Patent Application
20170073530
This patent document relates to systems, devices, and processes that use optical to electrical energy conversion based on nanoscale material designs.
Nanotechnology provides techniques or processes for fabricating structures, devices, and systems with features at a molecular or atomic scale, e.g., structures in a range of one to hundreds of nanometers in some applications. For example, nano-scale devices can be configured to sizes similar to some large molecules, e.g., biomolecules such as enzymes. Nano-sized materials used to create a nanostructure, nanodevice, or a nanosystem can exhibit various unique properties, e.g., including optical properties, that are not present in the same materials at larger dimensions and such unique properties can be exploited for a wide range of applications.
Techniques, systems, devices and materials are disclosed for solar-absorbing coatings with ultra-high optical performance, including highly-scalable, low-cost fabrication processes to manufacture the solar energy-absorbing coatings of the disclosed technology. In some implementations, the coatings include nanoparticles (NPs) of black oxides deposited on high-temperature metal alloy surfaces, e.g., which can be in the form of standalone NPs or NPs embedded in a dielectric ceramic matrix.
The systems, devices and techniques disclosed in this patent document provide for synthesized Co3O4 black oxide nanoparticles using a facile hydrothermal process and novel designs and fabrication processes of light-absorbing coating structure for high-temperature CSP systems. By introducing sacrificial polymer fillers into the nanopowder-based coating slurry, the surface texturing can be successfully obtained and the optical performance can be enhanced, as measured by a high figure of merit of 88.2%. For high temperature durability, a long-term aging test can be performed to show that the light-trapping structure remains intact after 750° C. exposure in air for 1,000 hours. Consequently, the FOM shows negligible change after the 1,000-hour exposure. The textured Co3O4 coating is a promising candidate for solar absorbing in next-generation high-temperature CSP systems. The Co3O4 layer can easily be spray-coated in a manner suitable for large-scale CSP receiver applications.
In one aspect, an optically selective coating includes a substrate including a solar energy absorbing material; and a nanostructure material formed over the substrate to absorb solar energy in a selected spectrum and reflect the solar energy in another selected spectrum.
The coating can be implemented to include one or more of the following features. The nanostructure material can include metal oxide nanoparticles embedded in a dielectric matrix material. The metal oxide nanoparticles can include black oxide nanoparticles and the dielectric matrix material can include ceramic, glass, or silica. The metal oxide nanoparticles can include Mn—Zn ferrites, Co ferrites, Co oxides, or Cu oxides. The metal oxide nanoparticles can include black oxides having an average nanoparticle size of 900 nm or less. The average nanoparticle size can be less than 500 nm. The average nanoparticle size can be less than 300 nm. The metal oxide nanoparticles can include Cu—Cr—O oxides. The Cu/Cr ratio can be substantially 1/2. The Cu/Cr ratio being substantially 1/2 can include 1±0.3/2±0.3. The Cu/Cr ratio being substantially 1/2 can include 1±0.15/2±0.15. The metal oxide nanoparticles can include Cu—Fe—Mn—O oxides. The Cu/Fe/Mn ratio can be substantially 1/1/1. The Cu/Fe/Mn ratio being substantially 1/1/1 can include 1±0.3/1±0.3/1±0.3. The Cu/Fe/Mn ratio being substantially 1/1/1 can include 1±0.3/1±0.3/1±0.3.
The coating can be implemented to include one or more of the following features. The nanostructure material can include nanorods. The nanostructure material can include a core-shell structure coated with nanoparticles. The core-shell structure can include yttrium oxide (Y2O3) nano-shell. The nanostructure material can include thermally resistant core-shell particles having semiconductor, metal and metal oxide as cores. The thermally resistant core-shell particles can include Fe3O4-Yttria, SiGe-Yttria, or Metal-Yttria core-shell nanoparticles. The coating can include an antireflection layer disposed over the nanostructure material. The nanostructure material can include Co Oxide and the antireflection layer can include MgF2. The nanostructure material can include embedded hole patterns. The nanostructure material can include polymer beads. The nanostructure material can include a double layer coating structure. Both layers of the double layer coating structure can be nonporous. Top layer of the double layer coating structure can be porous and bottom layer can be nonporous. The top layer can include CuFeMnO4 and the bottom layer include CuCr2O4.
In another aspect, a method of fabricating an optically selective coating includes providing a substrate that includes a solar energy absorbing material. The method includes forming a coat of nanostructure material over the substrate with the nanostructure material configured to absorb solar energy in a selected spectrum and reflect the solar energy in another selected spectrum. The forming includes performing one or more of hydrothermal, spark erosion, mechanical pulverization, or atomization.
The method can be implemented in various ways to include one or more of the following features. The nanostructure material can include at least one of semiconductor material including at least one of silicon (Si), germanium (Ge), SiGe, silicon boride, metal silicides, PBTe, PbSc, or PbS. The method can include creating a roughened surface on the coat of nanostructure material formed over the substrate. Creating the roughened surface can include incorporating and subsequently removing micron-sized sacrificial polymeric beads within the coat of nanostructure material. Creating the roughened surface can include introducing microfabricated patterns on the coat of nanostructure material. Forming the coat of nanostructure material over the substrate can include forming a double layer coating structure. Forming the double layer coating structure can include forming two nonporous layers. Forming the double layer coating structure can include forming a porous layer over a nonporous layer.
In another aspect, a concentrating solar power (CSP) system includes heat transfer fluids (HTFs); thermal energy storage system (TES); and a solar receiver in communication with HTFs, the solar receiver including a light absorbing coating layer based on cobalt oxide nanoparticles.
