Improved Solar Absorptance of WC/Co Solar Selective Absorbing Coating with Multimodal WC Particles

: One type of multimodal (comprised of nanometer and sub-micrometer WC particles) and two types of conventional (comprised of nanometer and sub-micrometer WC particles, respectively) WC/Co powders were deposited on AISI 304L stainless steel substrates by using high velocity oxygen fuel spraying. The use of multimodal WC particles was indicated to have a beneﬁcial effect on the solar absorptance ( α ) of the WC/Co coatings. The α of the multimodal WC coating reached 0.87, which was much higher than what can be achieved by either ﬁne (0.82) or coarse powders (0.80) alone. By microstructural analysis, the enhancement in solar absorptance of the multimodal WC/Co coating was ascribed to the layer of distributed WC particles. During the thermal spraying, the nanostructured WC particles underwent rapid melting for the large speciﬁc surface area while the aggregated powders were heated, but not necessarily melted. The molten nano-WC would ﬁll the available pores between the softened and heated aggregates, providing a layered distribution of WC particles for the spray-deposited coating. In this condition, the light-trapping in the multimodal coating will be enhanced due to the efﬁcient light reﬂection among the multimodal WC particles, which contributes to the enhancement of solar absorptance. Furthermore, the HVOF thermal spray gun is preferred over a plasma system due to the lower particle temperature and shorter residence time, which preserves a desirable WC phase and diminishes the tendency for decarburization.


Introduction
Metal-dielectric coatings that employ highly solar-absorbent and IR-transparent materials deposited onto highly IR-reflective metal substrates, such as Co/WC [1,2], Pt/Al 2 O 3 [3], Mo/Si 3 N 4 [4] and W/AlN [5], have been denoted to develop solar selective absorbing coatings for high temperature photo-thermal conversion applications due to their excellent absorptance (α) performance in the wavelength range of solar radiation (0.3~2.5 µm) and low thermal emittance (ε) in the infrared region (2.5~25 µm) [6]. The metal-dielectric selective coatings can offer a high degree of flexibility for tuning the absorption and scattering cutoff wavelengths by particle and matrix constituents, particle sizes and concentrations, coating thickness, etc. [2,7]. By materials selection, composition optimization and structure design, various kinds of coatings with absorptance better than 0.90 and emittance lower than 0.20 were successfully fabricated.
However, these high solar absorptivity, solar selective coatings either need high cost and vacuum processes, such as chemical vapor deposition and sputtering, or they will exhibit bad spectral selectivity around 1~2 µm [2]. In addition, the optical properties of these coatings will start to degrade with the coupled effects of air and high temperature, due to oxidation or diffusion of the metal elements into the dielectric matrix, which thus restricts their applications for future concentrating solar power operation at high temperatures (≥700 • C) [2].
High velocity oxygen fuel spraying (HVOF) is well suited to fabricate coatings for photo-thermal conversion at high temperatures thanks to its apparent advantages, such as lower particle temperature, higher powder particle velocity and shorter residence time [8]. Moreover, the low flame temperature can preserve the desirable WC phase, which compromises the density of the coating and the bond strength to the substrate, resulting in preferred mechanical performance and thermal stability. It has been well established that the powder morphology, spray parameters and type of feedstock could have a significant effect on the microstructure of the coating [9] and, in turn, the solar selectivity. The thermal sprayed coatings based on WC are widely used as hard coatings [10][11][12] and solar selective absorbing coatings [1,13]. However, enhancements in WC/Co coatings fabricated by nano-WC/Co powders have remained elusive due to the decarburization occurring under thermal spraying conditions.
In order to reduce the decarburization of the WC/Co coatings, substantial efforts have been made to use agglomerates as feedstock powders [10,14,15], which can minimize the contracting time of the powders that go through the high-temperature cycles due to the increase of momentum, thus limiting the amount of decarburization. Meanwhile, the agglomerated feedstocks also can create large impact forces as particles arrive at the substrate surface and promote strong particle-substrate adhesion which, in turn, leads to the formation of dense coatings [16,17]. Furthermore, the coarse and fine WC particles response differently under the combustion flame, which would lead to the formation of special microstructures. Thus, we can anticipate that the solar spectral properties of the multimodal WC/Co solar selective absorbing coating may be improved by using agglomerated feedstocks. However, only the hardness and abrasive wear resistance, rather than the solar spectral properties of these multimodal WC/Co coatings, have yet been investigated.
In the present work, a class of multi-scaled WC/Co agglomerated particles consisting of a mixture of sub-micrometer and nanometer WC particles was sprayed by employing HVOF. The optical properties and structure of the multimodal coating as well as two conventional coatings were investigated. The deposition behavior of the sprayed multimodal WC/Co solar selective absorbing coating was also discussed.

