with an average grain size of less than 1 micron. This is possible due to the enhanced sintering ability of the reactant nanopowders. The method of the present invention provides engineering of grain sizes and also provides means to limit the grain sizes to less than 1 micron in the final dense body.
Typically, the sintered body comprises the product multi-cation major phase, which is different form the constituent reactants, as determined by x-ray diffraction and electron microscopy measurements. In one embodiment, the major phase is one of an oxide, a boride, a carbide, a nitride an oxynitride, and combinations thereof. In one particular embodiment, the major phase is one of YAG, YAG:Nd, YAG, YAG:Yb and YbAG. In one embodiment, the sintered body has a density in a range from about 95% to 100% of the theoretical density of the major phase of the multi-cation ceramic material. In a second embodiment the sintered body has a density in a range from about 98% to 100% of the theoretical density and, in a third embodiment the sintered body has a density in a range from about 99% to 100% of the theoretical density. The sintered body generally has a grain size in a range from about 100 nm to about 3 microns. In one embodiment, the sintered body has an average grain size in a range from about 100 nm to about 2 microns, and, in another embodiment, in a range from about 100 nm to about 1 micron.
The processing of nanopowders presents many challenges, such as deagglomeration of powders, achieving high packing density in the green compact with controlled pore size and structure, and controlling grain size to achieve fine-grained ceramics having high mechanical strength. Because of their increased surface energy, primary nanocrystallites have a strong tendency to agglomerate into larger nanoparticles. These nanoparticles offer resistance to compaction due to increased electrostatic repulsion. The methods of the present invention successfully provide solutions to these problems and provide means of achieving high-density multi-cation of fine grain sizes.
Turning to
In one embodiment, the multi-cation ceramic is transparent. In one particular embodiment, the multi-cation ceramic is transparent to infrared radiation. In another embodiment, the multi-cation ceramic is transparent to ultraviolet radiation. In yet another embodiment, the multi-cation ceramic is transparent to visible light; i.e., in the optical wavelengths between about 400 nm and about 800 nm.
Referring to
The term ‘in-line transmission’ as used herein is understood to mean the ratio of the intensity of transmitted light to the intensity of incident light, obtained when a parallel beam of light of a certain intensity is incident perpendicular to the surface of a sample of given thickness. In the present embodiment, the in-line spectral transmission is determined on a polished plate of sintered body having a thickness of 1 mm at a wavelength of 554 nm.
The present invention makes it possible to fabricate simple, hollow, or complex-shaped multi-cation ceramic articles directly. Specifically, the sintered product can be produced in the form of useful ceramic articles such as plates, thin-walled tubes, long rods, spherical bodies, hollow shaped articles, and the like without significant or substantial machining.
In a particular embodiment, method 180, shown as a flow chart in
The multi-cation ceramic described herein may have a wide variety of uses. For example, it may be useful in any system where a ceramic protective material or a plate having the present light-transmitting properties is needed. Specifically, it may be useful as a light-transmitting filter; a light emitting scintillator, when exposed to high-energy radiation, for medical imaging; industrial and non-destructive evaluation; passive and active screening of baggage and containers; light transmitting windows; lamp envelopes; etch-resistant windows for industrial applications; high-temperature, high-strength composites; and damage tolerant composites for transparent armor.
The following example serves to illustrate the features and advantages offered by the present invention, and not intended to limit the invention thereto.
The following example describes the preparation method for transparent YAG Material, Y3Al5O12. Stoichiometric amounts of Y2O3 and Al2O3, corrected to account for ignition losses at high temperatures, were mixed with Tetraethylorthosilicate, deionized water, and dispersants ammonium polyacrylate, ammonium polymethacrylate, styrene, and acrylic copolymers alumina (Al2O3) spheres served as the grinding media. The material was shaken and then placed on a ball mill for 15 hr to form a suspension. The suspension was defoamed with 3 drops of octanol, and separated from the media by pouring through a sieve cap. The media was rinsed with additional deionized water and stirred with a magnetic stirrer, and the suspension was then spray dried at an inlet temperature of about 200° C. The dried material was collected from the cyclone collector and the spray chamber. The resulting powder was pressed into pellets using a die in a hydraulic press. The pellets were then placed in a watertight latex sleeve and cold isostatic pressed at 40 kpsi pressure to obtain pieces that were about 50% dense. The pieces were then heated in a box furnace under flowing O2 to burn off the organic binders and surfactants. The pre-sintering firing occurred at 900° C. with three intermediate steps. The pieces were cooled at 200° C./hr and then sintered at 1750° C. under vacuum to obtain near 100% dense pieces.
While typical embodiments have been set forth for the purpose of illustration, the foregoing description should not be deemed to be a limitation on the scope of the invention. Accordingly, various modifications, adaptations, and alternatives may occur to one skilled in the art without departing from the spirit and scope of the present invention.