The CSP system can be implemented in various ways to include one or more of the following features. The solar receiver including the light absorbing coating layer based on cobalt oxide nanoparticles can be configured to raise the temperature to above 700° C. The cobalt oxide nanoparticles have a diameter in 100s of nanometers. The light absorbing coating layer can include cobalt oxide nanopowders dispersed in silica matrix, and depositing on metal substrates via a spray coating process. The solar receiver can include black oxide coated alloy tubes. The light absorbing coating layer can include Cu—Cr—O or Cu—Fe—Mn—O oxides.
In another aspect, a hydrothermal method of synthesizing cobalt oxide nanoparticles includes introducing a solution of sodium hydroxide (NaOH) with a solution of cobalt chloride salt to induce precipitation of cobalt hydroxide. The hydrothermal method includes performing hydrothermal process to transform the precipitated cobalt hydroxide into cobalt oxide particles. The hydrothermal method includes washing the cobalt oxide particles. The hydrothermal method includes annealing the washed cobalt oxide particles for phase separation.
The hydrothermal method can include mixing annealed cobalt oxide particles with a SiO2 matrix.
Concentrated solar power (CSP) systems can convert concentrated sunlight into thermal energy (e.g., heat) by using solar absorbers. For higher Carnot efficiency of the power generation system, the desirable temperature of the HTF (heat transfer fluid) is 600° C. or higher, e.g., as the solar absorber temperature is higher than the HTF temperature.
For efficient operation, the solar absorber has to effectively absorb the solar energy in the solar wavelength spectrum (e.g., 0.4-2.5 μm range). In particular, for example, for solar thermal systems operating at high temperature, which is envisioned for future CSP systems such as solar towers, the solar absorbing coating also need to possess excellent durability at high temperature (e.g., above 600° C.) and oxidation resistance in air. It is desirable that the performance of the coating layer should not degrade significantly during the lifetime of the CSP systems, which is greater than 30 years. Even for absorbers placed inside evacuated enclosure, high temperature stability in air is still a very important metric because degradation of the absorbing coating could occur when the vacuum fails. In addition, it is expected that coating and its adhesion to the substrate must withstand more than 10,000 thermal cycles (e.g., from ˜200° C. to >600° C.) due to the intermittent nature of solar irradiation. Finally, it is desirable to make the coating with inexpensive starting materials and low-cost and scalable processes.
An ideal solar absorbing coating that possesses all the aforementioned metrics would not only directly reduce the initial and O&M cost of solar receivers, but also enable higher operating temperature of the power cycles, which means higher thermal-electricity conversion efficiency and lower overall system cost. Therefore, solar absorbing coatings have a significant impact on the performance/cost of the CSP technology, and are recognized as one of the potential opportunities for levelized cost of energy (LCOE) cost reduction in the roadmap for CSP power tower technology.
The figure of merit (FOM) of a solar absorbing coating can be defined as,
where R(λ) is the measured spectral selectivity, IQ) is the spectral solar radiance per square meter as defined by ASTM G173, B(λ,T) is the spectral thermal emission of a black body, and C is the concentration ratio (e.g., number of suns, or ratio of reflector area to absorber area). The temperature of the receiver (and therefore black body) is assumed to be 750° C. In practice, for example, all integrals are evaluated in the range of 300 nm-20 μm, as only negligible quantities of solar power are present outside this range. Eq. (1) shows that the FOM depends on the concentration ratio (C) and the temperature of the absorber (T).
Conventional state-of-the-art solar absorbing materials for high concentration ratio and high-temperature operation can include Pyromark 2500. For example, Pyromark 2500 is a silicone-based high-temperature paint that has been used on central receivers to increase solar absorptance. In the past, Pyromark 2500 high-temperature paint has been used on central receivers, including the Solar One Central Receiver Pilot Plant. The manufacturer of Pyromark 2500, Tempil, states that Pyromark 2500 resists temperatures up to 1093° C. (2000° F.) and can be applied on steel, aluminum, alloys, and ceramics. Pyromark 2500 has a very high solar absorptance (˜0.96), but it also has a very high thermal emittance (>0.8) at the temperatures of interest (>600° C.).
Table 1 shows the FOM of Pyromark 2500 under different irradiance (Irradiance=C.I) and receiver temperature (T). It can be seen that the FOM of Pyromark is quite high. For example, at 700° C. receiver temperature with 106 W/m2 irradiance (or 1000 sun), the FOM is 0.91. The FOM is considerably lower than the solar absorptance (0.95) because of the high thermal emittance (>0.80).
Despite its high FOM, Pyromark tends to degrade at high temperature. For example, it was reported that the solar absorptance decreased 3% from an initial value of 0.97 after 300 h of aging at 750° C. and after 20 h of aging at 850° C. Therefore, during CSP operation, the receiver coating has to be repaired after every 1-3 years, which represent a significant O&M cost. It is thus apparent that solar absorbing materials with high FOM and excellent durability at high temperature are needed to reduce the LCOE of CSP systems.
Techniques, systems, devices and materials are disclosed for solar-absorbing coatings with ultra-high optical performance, including highly-scalable, low-cost fabrication processes to manufacture the solar energy-absorbing coatings of the disclosed technology. In some implementations, the coatings include nanoparticles (NPs) of black oxides deposited on high-temperature metal alloy surfaces, e.g., which can be in the form of standalone NPs or NPs embedded in a dielectric ceramic matrix. The nanoparticles can include at least one of silicon (Si), germanium (Ge), SiGe, silicon boride, PbTe, PbSe, PbS, silicon boride, or metal silicides.
The disclosed technology employs a highly scalable, low cost process to make the solar absorbing coating with ultra-high optical performance. The solar absorbing coating is based on nanoparticles (NPs) of black oxides deposited on high-temperature metal alloy surfaces, e.g., either in the form of standalone NPs or embedded in a dielectric ceramic matrix. The exemplary NPs can be fabricated by a variety of processes, including ‘spark erosion’ or ‘hydrothermal’. The solar absorbing coating material can be applied onto solar receivers by low cost coating processes such as spray coating.