Agglomerated Feedstock Preparation
Two kinds of WC/Co powders were used in the present work, namely single sized and multimodal mixtures of spherical particles with carbide grain size of sub-micrometer (99.5 wt %, 2 µm, Aladdin, Shanghai, China), nanometer (99.5 wt %, 0.7 µm, Aladdin, Shanghai, China), and sub-micrometer plus nanometer grains, as illustrated in Table 1. The spray powders with a size of approximately 45 µm, measured by laser granulometry (Bettersize, Dandong, China), were produced from the spray dry and conversion as shown in Figure 1a-f, of which, the feedstock powders exhibited agglomerated spherical morphology. It can be seen that the multimodal agglomerated feedstock shown in Figure 1c, fconsist of WC particles and Co phase.

Coating Preparation
AISI 304L stainless steel substrates (30 mm × 40 mm × 1 mm) were cleaned repeatedly by acetone on one side, and their surfaces were roughened prior to spraying. The agglomerated powders were sprayed onto the substrates by ZB-2000 HVOF system (Beijing Zhen Bang Aerospace Precision Machinery Co. Ltd., Beijing, China). The samples produced by HVOF using the sub-micrometer, nanometer and the multimodal WC were denoted as B1, B2 and B3, respectively. Details of the optimized spraying parameters used to fabricate the coatings are illustrated in Table 2, and the thickness of the coatings was measured to be approximately 45 μm.

Solar Absorbing Property and Coating Characterization
The solar absorbing and emitting properties of the deposited solar selective absorbing coatings were measured at room temperature. The near-normal spectral reflectance (R) and transmittance (T) of the coatings were measured in the wavelength range of 0.3~2.5 μm by a Shimadzu UV3600 UV/VIS spectrophotometer (Kyoto, Japan). The near-normal spectral reflectance in the wavelength range of 2.5~25 μm was measured by a Bruker Tensor 27 Fourier Transform spectrometer (Bruker, Karlsruhe, Germany). The absorptance (α) and emittance (ε) of the deposited coatings were calculated according to the reflectance by the following equations:

Coating Preparation
AISI 304L stainless steel substrates (30 mm × 40 mm × 1 mm) were cleaned repeatedly by acetone on one side, and their surfaces were roughened prior to spraying. The agglomerated powders were sprayed onto the substrates by ZB-2000 HVOF system (Beijing Zhen Bang Aerospace Precision Machinery Co. Ltd., Beijing, China). The samples produced by HVOF using the sub-micrometer, nanometer and the multimodal WC were denoted as B1, B2 and B3, respectively. Details of the optimized spraying parameters used to fabricate the coatings are illustrated in Table 2, and the thickness of the coatings was measured to be approximately 45 µm.

Solar Absorbing Property and Coating Characterization
The solar absorbing and emitting properties of the deposited solar selective absorbing coatings were measured at room temperature. The near-normal spectral reflectance (R) and transmittance (T) of the coatings were measured in the wavelength range of 0.3~2.5 µm by a Shimadzu UV3600 UV/VIS spectrophotometer (Kyoto, Japan). The near-normal spectral reflectance in the wavelength range of 2.5~25 µm was measured by a Bruker Tensor 27 Fourier Transform spectrometer (Bruker, Karlsruhe, Germany). The absorptance (α) and emittance (ε) of the deposited coatings were calculated according to the reflectance by the following equations: (2) where I sol (λ) is the solar radiation power at AM1.5, R(λ) is the spectral reflectance of the sample, and I b (λ) is the spectral black body emissive power at room temperature [18]. At least four samples were selected for spectral testing and the average values were used as the solar absorptance.
The phase compositions of the powders and coatings were analyzed by X-ray diffraction (XRD, D8 Advance, Bruker, Karlsruhe, Germany) employing Cu Kα radiation (λ = 1.54056 Å). The surface morphologies and chemical composition were characterized by scanning electron microscopy (SEM, JSM-IT300, JEOL Ltd., Tokyo, Japan), equipped with an energy dispersive spectrometer. The porosity measurements were performed by digital image analysis software SISC IAS V8.0 (Leica, Wetzlar, Germany). Figure 2 presents the X-ray diffraction patterns of the agglomerated powders and the sprayed coatings. It can be seen that only peaks of WC and Co phase are presented in the patterns of both the as-sprayed coatings and the agglomerated powders. This fact suggests that no decarburization occurred or the extent of decarburization, if any, was too small to be detected by the X-ray diffraction in the present experiment conditions. This can be ascribed to the fact that the agglomerated structure minimized the amount of feedstock powders that went through the high-temperature cycle due to the increment of momentum, thus limiting the amount of decarburization. Furthermore, the HVOF thermal spray gun is preferred over a plasma system due to the lower particle temperature and shorter residence time, which preserves a desirable WC phase and diminishes the tendency for decarburization.

