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Journal of Nanomaterials
Volume 2013 (2013), Article ID 953790, 10 pages
Enhanced Visible Light Absorption by 3C-SiC Nanoparticles Embedded in Si Solar Cells by Plasma-Enhanced Chemical Vapor Deposition
Department of Mechanical Engineering and Research Center of Industrial Technology, Chonbuk National University, Jeonju 561-756, Republic of Korea
Received 23 July 2013; Revised 4 October 2013; Accepted 28 October 2013
Academic Editor: Takuya Tsuzuki
Copyright © 2013 Bhaskar Parida et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.
Solar cells with 3C-SiC nanoparticles embedded in the Si were investigated by plasma-enhanced chemical vapor deposition. Several sizes of SiC nanoparticles were used as the intermediate layer for the solar cell. The Si thin films showed the formation of micro- and nanocrystallites on the SiC nanoparticle sites, which play an important role of heating block as a nanosubstrate. The Raman spectra revealed that the SiC nanoparticles were embedded in mixed phases of amorphous and nanocrystalline Si. Compared to the conventional solar cell sample, the photoreflectance was significantly reduced in the UV/visible spectral region due to the presence of the embedded 3C-SiC nanoparticles. The Si nanocrystals formed by the thin film deposition played an important role in reducing the photoreflectance within the visible to infrared spectral zones. Furthermore, the SiC nanoparticles contributed less in the photoabsorption at a longer infrared spectral zone wavelength of 1200 nm.
In recent years, several nanostructures, such as nanowires, quantum dots, photonic crystals, and ultra-small nanoparticles, have been widely investigated to improve the efficiency of Si solar cells [1–4]. These ultra-small nanoparticles used in Si solar cells enhance the light coupling in the ultraviolet (UV)/visible spectral range to increase the radiative recombination of photoexcited excitons and carrier transportation and produce a high voltage with improved power performance . Si solar cells have very low UV spectral response due to low band gap energy (), which is a major limitation for collecting photogenerated carriers across Si to generate electrical energy from the UV spectra. To overcome such limitation, nanocrystals have been hybridized on Si solar cells to achieve a twofold enhancement in the cell efficiency under UV light, and wide band gap materials have been used .
Silicon carbide (SiC) is an indirect and wide band gap () semiconductor with quite good electrical properties such as high electron mobility and saturation drift velocity. SiC is widely used in photonics and optoelectronics [7, 8]. SiC/TiO2 nanocomposites can be used as a photoelectrode that produces high power conversion efficiency in dye-sensitized solar cells . SiC used as a window layer in a homojunction photodiode enhances the quantum efficiency with increased photo response in the shorter wavelength spectral region . Furthermore, colloidal SiC nanocrystals absorb light in the UV/visible spectral range  and act as an antireflection coating on the Si solar cell . Therefore, it is of interest to use SiC nanoparticles on Si solar cells to increase the photo response in the shorter wavelength in order to enhance photocurrent generation.
In this work, Si solar cells were investigated using 3C-SiC nanoparticles as an intermediate layer. Ultra-small SiC nanoparticles were fabricated by an anisotropic wet chemical etching process using 50 nm SiC nanoparticles. In this process, SiC nanoparticles of 7, 10, 20, and 50 nm were sprayed on Si solar cells surfaces, and a 100 nm thick Si thin film was deposited by plasma-enhanced chemical vapor deposition (PECVD). Si nanocrystals and nanoclusters were formed by Si thin film deposition. The SiC nanoparticles showed very low photoreflectance (PR) in the UV to visible spectra region depending on size. Furthermore, the deposited Si thin film containing Si nanocrystals enhanced the photo absorption in the IR spectral zone, and the SiC nanoparticles showed very high PR above the IR region.
2. Experiment Details
In the experiment, 2 × 2 cm2, single crystalline p-n junction type microtextured Si solar cells were used. In order to remove the phosphosilicate glass, the samples were etched with 5% HF for 30 sec, rinsed with ultra-pure deionized (DI) water for 5 min, and dried using a N2 gun. Then, 10 nm, 20 nm, and 50 nm diameter 3C-SiC nanoparticles powders (Nanostructured & Amorphous Materials, Inc) were mixed with 5 mL of ethanol to form suspensions. Furthermore, chemical etching of SiC nanoparticles was performed to obtain ultra-small SiC nanocrystals less than 10 nm. Next, 1 gm of 50 nm SiC nanoparticles was etched in a 40% HF and 65% nitric acid (HNO3) solution at 100°C for 1 hour. After etching, the cubic SiC nanoparticles were repeatedly washed with DI water and dried in an oven at 70°C for several hours. To obtain numerous separated nanoparticles, the etched porous powder was mechanically ground with an agate mortar for 1 hr. The ground powder was then dispersed in ethanol and ultrasonicated for 30 min. The formed suspension was centrifuged at an acceleration of 3000 g for 45 min, and the top part of the suspension, which contained uniformly dispersed cubic SiC nanocrystals, was collected. The dispersed nanoparticles with diameters of 7, 10, 20, and 50 nm were sprayed over the microtextured Si solar cell samples and dried in an oven at temperature 70°C for 10 min.