In some implementations, for example, first, black oxide particles with appropriate size (˜100 nm) are fabricated by hydrothermal. The use of other nanoparticle synthesis methods such as spark erosion, mechanical pulverization, atomization, etc. to provide the desired nanoparticle size and shape are not excluded for this method. Exemplary materials include black oxides, e.g., including Mn—Zn ferrites, Co ferrites, and Co oxides. Other forms of oxides, e.g., including CrO2, MnO2, CuO can be used. Table 2 shows a list of possible candidates of black oxides suitable for this application, along with their optical bandgap and melting points.
Second, for example, these exemplary NPs are then coated onto solar receiver surface. The coating can be accompanied with water or organic solvent that is eventually dried, or with dielectric materials such as SiO2 or other types of oxides. The coating can be done with spin coating, drop casting, spray coating, inkjet printing, and other forms of coating processes.
Followed by the coating process, for example, a curing process can be used to dry the water or organic solvents and harden the matrix material.
Exemplary implementations of the methods were performed to produce exemplary solar absorbing coatings. In the exemplary implementations, for properly chosen materials and morphology, the exemplary measurement and simulation results showed that such a nanoparticle based solar absorbing coating structure can achieve a high FOM of 0.88 or higher. Moreover, solar absorbing coatings made from some of the black oxide NPs were shown to be durable at temperature (e.g., up to 750° C.), stable after thermal cycling, and resistance to oxidation at high temperature.
Table 2 shows some exemplary materials based on desirable optical properties and bandgaps. For example, metal oxides with low band gap is necessary to achieve higher absorption of sun light from UV to NIR spectrum range because the solar spectrum with higher energy than the bandgap can be absorbed into the metal oxides to be used for exciting electron from valence band to conduction band. And metal oxide type of semiconductor is more recommended for CSP application rather than metalloid semiconductors because those metalloid semiconductors such as silicon proved to be thermally unstable at high temperature operation which is from 400° C. ° to 750° C. used in CSP power plant. For example, some metal oxides were reviewed to apply for the light receiver materials with higher absorption, as shown in Table 2.
As exemplary candidates for higher absorption materials, CrO2 and MnO2 are appropriate based on their very low band-gap energies. But their melting temperature may be too low to be applied for high temperature operation. Fe3O4 also has high solar absorption, but it can be easily converted to Fe2O3 by thermal oxidation at target temperature (750° C.) in air atmosphere. NiO looks black at room temperature which means the high absorption of visible light, but it also changes the color from black to green when heated up to 750° C. in air atmosphere.
Therefore, in the disclosed methods, spinel structured ferrites were focused on, e.g., including, but not limited to, MFe2O4 (where M=Mn, Co, MnZn), cobalt oxide (CoO), and copper oxide (CuO), all of which possess both low bandgaps and good stability at high temperature.
Mn—Zn Ferrites
The optical properties of Mn—Zn ferrites is expected to change with the content ratio of Mn vs. Zn elements in the ferrite composition, which may result from the different values oxygen deficiency, which in turn affects the electrical conductivity, dielectric constant, or refractive index depending on the compositions.
A facile hydrothermal process was employed to synthesize the Mn—Zn ferrites. For example, hydrothermal was employed because of it is scalable to industrial application. Also, hydrothermal yields nano-sized powders. An exemplary synthesis procedure 100 is shown in
The methods of the disclosed technology can control the composition of ferrites nanoparticles with a spinel structure (AB2O4) and evaluate the optimal Mn/Zn ratio of the ferrites. As shown in
For example, the typical size of as-synthesized Mn—Zn ferrites was found to be nano size (e.g., 50˜100 nm average diameter) which was obtained from SEM images 300, 302, and 304 especially for MnFe2O4, (Mn0.8, Zn0.2)Fe2O4 and (Mn0.5, Zn0.5)Fe2O4 respectively showing a dark color, as shown in
Information of Mn—Zn ferrites is summarized on Table 3, e.g., including the exact compositions, hydrothermal conditions, particle size, and color of the resultant powders.
The synthesized Mn—Zn ferrites particles with different compositions were then made to be of black color by annealing (e.g., at 850° C. for 2 hr in air atmosphere) in order to stabilize the crystal structure of Mn—Zn ferrites at a high temperature like 750° C. which is the targeted operation temperature of the CSP system.