Phases Analysis
where Isol(λ) is the solar radiation power at AM1.5, R(λ) is the spectral reflectance of the sample, and Ib(λ) is the spectral black body emissive power at room temperature [18]. At least four samples were selected for spectral testing and the average values were used as the solar absorptance. The phase compositions of the powders and coatings were analyzed by X-ray diffraction (XRD, D8 Advance, Bruker, Karlsruhe, Germany) employing Cu Kα radiation (λ = 1.54056 Å). The surface morphologies and chemical composition were characterized by scanning electron microscopy (SEM, JSM-IT300, JEOL Ltd., Tokyo, Japan), equipped with an energy dispersive spectrometer. The porosity measurements were performed by digital image analysis software SISC IAS V8.0 (Leica, Wetzlar, Germany). Figure 2 presents the X-ray diffraction patterns of the agglomerated powders and the sprayed coatings. It can be seen that only peaks of WC and Co phase are presented in the patterns of both the as-sprayed coatings and the agglomerated powders. This fact suggests that no decarburization occurred or the extent of decarburization, if any, was too small to be detected by the X-ray diffraction in the present experiment conditions. This can be ascribed to the fact that the agglomerated structure minimized the amount of feedstock powders that went through the high-temperature cycle due to the increment of momentum, thus limiting the amount of decarburization. Furthermore, the HVOF thermal spray gun is preferred over a plasma system due to the lower particle temperature and shorter residence time, which preserves a desirable WC phase and diminishes the tendency for decarburization. In addition, the X-ray powder diffraction patterns of the spray powders, as shown in Figure 2a, exhibit sharp and intense features, indicating their highly crystalline nature. Moreover, the Co phase in the spray powders exhibits a hexagonal structure as the three peaks appear at 41.7°, 44.2° and 47.6°, corresponding to (100), (002) and (101) of hcp-Co (ICSD 05-0727), respectively. However, the In addition, the X-ray powder diffraction patterns of the spray powders, as shown in Figure 2a, exhibit sharp and intense features, indicating their highly crystalline nature. Moreover, the Co phase in the spray powders exhibits a hexagonal structure as the three peaks appear at 41.7 • , 44.2 • and 47.6 • , corresponding to (100), (002) and (101) of hcp-Co (ICSD 05-0727), respectively. However, the diffraction patterns of the sprayed coatings exhibit broaden peaks, indicating the presence of non-crystalline phases. This can be attributed to the fact that the particles can reach quite high temperatures during the HVOF process, while they did not have enough time to crystallize under a high cooling rate [8]. Moreover, a portion of the Co phase was transformed into face-centered cubic structure by polymorphic transformation during the HVOF, as shown in Figure 2b, which would be beneficial to the adhesion strength to the substrate due to the good ductility of the face-centered cubic Co phase. Figure 3 shows the reflectance curves in 0.3-2.5 µm for the conventional and multimodal coatings together with the calculated absorptance. The multimodal absorbing coating (B3) exhibited a relatively high absorptance of 0.866, which was higher than the conventional coatings with values of 0.803 (B1) and 0.825 (B2), respectively. As the nano-sized WC can offer significant potential as a material showing enhanced or tunable light harnessing [19][20][21][22], thus the absorptance of sample B2 was measured to be higher than that of sample B1. The enhancement in solar absorptance in the multimodal (B3) coating over the conventional (B1 and B2) coatings will be discussed in Section 4. diffraction patterns of the sprayed coatings exhibit broaden peaks, indicating the presence of noncrystalline phases. This can be attributed to the fact that the particles can reach quite high temperatures during the HVOF process, while they did not have enough time to crystallize under a high cooling rate [8]. Moreover, a portion of the Co phase was transformed into face-centered cubic structure by polymorphic transformation during the HVOF, as shown in Figure 2b, which would be beneficial to the adhesion strength to the substrate due to the good ductility of the face-centered cubic Co phase. Figure 3 shows the reflectance curves in 0.3-2.5 μm for the conventional and multimodal coatings together with the calculated absorptance. The multimodal absorbing coating (B3) exhibited a relatively high absorptance of 0.866, which was higher than the conventional coatings with values of 0.803 (B1) and 0.825 (B2), respectively. As the nano-sized WC can offer significant potential as a material showing enhanced or tunable light harnessing [19][20][21][22], thus the absorptance of sample B2 was measured to be higher than that of sample B1. The enhancement in solar absorptance in the multimodal (B3) coating over the conventional (B1 and B2) coatings will be discussed in Section 4.