Next, 100 nm thick Si film was deposited on each SiC nanoparticle-coated, microtextured Si solar cell sample using a parallel plate PEVCD consisting of an ultra-high-vacuum chamber (base pressure 1 × 10−9 Torr) and a RF generator (13.56 MHz), connected through a matching network at the top of the reactor electrode. The bottom electrode was grounded and also acted as the substrate holder. The deposition process was performed using 60 W of input power. The samples were heated to 200°C during the deposition. The precursor gases were high purity (99.99% or higher) SiH4 and H2 of 166 and 33 sccm, respectively. The total pressure during the deposition process was maintained at approximately 1 × 10−9 Torr. The deposition was performed for 166 sec. The structural, vibrational, and optical properties of the embedded SiC nanoparticle Si solar cell samples were characterized by a field-emission scanning electron microscope (FE-SEM), X-ray diffraction (XRD), Raman spectroscopy, and PR measurements. Furthermore, the sizes of the SiC nanoparticles were measured by a transmission electron microscope (TEM).
3. Results and Discussion
Figure 1 shows the high resolution TEM (HR-TEM) and TEM images of the 3C-SiC nanoparticles of various sizes dispersed on a carbon-coated TEM grid where (a), (b), (c), and (d) are the SiC nanoparticles of diameter 7 nm, 10 nm, 20, and 50 nm, respectively. The colloidal nanoparticles were investigated using a FE-TEM (JEOL JEM2200FS). Figure 1(a) demonstrates that the 3C-SiC nanocrystals were nearly spherical with an average diameter of 7 nm. However, the lattice fringes of the nanocrystals correspond to different planes that indicate that the nanocrystals are a mix of single and polycrystals. Figures 1(b) and 1(c) are the TEM images of the spherical 10 and 20 nm SiC nanoparticles that are randomly distributed and slightly agglomerated. However, the 50 nm SiC nanoparticles shown in Figure 1(d) are highly agglomerated. The selected area electron diffraction (SAED) pattern of each nanoparticle shown in the top, right corner of their corresponding images indicates that the SiC nanoparticles are crystalline.
Figure 2 shows the FE-SEM images of the removed saw damage flat Si solar cell samples coated with various sizes of SiC nanoparticles. Figure 2(a) shows the sample coated with 7 nm SiC nanoparticles. Similarly, Figures 2(b), 2(c), and 2(d) show the FE-SEM images of the samples coated with 10, 20, and 50 nm SiC nanoparticles, respectively. The morphology of the SiC nanoparticles was spherical. The nanoparticles were very agglomerated and adhered strongly to the solar cell surface. The density of the SiC nanoparticles varies between the samples due to nonuniform distribution during coating.
Figure 3 shows the FE-SEM images of the solar cell surface coated with 3C-SiC nanoparticles before Si deposition by PECVD. Figure 2(a) shows the surface morphology of the sample, where 7 nm SiC nanoparticles were coated on the solar cell surface. Similarly, the surface morphology of the samples coated with 10, 20, and 50 nm SiC nanoparticles are shown in Figures 2(b), 2(c), and 2(d), respectively. The SiC nanoparticles were spherical and adhered strongly to the solar cell surface. Furthermore, the nanoparticles were nonuniform in distribution and highly agglomerated on the surface because of the oven-drying process at 70°C. The density of the 7 nm SiC nanoparticles was low, and they were aggregated on the bottom part of the microtextured pyramids of the sample, whereas the 50 nm SiC nanoparticles had a very high density compared to the other samples. Compared to the other samples, the top of the microtextured solar cell sample surface (d) was fully covered by 50 nm SiC nanoparticles.