When the particles were annealed, some particle size growth appeared so that they have the size of 100-500 nm, as shown in
Co Ferrites
Co-ferrite (CoFe2O4) also shows the black color which is expected to have a high absorption of a visible light because this material has low bandgap of 1.2 eV (e.g., 1.034 μm). This type of nanoparticle can be synthesized through 2-step synthesis method which is similar to one of Mn—Zn ferrites. Especially, for example, chloride salt of cobalt and iron was useful for producing black-colored Co-ferrite nanoparticles which has a nano-sized cubic structure, as shown in
Cobalt Oxide Nanoparticles and Nanorods
Cobalt oxide (CoO) has a relatively low bandgap which is 0.47 eV (e.g., 2.64 μm, at the temperature of 250 K) so that the high absorption effect is expected to obtain. These exemplary cobalt oxide NPs were also made by the hydrothermal synthesis, which was similar to the exemplary MnZn-ferrites method. For example, cobalt chloride salt was used as a precursor material and the temperature of hydrothermal synthesis was 150° C. for 20 hr, for example. The synthesized CoO NPs and annealed NPs were observed with SEM images 600 and 602, as shown in
In order to increase the crystallization and the thermal stability, the synthesized cobalt oxide particles were annealed (e.g., at 750° C. for 2 hr in air atmosphere) after which particle size increased to 100-300 nm and the color was black. By means of EDX composition analysis, the annealed particles proved to be cobalt oxide as shown in
Secondly, nanorods (NRs) of cobalt oxide were synthesized by hydrothermal method using cobalt chloride salt and urea (CO(NH2)2) at 105° C. for 10 hour. After drying precipitates in a vacuum oven, the annealing process was made at 300° C. for 3 hour in air. For example, cobalt oxide made by this method can be Co3O4 which has a bandgap of 1.28 eV (e.g., 0.969 μm). The synthesized nanorods of Co3O4 have black color which is caused by the bandgap as low as Co-ferrite. The exemplary images and size information 700 and 702 are summarized in
Copper Oxide Nanoparticles and Nanorods
The bandgap of copper oxide (CuO) is as low as 1.2 eV (e.g., 1.034 μm) which can be applicable for CSP light receiver material. At first, copper oxide particles were synthesized with hydrothermal method using copper chloride salt and annealed (e.g., at 750° C. for 2 hr in air). The image and particle size measured by SEM 800 are shown in
In addition to copper oxide particles, CuO nanowires were also thermally grown on Cu foil by heat treatment at 500° C. for 5 hr in air atmosphere. The images and size of this CuO nanowires were observed with SEM (800, 902 and d904), as shown in
Ceramic Nano-Shell Coating
The refractory yttrium oxide (Y2O3) nano-shell was introduced as a new core-shell type structure. Such a structure coated with tight shell of very stable oxide like Y2O3 is expected to prevent nanoparticles from sintering-induced coarsening during high temperature service. Also, the presence of stable oxide shell could beneficially stabilize the oxidation state (oxygen deficiency or oxygen stoichiometry) of metal oxides much more than the oxide without an yttria shell. In order to confirm these effects of yttria shell, Fe3O4— Y2O3 core-shell nanoparticles were synthesized utilizing the concept of a reverse emulsion method which was previously applied for SiO2 shell, with 20-30 nm Fe3O4 particles and Y(O-iPr)3 (yttrium iso-propoxide) precursor, as the procedure 1000 described in
For example, when the exemplary core-shell nanoparticle was observed with TEM, the core was Fe3O4 having (220) and (400) plane as a main crystal structure and the shell could be estimated to be Y2O3 which had (026), (541), (046), or (543), as shown in
The formation of yttria shell could be also confirmed by EDX analysis (Graph 1200) from which Y element occupied around 4 at % and Fe element was approximately 26 at %, as shown in
Yttria shell effect can be evaluated by comparing the sintered size between bare Fe3O4 NPs and Y2O3-coated Fe3O4 NPs, as shown in images 1300, 1302, 1304 and 1406 of
This type of ceramic nanoshell can be applied for other metal oxide particles such as metal-ferrites, cobalt oxide, and copper oxide to keep particles from sintering and growing at high temperature. In addition to yttria shell, for example, silica (SiO2) shell can be considered to reduce the sintering phenomena and to increase the thermal stability of oxygen stoichiometry of metal oxides.
Coating Procedure and Surface Enhancement—Coating Procedure
An illustrative process diagram of an exemplary coating procedure of the sunlight absorbing coating layers is shown in
Coating Procedure and Surface Enhancement—Surface Enhancement
A surface with proper roughness can possess enhanced solar absorption. The length scale most relevant to optical performance lies in the 100's of nanometers to a few microns. For example, in order to enhance the roughness of otherwise flat surfaces made from the spray coating process, two different techniques were employed that are both effective and scalable. Combing these two exemplary techniques result in a greater FOM.
Coating Procedure and Surface Enhancement—Polymer Beads
In some exemplary implementations, for example, porous coating structures were first made by using sacrificial organic additives, e.g., such as polymer beads, which were initially mixed with the coating materials and subsequently removed upon high-temperature annealing, leaving behind voids that give rise to porous structures and rough surfaces. For example, polystyrene beads were applied with controllable size distribution (other type of polymer beads should also be feasible). For example, in order to make porous coating layers and enhance the surface roughness on black oxide coating samples, the volumetric concentration of the polymer beads, the black oxide powders, and SiO2 matrix was optimized.
The detailed processes of making the porous and rough structures using the polymeric beads are as follows: (a) mixing silicon resin and xylene and isobutanol (3:1) mixture by using probe-sonication for 30 mins, (b) adding the polymer beads and the homogenization by using probe-sonication for 30 min, (c) adding the black oxide powders into the solution, (d) ball milling with YSZ grinding balls for 24 hours, (e) spraying the slurry on Inconel substrate, and (f) removing the polymer beads by heating the samples at 750° C. for 30 min.
The enhanced surface roughness was observed in SEM images 1500, 1502 and 1504 (
Coating Procedure and Surface Enhancement—Polymer Stamps
An exemplary approach was employed to achieve larger surface roughness based on microfabricated stamps. Since micro-sized patterning is relatively easy to fabricate, a photolithography technique was employed to introduce micro-sized patterns on solar absorbing coating layer. One attempt included making a SU-8 stamp of 10 μm-tall and 3 μm (diameter)-3 μm (distance between next pillars) sized pillars to make hole patterns on solar absorbing coating layer as shown in image 1600 of
Exemplary Performance of Solar Absorbing Coating Made of Black Oxide Nanoparticles
Coating Procedure and Surface Enhancement—Adhesion to the Substrate
In some implementations, for example, the tape test was used to evaluate the adhesion of the coating layers.
Mn—Zn Ferrites
As shown in Graph 1800 of
Co Ferrites
Solar absorbing coating layers were fabricated with the synthesized CoFe2O4 nanoparticles having two kinds of different size including 50-100 nm and 100-300 nm. In this exemplary case, the Co-ferrites nanoparticles were applied for solar absorbing coating layer in an as-synthesized state without an additional annealing treatment. The reflection measurement was made at room temperature before annealing solar absorbing coating layers.