Discussion
As shown above, the fabricated multimodal coating can combine the benefits of coarse and fine WC grains, leading to a better solar selectivity than what can be achieved by either fine or coarse grains alone. To better understand the enhancement in absorptance of the multimodal coating over the conventional coatings, the surface morphologies were examined, since the optical properties of the solar selective absorbing coatings are surface sensitive properties [23]. Figure 4 shows secondary electron SEM images of the HVOF deposited coatings. The asdeposited coatings consist of closely packed particles and micro-pores. Meanwhile some un-melted or semi-melted particles were also observed on the HVOF coatings. This is because the agglomerated particles resist being fully melted during the HVOF spraying process [24], and thus lead to a rather rougher surface for the HVOF coating (Figure 4b,d,f). The surface particles of the multimodal coating were finer than the conventional coatings, as shown in Figure 4a-c, which would increase the solar reflection and therefore be beneficial to the solar absorptance.

Discussion
As shown above, the fabricated multimodal coating can combine the benefits of coarse and fine WC grains, leading to a better solar selectivity than what can be achieved by either fine or coarse grains alone. To better understand the enhancement in absorptance of the multimodal coating over the conventional coatings, the surface morphologies were examined, since the optical properties of the solar selective absorbing coatings are surface sensitive properties [23]. Figure 4 shows secondary electron SEM images of the HVOF deposited coatings. The as-deposited coatings consist of closely packed particles and micro-pores. Meanwhile some un-melted or semi-melted particles were also observed on the HVOF coatings. This is because the agglomerated particles resist being fully melted during the HVOF spraying process [24], and thus lead to a rather rougher surface for the HVOF coating (Figure 4b,d,f). The surface particles of the multimodal coating were finer than the conventional coatings, as shown in Figure 4a-c, which would increase the solar reflection and therefore be beneficial to the solar absorptance. Furthermore, the cross-section microstructures of the as-deposited coatings illustrated in Figure 5 shows pot-like WC grains varying in size from 1 to 3 μm and a Co-rich matrix. It has been established that the HVOF sprayed WC-Co coatings exhibit multi-phase microstructures with a lower fraction of WC than the starting agglomerated powders [25]. From these figures, it can be seen that all of the coatings bonded to the substrates well with no distinctive cracks. Moreover, the overall porosity percentages were estimated to be about 1% for the multimodal coating (B3), and 3% and 2% for the B1 and B2 coatings, respectively, which were lower than the reported values [26]. The formation of dense coatings by HVOF is closely related to the use of agglomerated feedstock. During the thermal spraying, particles of different sizes respond to the combustion flame differently. The nanostructured WC particles adhering to the surface underwent rapid melting due to the large surface area while leaving the coarse WC particles largely un-melted, but softened by heating. In this case, the heated but not necessarily melted part of the particle retains the original micro-porosity when it impacts the substrate. The molten nano-WC would fill the available pores between the softened and heated aggregates, providing a dense spray-deposited coating. In addition, the large particle velocities and lower particle temperatures during HVOF can also contributed to further densification of the coating. Furthermore, the cross-section microstructures of the as-deposited coatings illustrated in Figure 5 shows pot-like WC grains varying in size from 1 to 3 µm and a Co-rich matrix. It has been established that the HVOF sprayed WC-Co coatings exhibit multi-phase microstructures with a lower fraction of WC than the starting agglomerated powders [25]. From these figures, it can be seen that all of the coatings bonded to the substrates well with no distinctive cracks. Moreover, the overall porosity percentages were estimated to be about 1% for the multimodal coating (B3), and 3% and 2% for the B1 and B2 coatings, respectively, which were lower than the reported values [26]. Furthermore, the cross-section microstructures of the as-deposited coatings illustrated in Figure 5 shows pot-like WC grains varying in size from 1 to 3 μm and a Co-rich matrix. It has been established that the HVOF sprayed WC-Co coatings exhibit multi-phase microstructures with a lower fraction of WC than the starting agglomerated powders [25]. From these figures, it can be seen that all of the coatings bonded to the substrates well with no distinctive cracks. Moreover, the overall porosity percentages were estimated to be about 1% for the multimodal coating (B3), and 3% and 2% for the B1 and B2 coatings, respectively, which were lower than the reported values [26]. The formation of dense coatings by HVOF is closely related to the use of agglomerated feedstock. During the thermal spraying, particles of different sizes respond to the combustion flame differently. The nanostructured WC particles adhering to the surface underwent rapid melting due to the large surface area while leaving the coarse WC particles largely un-melted, but softened by heating. In this case, the heated but not necessarily melted part of the particle retains the original micro-porosity when it impacts the substrate. The molten nano-WC would fill the available pores between the softened and heated aggregates, providing a dense spray-deposited coating. In addition, the large particle velocities and lower particle temperatures during HVOF can also contributed to further densification of the coating. The formation of dense coatings by HVOF is closely related to the use of agglomerated feedstock. During the thermal spraying, particles of different sizes respond to the combustion flame differently. The nanostructured WC particles adhering to the surface underwent rapid melting due to the large surface area while leaving the coarse WC particles largely un-melted, but softened by heating. In this case, the heated but not necessarily melted part of the particle retains the original micro-porosity when it impacts the substrate. The molten nano-WC would fill the available pores between the softened and heated aggregates, providing a dense spray-deposited coating. In addition, the large particle velocities and lower particle temperatures during HVOF can also contributed to further densification of the coating.