Figure 4 shows the FE-SEM images of the surface morphology of all SiC nanoparticle-embedded, microtextured Si solar cell samples. The SiC nanoparticles are embedded in a 100 nm Si thin film deposited by PECVD. Figure 4(a) shows the deposited Si thin film on the 7 nm SiC nanoparticles coated on the microtextured Si solar cell sample, illustrating tetragonal Si microcrystallites of several micrometers. Figure 4(b) shows the Si thin film deposited on the microtextured Si surface, where the 10 nm SiC nanoparticles were coated on the whole surface. The deposited surface shows the nanoscale roughness covering the SiC-coated layer. Similarly, the images of Figures 4(c) and 4(d) are Si thin films deposited on the Si microtextured surfaces of samples embedded with 20 and 50 nm SiC nanoparticles, respectively, which exhibited similar nanostructured surfaces. The inset images show the magnified nanosurface structures with protrusions on the SiC sprayed sites.
The Si thin film deposited sample on the microtextured surface coated with 7 nm SiC nanoparticles was very similar to that observed in a previous work , and the formation of such types of Si microcrystals are theoretically well explained [14, 15]. These microcrystals were formed on the 7 nm SiC nanoparticle-embedded sample, where the SiC was highly agglomerated. The SiC nanoparticles in the sample surface peaks provide an environment in which Si species collected on the SiC sites. The Si nanocrystals are formed due to the surface energy caused by the extraction of hydrogen radicals from the silicon lattice that enhanced the nucleation and formation of Si nanocrystals during the plasma treatment of PECVD [16, 17]. According to the surface diffusion model , Si atoms nucleate crystallites in the early stage of deposition and diffuse for planar growth of island coalescence. For the samples with microtextured surfaces coated by 10, 20, and 50 nm SiC nanoparticles, the SiC nanoparticles covered the whole surface and provided nucleation sites. The planar growth of Si thin films by the surface diffusion process covers the whole surface area. The SiC nanosites also show enhanced growth of nanocrystallites, as shown in the magnified images of the insets. The SiC thin film deposition shows the formation of Si nanocrystallites with mixed phase crystallinity , and the formation mechanism of the nanocrystallites on the highly heat capacitive SiC nanosites is believed to be a nanofurnace process.
The plasma-enhanced growth of Si nano- and microcrystallites on the sites of seeds of SiC nanoparticles from the nanofurnace mechanism is shown in Figure 5. The SiC is highly heat capacitive and can be used as a crucible material in a furnace, while the SiC nanoparticle acts as a heating block in the form of a nanosubstrate or a plasma-heated nanofurnace. Generally, when Si thin film is deposited by PECVD on a Si microtextured surface, the reference sample provides very uniform epitaxial growth of amorphous thin films. From the comparison of the SEM images of Figures 3 and 4, the morphology of Si thin film deposition is very consistent to the positions of SiC nanoparticles. Since the Si thin film deposition was the same for all samples, the difference in morphology corresponds to the difference in nanoparticle size. As shown in Figure 3(a), the SiC nanoparticles were sprayed on the valleys of the microtextured peaks of the Si surface, microcrystallites were formed on the valleys, and uniform deposition of the amorphous Si thin film was observed in the other areas. However, as shown in Figures 3(b)–3(d), the SiC nanoparticles were sprayed on the whole microtextured surface, and thin films grew on the areas of convex protrusions on the sites of the SiC nanoparticles. For the microtextured samples after spraying with SiC nanoparticles, the plasma of the Si species in H2 gas ambient heated the SiC nanoparticles, as in Figures 5(a)–5(c). The SiC nanosite as a nanofurnace can be energized by the plasma radiation, which can locally melt the Si surface and form a nucleation seed for the nanocrystallites by feeding the source of the Si plasma species, as shown in Figures 5(d)–5(f). For nanocatalytic growth of Si nanowires by the Ni-assisted solid-liquid-solid mechanism, SiC nanoparticles enhance the supersaturated Si diffusion process and form a supersaturated Si melt . Without a nanocatalyst of Ni nanoparticles, this work demonstrates the formation of micro- and nanocrystallites but not the growth of Si nanowires. Detailed analysis was performed using XRD and Raman spectroscopies.
Figure 6 shows the XRD patterns for the solar cell samples on which the 3C-SiC nanoparticles embedded in Si thin film grown by PECVD are measured using CuKα radiation. XRD analysis reveals that all samples show characteristic planes at (111), (200), (220), and (222), corresponding to the peaks centered at = 35.05°, 41.2°, 58.38°, and 77.38°, respectively, of the cubic SiC nanoparticles previously indexed . Furthermore, additional peaks of Si and SiO2 were observed. The broad and intense peak at 71.3° is from the Si substrate, whereas the peaks with low intensity at 56.6° and 71.3° are from the Si thin film deposited by PECVD . The peak at 49.8° is from graphite .