As shown in
Cobalt Oxides: As-Coated CoO
Solar absorbing coating samples were made using synthesized nano-sized CoO powders and evaluated by the optical measurement.
Effect of Roughness Created Using Polymer Beads
Effect of Antireflection Coating
Antireflection coating has also been applied to further enhance the absorption. As an example, MgF2 was applied of approximately 300 nm thick on top of the CoO layer. MgF2 has a refractive index of about 1.35, which is between that of air (1.0) and SiO2 (1.5). Therefore, an MgF2 layer reduces the light reflection and improves the absorption. As shown in Graph 2100 of
High-Temperature Durability and Oxidation Resistance
Solar absorbing coating layers with Mn—Zn ferrites and Co-ferrites were annealed at 750° C. for 10 hr in air, for example, in order to evaluate the thermal performance of solar absorbing coating layers at high temperature (750° C.) which is the target operation temperature of CSP system.
As shown in
FOM (t = 10 hr; 750° C.)
For the solar absorbing coating layers made from the CoO powders, three different samples were fabricated and evaluated for the isothermal endurance. Based on SEM images of a regular CoO sample before (
In addition, concentrating solar power is becoming an increasingly important part of the renewable energy portfolio. However, further cost reduction is desired to make CSP competitive with traditional energy technologies. Higher operating temperature is considered an attractive avenue leading to higher power conversion efficiency and lower cost, but tremendous technical challenges exist with higher temperature operation of CSP, with one of the main issues being the lack of a high-performance solar absorbing material that is durable at 750° C. or above. In another aspect of this patent document, described is a black oxide material, made of cobalt oxide nanoparticles, that is synthesized and utilized as a high-temperature solar absorbing material. The nanoparticles are embedded in a dielectric matrix through a scalable spray coating process. The top layer of the coating is further improved with light-trapping structures using sacrificial fillers introduced from the same coating process. After the surface modification of cobalt oxide coating, a high thermal efficiency of 88.2% can be achieved using the disclosed technology. More importantly, the coating shows no degradation after 1,000-hour annealing at 750° C. in air, while the existing commercial light absorbing coating was reported to degrade by long-term exposure at high temperature. The materials and processes described in this patent document are promising for solar absorbing coating for future high-temperature CSP systems.
Introduction
The development and deployment of renewable energy sources is becoming an increasingly urgent need for human society. Concentrating solar power (CSP) systems (or solar thermal systems) are becoming an important part of the major portfolio of renewable energy generation. One of the key potential advantages of CSP over many other forms of the renewables is the possibility of inexpensive energy storage using thermal energy storage systems (TES), which is useful for grid-level power management. The TES can extend the electricity generation capability to periods with no sunlight available, thereby significantly expanding the value and usage of solar energy. CSP systems can also be hybridized with other alternative energy systems, such as solar photovoltaic, thermoelectric, or thermophotovoltaic systems, to increase the penetration of renewable energy power. Despite these perceived benefits, the levelized cost of energy (LCOE) of CSP, however, is still too high to compete with traditional thermal power plants and some other alternative energy technologies (such as photovoltaics).
In order to develop a cost-competitive CSP technology, it is imperative to increase the system power conversion efficiency. To maximize the efficiency of CSP, it is desirable to raise the operating temperature for higher Carnot efficiency. As a result, the temperature of heat transfer fluids (HTFs) needs to be 700° C. or higher. Toward this aim, all of the components of CSP systems, such as solar field, HTFs, power block, TESs, and solar receivers need to be made compatible with the higher-temperature operation.
As far as the solar receiver is concerned, the light-absorbing coatings on the receiver play an important role by absorbing solar thermal energy and raising the temperature of the HTFs to above 700° C. Although spectrally selective coatings (SSCs) with multilayers/graded cermets or tandem structures have been developed and stably operated in vacuum in parabolic trough CSP systems, none of these SSC structures can operate at high temperatures in air, which is needed in future solar-tower based CSP systems. The state-of-the-art solar absorbing material used in solar towers is based on a commercially available black paint called Pyromark 2500®. Pyromark 2500® is known to have high thermal efficiency above 600° C. and has been used for central solar receivers of CSP plants. However, according to prior studies, the absorptivity degraded after high temperature (>700° C.) exposure due to crystal structure changes and phase instability. Therefore it is clear that a new light absorbing coating material with high absorption efficiency and excellent durability at elevated temperature in air environment needs to be developed for the next generation CSP systems.
Since the light absorption is directly related to solar energy generation efficiency, a large number of studies about optical absorption enhancement have been actively pursued. Several light trapping approaches were studied, such as texturing, metallic nanostructures, and photonic and plasmonic structures. However, most of these studies about light trapping have been applied on photovoltaic applications using vacuum deposition methods. As the result, these processes are not necessarily compatible with CSP applications, where spray coating is generally employed to coat the light absorbing layers onto solar tower receivers, for example, Pyromark 2500® in Solar One and Solar Two central towers.
Here, we report a highly efficient and high-temperature durable light absorbing coatings based on cobalt oxide nanoparticles for CSP receivers. Cobalt oxide materials have been studied as selective absorbing layers and fabricated using spray pyrolysis method, chemical vapor deposition and electrodeposition. Although several previous studies showed the applicability as solar collectors within the temperature range of 300° C.˜650° C., there is no existing light absorbing coating suitable for CSP operating at higher temperature (˜750° C.) without performance degradation. In some implementations of the disclosed technology, the cobalt oxide nanoparticles can be synthesized via a facile hydrothermal process and utilized as the light-absorbing material in the coating layers. The coating layers consist of or includes cobalt oxide nanopowders dispersed in silica matrix, and can be deposited on metal substrates via a simple and scalable spray coating process, which is compatible with CSP applications. The disclosed technology includes using novel and yet simple surface texturing techniques based on sacrificial polymer beads that can be easily integrated with the spray coating process, to improve the light absorption. Finally, the developed coating layer exhibited unprecedented high-temperature durability, showing no degradation in structural or optical properties after annealing at 750° C. in air for 1,000 hours.