The WC grains would dissolve into the liquid metal, resulting in a solution of tungsten and carbon in cobalt. After the agglomerated powders reaching the substrate, the semisolid nanoparticles can provide a matrix in which the coarser particles remain embedded. The multimodal coating consists of coarse and fine WC grains, as shown by the arrows in Figure 5f, which is helpful for the formation of a denser coating than what can be accomplished by either coarse or fine grains alone.
It is worth noting that the element distributions in the multimodal coating and the conventional coatings are somewhat different, as shown in Figure 6. The gray regions were identified by energy dispersive spectrometer (EDS, JEOL, Ltd., Tokyo, Japan) analysis to be the Co-rich phase. Further examination suggested that the gray and bright regions contained dissolved W element and C element in addition to Co element. The bright regions were identified to contain higher levels of tungsten due to a greater degree of WC particle dissolution [25]. According to the EDS maps for carbon distribution, the multimodal coating (B3) has a lower content of bright phase, which suggests the agglomerated powders can prevent the dissolution of WC into the Co phase during spraying. The WC grains would dissolve into the liquid metal, resulting in a solution of tungsten and carbon in cobalt. After the agglomerated powders reaching the substrate, the semisolid nanoparticles can provide a matrix in which the coarser particles remain embedded. The multimodal coating consists of coarse and fine WC grains, as shown by the arrows in Figure 5f, which is helpful for the formation of a denser coating than what can be accomplished by either coarse or fine grains alone.
It is worth noting that the element distributions in the multimodal coating and the conventional coatings are somewhat different, as shown in Figure 6. The gray regions were identified by energy dispersive spectrometer (EDS, JEOL, Ltd., Tokyo, Japan) analysis to be the Co-rich phase. Further examination suggested that the gray and bright regions contained dissolved W element and C element in addition to Co element. The bright regions were identified to contain higher levels of tungsten due to a greater degree of WC particle dissolution [25]. According to the EDS maps for carbon distribution, the multimodal coating (B3) has a lower content of bright phase, which suggests the agglomerated powders can prevent the dissolution of WC into the Co phase during spraying. In addition, the multimodal coating exhibited a more uniform element distributions combined with the coarse and fine WC particles, as illustrated in Figure 7. The formation of multimodal WC particles in the multimodal coating can be directly related to the following three factors: The formation of multimodal WC particles in the multimodal coating can be directly related to the melting behaviors of coarse and fine WC particles. The nanometer WC particles have lower softening and melting temperatures than the sub-micrometer WC particles, due to the larger surface area to volume ratio. Thus, the fine WC particles were sufficiently melted during HVOF and distributed uniformly among the grain boundaries of Co grains, while the coarse WC particles distributed unevenly due to their insufficient melting. In addition, the momentum of coarse WC particles was larger than that of fine WC particles. The coarse and fine WC particles cannot reach the substrate simultaneously, which would lead to a difference in deformation degree. Thus, the coarse WC particles exhibited a flat shape, as shown in Figure 5f.
As described above, there is a benefit to solar absorptance by using a multimodal feedstock powder for thermal spraying. The enhancement in the solar absorptance results from a strong interaction with light in the multimodal coating consisting of coarse and fine WC particles. For nanoscaled WC particles, the interaction with light is significantly enhanced as the resonant absorption of solar by plasmons, which are collective oscillations of large concentrations of nearly free electrons [27]. Meanwhile, the multimodal distributed WC layer can enhance the solar reflection, which can In addition, the multimodal coating exhibited a more uniform element distributions combined with the coarse and fine WC particles, as illustrated in Figure 7. The formation of multimodal WC particles in the multimodal coating can be directly related to the following three factors: The formation of multimodal WC particles in the multimodal coating can be directly related to the melting behaviors of coarse and fine WC particles. The nanometer WC particles have lower softening and melting temperatures than the sub-micrometer WC particles, due to the larger surface area to volume ratio. Thus, the fine WC particles were sufficiently melted during HVOF and distributed uniformly among the grain boundaries of Co grains, while the coarse WC particles distributed unevenly due to their insufficient melting. In addition, the momentum of coarse WC particles was larger than that of fine WC particles. The coarse and fine WC particles cannot reach the substrate simultaneously, which would lead to a difference in deformation degree. Thus, the coarse WC particles exhibited a flat shape, as shown in Figure 5f. Furthermore, the multimodal WC coating offered great potential for light-trapping, as the nano-WC showed enhanced or tunable light harnessing characteristics. Light was reflected between the sub-micrometer WC particles and the uniform nanometer WC particles, resulting in more efficient light-trapping properties in the multimodal WC coating than in the conventional coatings. However, further optimization of the coating, including particle size selection, particle distribution and coating surface morphology, is likely to increase the solar absorptance even more. Thus, optimal parameters, such as particle size range and distribution, warrant further investigation.