Cobalt Oxide Nanoparticle Synthesis and Sample Preparation
Cobalt oxide nanoparticles of right sizes can be synthesized for high light absorption. For nanoparticles (aspect ratio ˜1), the optimal size for absorbing visible and near infrared light is probably around 200˜400 nm. If the particle size was too small, the resultant coating film would have small surface roughness, which is not effective for light trapping. In addition, for high temperature application, very small nanoparticles (<100 nm) would agglomerate and become larger size particles. Therefore, techniques employed can produce nanoparticles with 100s of nanometers in diameter. Metal oxide nanoparticles can be prepared by a number of different methods, such as sol-gel technique, mechanical grinding (ball milling), mechanochemical synthesis, and hydrothermal synthesis, etc. The hydrothermal method can be used to synthesize Co3O4 nanoparticles for convenience. However, it should be noted that other inexpensive nanoparticle synthesis techniques mentioned above may also be used for producing metal oxides for SSC applications.
Cobalt oxide nanoparticles can be synthesized via a hydrothermal process using cobalt chloride salt (CoCl2.6H2O) as the precursor. 10 M solution of sodium hydroxide (NaOH) can be gradually dropped into 1 M solution of cobalt chloride to induce precipitation of cobalt hydroxide until pH value of the reacted solution reached 11. The hydrothermal synthesis can be performed at 150° C. for 20 hours in order to transform the precipitated cobalt hydroxide into cobalt oxide. The cobalt oxide particles can be washed with de-ionized water using a centrifuge and dried using a freeze-dryer. The as-synthesized nanoparticles can be annealed at 750° C. for 2 hours for phase stabilization.
For the fabrication of Co3O4 slurry, methyl phenyl polysiloxane resin (SILIKOPHEN® P 80/X) can be utilized as precursor of SiO2 matrix. The volume ratio between the active material (cobalt oxide nanopowders) and the SiO2 matrix can be systematically varied and optimized. The required amount of resin can be diluted with an organic solvent mixture consisting of or including two miscible solvents, xylene and isobutanol (volume ratio 3:1). The optimum dilution was important to ensure good quality of the coating layers, because too viscous slurry could not make a smooth spray stream while very dilute slurry could not make a stable spray-coating onto substrates. In order to dissolve the resin in the solvent, the mixture can be sonicated for 30 minutes with a probe type sonicator. During sonication, the solution container can be cooled in an ice-bath to avoid concentration change due to the evaporation of organic solvents. Co3O4 powders can be mixed with the prepared solution and yttria stabilized zirconia (YSZ) grinding balls can be added into the blend. The ball milling can be conducted for 24 hours in order to make the mixture homogeneous.
The black oxide spray coating can be performed using a spray gun on a high temperature Ni alloy (Inconel 625) sheet coupons (½″×½″ in size). The spray pressure can be set at 40 psi and the distance between the spray gun and the Inconel substrate is about 10 cm, which has been optimized for the best coating quality. After spray coating, the samples can be heated at 250° C. for 1 hour for curing of SiO2 resin. All of the coating samples consist of or include two layers: the base layer of approximately 30 μm thick and a top layer with surface-topography-modified structure described in the next paragraph.
Cobalt Oxide Surface Texturing
The first method to alter the surface texturing and topography of the top layer to improve optical absorption includes employing imprinting stamps with SU-8 polymer pillars which are prepared by using standard microfabrication processes. In one example, the polymer pillars can be 3 μm in both diameter and spacing and 10 μm in height. The stamps are then pressed onto coated Co3O4 coating surface and left as imprinted prior to the resin curing step. Then, the sample can be annealed at 750° C. for 1 hour to burn away the remaining polymer pillars.
The second method can be used to create roughened surface and includes incorporating and subsequently removing micron-sized sacrificial polymeric beads within the Co3O4 coating layer. The volumetric concentration of Co3O4, polymer beads and silicone resin can be optimized to yield the best optical performance (as shown in Table 14), and the mixtures can be sonicated with a probe type sonicator for proper mixing.
Then, a desired amount of silicone resin can be added, followed by the same ball milling and spray coating processes described in the prior paragraphs. Finally, the coated layers can be annealed at 750° C. for 1 hour to remove the polymeric beads and leave behind the porous and topographically rough top surface of Co3O4 layer.
Optical Performance and High Temperature Endurance Evaluation
The thermal efficiency of a solar receiver, which measures the ratio of the energy absorbed relative to the incident solar energy, and FOMs can be calculated from Eq. 1.
where R(λ) is the spectral reflectivity, I(λ) is the spectral solar radiance per square meter as defined by the reference solar spectral irradiation (ASTM G173), B(λ,T) is the spectral thermal emission of a black body at temperature T, and C is the concentration ratio. In the calculations of equation 1, the black body temperature T of the solar receiver is assumed to be 750° C. and C is assumed to be 1,000 (1,000 sun), which are the target temperature and concentration ratio, respectively, for enhanced efficiency of CSP systems. All of the integrals to calculate FOMs are evaluated in the range from 300 nm to 20 μm, as only negligible quantities of solar power are present outside this range. Reflection data can be measured at room temperature using a Labsphere® 4″ integration sphere to collect all angles of reflection from samples and Andor® 303i spectrometer equipped with a Si based (spectral range 300-1100 nm) and InGaAs based (spectral range 900 nm-2500 nm) detector. Reflection behavior of samples outside of the measured spectral range of 400 nm-2.5 μm can be extrapolated for use in Eq. 1. While the reflection data can be measured at room temperature, it is highly desirable to obtain the reflection spectra at the actual operating temperature of ˜750° C. High temperature optical measurement in non-vacuum environment is highly challenging due to the heat conduction and possible damage to lenses, integration sphere, and other optical system parts. Such measurements can be obtained with improved design of the optical measurement system.
To characterize the durability of the coating at elevated temperature, the long-time annealing tests at 750° C. in air can be carried out on the coated samples as well as the Co3O4 nanopowders with the annealing time up to 1,000 hours. The composition of the material before vs after the annealing can be analyzed using XRD (Broker D8 Discover) using a scan speed of 0.037° s−1 in the 2θ range of 20˜80°; the structural integrity can be examined using optical microscope and SEM (Phillips XL30 FEG); the thermal stability of Co3O4 phase at high temperature (750° C.) in air can be also evaluated using thermogravimetric analysis (TGA, TA Instruments SDT Q600) with air of 20 ml/min flow rate; finally, the optical properties of the samples can be measured with the same procedure as above.
Cobalt Oxide Nanopowders Synthesis and Coating Process
Cobalt oxide nanoparticles can be synthesized by the hydrothermal process. Both the as-synthesized and annealed cobalt oxide nanoparticles can be examined with scanning electron microscopy (SEM). The diameter of the as-synthesized powders ranges from 100 to 300 nm after stabilizing heat treatment, as shown in
Light Absorbing Coating Structure Modification
After establishing the principle of enhanced light absorption with surface hole patterning, a more scalable process based on sacrificial polymer beads can be developed, as described in section 2.2. The details of the samples are provided in Table 14. From the SEM images 2600 and 2602 shown in
High Temperature Stability of Co3O4 Light Absorbing Coating
The receiver coating in the next generation CSP systems should possess not only high thermal efficiency but also high temperature stability because of the anticipated trend of higher operating temperature (above 700-750° C.). The high-temperature stability of the coating depends on both the intrinsic material properties (e.g., phase transformation at high temperature) and structural integrity of the porous coating, as well as its adhesion to the substrate. The high-temperature annealing test can be performed in air as described in Section 2 for both the coating sample and the nanopowders. For the coated sample, the one with 1:5 volume ratio of cobalt oxide powders to polymer beads (Co3O4-3) can be used because it showed the best FOM.
The microstructural and XRD analysis results are displayed in
The FOMs of the best-performing samples with 1:5 volume ratio of black oxide powders to polymer beads (designated as Co3O4-3A and Co3O4-3B samples) after various annealing durations ranging from 0 to 1,000 hours are shown in
Yttria (Y2O3)-Coated Core-Shell Nanoparticles:
A thermally stable nanoshell of Y2O3 can be utilized to make thermally resistant core-shell particles having semiconductor, metal and metal oxide as cores, such as Fe3O4-Yttria, SiGe-Yttria, and Metal-Yttria core-shell nanoparticles.
A1 : 3.358/nm=0.2978 nm: Fe3O4 (220)
A2: 4.781/nm=0.2099 nm: Fe3O4 (400)
A3: 6.186/nm=0.1616 nm: Y2O3 (026) or Y2O3 (541)
A4: 6.763/nm=0.1488 nm: Y2O3 (046) or Y2O3 (543)
Further advanced series of black-oxide nanoparticle based sunlight-absorbing coating materials can be implemented using the disclosed technology. These advanced nano black-oxide nanoparticle materials include a Cu—Cr—O ceramic system. An example of the Cu—Cr—O ceramic system can include a composition of CuCr2O4. In another aspect, the advanced nano black-oxide nanoparticle materials include a Cu—Fe—Mn—O ceramic system. An example of the Cu—Fe—Mn—O ceramic system can include a composition of CuFeMnO4. The effects of compositions and synthesis procedures on the properties of these two nano black-oxide materials are described below.
For the copper chromite oxide system, the change in chemical composition and stoichiometry significantly affects the sun-light absorbing optical properties. Such variation of Cu/Cr ratio was produced by chemical synthesis using different ratio of precursor chemicals, for example, using a hydrothermal process (essentially chemical reactions in a higher pressure, steam-like autoclave environment), with the particles so prepared subjected to higher temperature crystallization process.
These black-oxide nanoparticles are then dispersed in a silica base matrix. Such composite structured coating layer can be prepared, for example, by mixing 20-40% volume % of nano black-oxide particles in a liquid spin-on glass precursor followed by spray coating, brush coating, or doctor blade coating to form a uniform thickness layer, then baking the coating at 200-500° C. to burn away the polymer component and create a dense silica matrix nanocomposite having 30-100 um thick layer well adhered on a metallic substrate that are durable at high temperature such as Inconel alloys. Other alloys such as Haynes alloys or stainless steels can also be used for transporting the heat transfer fluid such as a molten salt, hot oil or steam to the CSP power generator.
Shown in
The optical properties of CuFeMnO4 layer was evaluated after the particles were incorporated into the sunlight absorbing coating. The CuFeMnO4 black-oxide nanoparticles were then dispersed in a silica base matrix, for example, by mixing 20-40% volume % of nano black-oxide particles in a liquid spin-on glass precursor followed by spray coating, brush coating, or doctor blade coating to form a uniform thickness layer. The coated layer is then baked/cured at 200-500° C. to burn away the polymer component and create a dense silica matrix nanocomposite having 30-100 um thick layer well-adhered on a metallic substrate that are durable at high temperature such as Inconel alloys, Haynes alloys or stainless steels.
The optical properties of the sunlight absorbing coating containing Cu—Fe—Mn—O based black-oxide nanoparticles are strongly dependent on the composition of the oxide material.