Conclusions
Multimodal WC/Co coating with coarse and fine WC particles fabricated by HVOF using agglomerated feedstock powders exhibited a higher solar absorptance than what can be achieved by either coarse or fine powders alone. The enhancement in solar absorptance of the multimodal WC/Co coating was attributed to the formation of a dense coating with no decarburized phases as well as the layer of distributed WC particles formed during the thermal spraying. These results indicate that the multimodal WC/Co absorbing coating fabricated by HVOF could potentially be employed on a large scale for solar photo-thermal conversion. As described above, there is a benefit to solar absorptance by using a multimodal feedstock powder for thermal spraying. The enhancement in the solar absorptance results from a strong interaction with light in the multimodal coating consisting of coarse and fine WC particles. For nano-scaled WC particles, the interaction with light is significantly enhanced as the resonant absorption of solar by plasmons, which are collective oscillations of large concentrations of nearly free electrons [27]. Meanwhile, the multimodal distributed WC layer can enhance the solar reflection, which can further increase the solar absorptance.
Furthermore, the multimodal WC coating offered great potential for light-trapping, as the nano-WC showed enhanced or tunable light harnessing characteristics. Light was reflected between the sub-micrometer WC particles and the uniform nanometer WC particles, resulting in more efficient light-trapping properties in the multimodal WC coating than in the conventional coatings. However, further optimization of the coating, including particle size selection, particle distribution and coating surface morphology, is likely to increase the solar absorptance even more. Thus, optimal parameters, such as particle size range and distribution, warrant further investigation.

Conclusions
Multimodal WC/Co coating with coarse and fine WC particles fabricated by HVOF using agglomerated feedstock powders exhibited a higher solar absorptance than what can be achieved by either coarse or fine powders alone. The enhancement in solar absorptance of the multimodal WC/Co coating was attributed to the formation of a dense coating with no decarburized phases as well as the layer of distributed WC particles formed during the thermal spraying. These results indicate that the multimodal WC/Co absorbing coating fabricated by HVOF could potentially be employed on a large scale for solar photo-thermal conversion.