Different types of black oxide nanoparticles exhibit quite different sunlight absorbing and reflecting properties. It has been discovered, according to the disclosed technology, that a combination of two or more different oxide layers in the coating material can provide further improved optical properties. Examples of such mixed double layer structures combining CuFeMnO4 and CuCr2O4 are presented in
Shown in the graph 4100 of
The CSP solar receiver structure (e.g., black oxide coated Inconel® alloy tubes) is heated and cooled everyday from the high temperature of e.g., 750° C. during the daytime due to the concentrated sunlight reflected and focused onto the receiver by an array of mirrors. Therefore the receiver sunlight-absorbing coating is thermally cycled every day. The thermal expansion match between the oxide coating layer and the metallic tube substrate material is substantial, and if the adhesion of the coating onto the metal substrate is not strong, the thermal cycling can induce undesirable delamination and flaking-off of the coating material. The nano black oxide coatings, according to the disclosed technology, are desirably highly adherent too the Inconel and stainless steel substrates, as shown in
The degradation of the sunlight to heat conversion efficiency FOM (Figure-of-Merit) needs to be minimized on thermal cycling. Shown in table and graph 4300 in FIG. 43 is the exemplary comparative thermal cycling induced changes in the Figure of Merit (FOM), which shows that the nano black-oxide based coatings are superior to the commercial Pyromark® coating in terms of minimal loss of FOM on thermal cycling.
The disclosed technology has a significant low cost potential for the solar absorbing coating technology. The cost mainly may come from three sources, e.g., the NP fabrication process, raw material costs, and coating process, all of which are low cost. The application of the absorbers can be primarily targeted at and concentrated solar power systems with high temperature operation (e.g., T>600° C.), where solar absorptance and high-T durability are the prime concern.
In concentrated solar power (CSP) with very high concentration ratios (e.g., >100 times), e.g., solar tower, the heat transfer fluids inside the solar absorbers can be heated up to above 600° C., which can be used to drive turbines or other engines to generate electricity, so called the concentrating solar power. The CSP capacity reaches an installed capacity of ˜1.17 GW as of 2011. Currently, about 17 GW of CSP projects are under development worldwide (e.g., US: 8 GW; Spain: 4.46 GW; China: 2.5 GW). The IEA publication (ETP 2008) lists CSP as one of the many cost-effective technologies that will lower CO2 emissions. In the ETP BLUE Map scenario, CSP produces 2,200 TWh annually by 2050 from 630 GW capacities. CSP is expected to contribute ˜5% of the annual global electricity production in 2050 in this scenario. In the Advanced scenario of CSP Global Outlook 2009, the estimated global CSP capacity by 2050 is 1,500 GW, with an annual output of 7,800 TWh. Assuming, $1/Watt for the electricity cost, the economy scale of CSP power plants is $630 billion (630 GW) to $1.5 trillion (1,500 GW) by 2050. Since 8-10% of the cost goes to solar absorbers, the market size for the solar absorbers for CSP application ranges from $63-150 billion (e.g., note: this is the cumulative market size till 2050, not annual).
In some aspects, the disclosed technology includes a concentrated solar power system incorporating the disclosed solar absorbing coatings and layers, as well as further modified or related design and structures.
In some aspects, the disclosed technology includes a hydrothermal method for fabrication of black oxide nanoparticles (NPs).
In some aspects, the disclosed technology includes methods for using ceramic shell coating to mitigate the coarsening and sintering effect of the NPs at high temperature, and possibly reducing the probability of oxygen stoichiometry change during high temperature operation.
In some aspects, the disclosed technology includes structure and fabrication methods for making the solar absorbing coating on metallic surfaces.
In some aspects, the disclosed technology includes a surface textured layer design for solar absorbing coating so as to improve light absorption, enhance adhesion, and improve temperature-related reliability For example, the use of antireflection coating on the solar absorbing coating can improve the absorptance.
In some aspects, the disclosed technology includes deposition methods and on-site repair methods for the spectrally selective coating using spray coating, brush coating, etc. of nanocomposite precursors and curing.
In some aspects, the disclosed technology includes devices and applications for concentrated solar power type solar energy conversion to steam or electricity, or water heating, home/building heating, or other energy conversion approaches.
While this patent document contains many specifics, these should not be construed as limitations on the scope of any invention or of what may be claimed, but rather as descriptions of features that may be specific to particular embodiments of particular inventions. Certain features that are described in this patent document in the context of separate embodiments can also be implemented in combination in a single embodiment. Conversely, various features that are described in the context of a single embodiment can also be implemented in multiple embodiments separately or in any suitable subcombination. Moreover, although features may be described above as acting in certain combinations and even initially claimed as such, one or more features from a claimed combination can in some cases be excised from the combination, and the claimed combination may be directed to a subcombination or variation of a subcombination.
Similarly, while operations are depicted in the drawings in a particular order, this should not be understood as requiring that such operations be performed in the particular order shown or in sequential order, or that all illustrated operations be performed, to achieve desirable results. Moreover, the separation of various system components in the embodiments described in this patent document should not be understood as requiring such separation in all embodiments.
Only a few implementations and examples are described and other implementations, enhancements and variations can be made based on what is described and illustrated in this patent document.
This patent document claims priorities to and the benefits of (1) U.S. Provisional Application No. 61/952,774 entitled “SOLAR ENERGY ABSORBING COATINGS AND METHODS OF FABRICATION,” and filed Mar. 13, 2014, and (2) U.S. Provisional Application No. 62/093,296 entitled “SOLAR ENERGY ABSORBING COATINGS AND METHODS OF FABRICATION,” and filed Dec. 17, 2014, the entire contents of which are incorporated by reference in this document.
This invention was made with government support under grant DE-EE0005802 awarded by the Department of Energy (DOE). The government has certain rights in the invention.
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/US15/20589 | 3/13/2015 | WO | 00 |
| Number | Date | Country | |
|---|---|---|---|
| 61952774 | Mar 2014 | US | |
| 62093296 | Dec 2014 | US |