The graphite peak was due to the mixture of 3C-SiC nanoparticles. The additional peaks in the 7 nm SiC nanoparticle-embedded sample indicate the presence of SiO2, although these peaks are not considered here. However, the very narrow and intense peak at the (111) plane indicates that the particle sizes increased due to a chuck temperature of 200°C and good crystallization. A narrow and intense peak at appears due to the CuKα radiation diffracted from Si, and the broad high peak at appears from the single crystal Si substrate, in good agreement with a previous study . Furthermore, a stacking fault did not appear at .
Figure 7 shows the room temperature Raman spectra of the solar cell samples with different size cubic SiC nanoparticles embedded in the Si thin film deposited by PECVD as measured by a micro-Raman spectrometer with an irradiation wavelength of 632.768 nm. A wide and small peak at 299.97 cm−1 appeared due to the second-order acoustic phonon mode of bulk Si. However, the optical phonon peaks for SiC nanoparticles samples with 7, 10, 20 nm were observed at 519 cm−1, but the peak was shifted to 503.55 cm−1 for the sample with 50 nm nanoparticles. Generally, the Raman peaks from micro- and nanocrystalline silicon appear at approximately 490–515 cm−1 depending on crystallite size. In our case, the 7, 10, and 20 nm embedded samples show perfect crystalline phases of Si, while the 50 nm SiC-embedded sample exhibited a nanocrystalline phase that indicates a phase decrease with increase in SiC nanoparticle size. Furthermore, the 20 and 50 nm SiC-embedded samples show a high and low amorphous tail below 503.55 and 519 cm−1, respectively, whereas the 7 and 10 nm SiC-embedded samples have a weaker peak at 472.6 cm−1 due to the presence of the amorphous silicon phase in the surface layer. Therefore, the 3C-SiC nanoparticles are embedded under the mixed phase of nanocrystalline and amorphous silicon.
The shifts of the phonon peaks from 519 to 503.55 cm−1 with broadening depend on the size-dependent phonon confinement effect . However, a stress-free 3C-SiC single crystal has two strong transverse and longitudinal optical phonon modes (TO and LO) with Raman shifts at 796 and 972 cm−1, respectively. In our case, only the sample (d) shows a TO phonon mode whose Raman shift at 791 cm−1 indicates that the 100 nm thin film of Si dominates all the SiC nanoparticles, except the 50 nm SiC-embedded sample. Furthermore, the Raman peaks at 1316.22 and 1604.8 cm−1 are related to the D and G bands, respectively, of the C-C of the graphite nanoparticles that are mixed with 3C-SiC nanoparticles .
Figure 8 shows the PR spectra of the SiC nanoparticle-coated and embedded Si solar cell samples. Figure 8(a) shows the PR of the SiC nanoparticles coating the flat Si solar cells. The flat reference sample shows the highest PR that was greater than 30% in all wavelengths of the solar spectrum, satisfying the poor absorption property of Si due to its narrow band gap. The 50 nm SiC nanoparticle-coated flat Si solar cell shows slightly lower PR than the reference. However, the 7–20 nm SiC nanoparticle-coated flat Si solar cells show approximately 20% reduced PR in the UV/VIS wavelength of 242–472 nm compared to the 50 nm SiC nanoparticle-coated sample. Figure 8(b) shows the PR of the microtextured Si solar cell samples coated with SiC nanoparticles. The PR of the SiC nanoparticle-coated sample is reduced to a wavelength less than 472 nm compared to the microtextured reference sample. As decreasing the particles size from 7 to 50 nm, the PR intensity was gradually decreased and the PR peak was red shifted. The 50 nm SiC nanoparticle-coated sample shows a similar PR to the microtextured sample above the visible wavelength of 472 nm; however, in the same region, the PR reduced with decreasing SiC nanoparticles size. The decreased PR in the UV/VIS region caused by the SiC nanoparticle-coated Si solar cell samples satisfies the size-dependent and wide band gap property of SiC.
In Figure 8(c), the microtextured references sample shows the highest PR from the UV to visible spectral region wavelengths of 200–600 nm compared to the Si thin film deposited over the SiC nanoparticle-coated solar cell samples. The 20 nm SiC nanoparticle-embedded sample shows greater photoabsorption in the UV and visible region with wavelengths of 233 and 518 nm, respectively, and a high PR in the visible spectra region with a wavelength 668 nm. High photoabsorption and low PR in the UV spectral region with wavelengths of 236 and 272 nm, respectively, were observed for the embedded 7 nm SiC nanoparticles but not for the 10 nm or 50 nm SiC nanoparticle-embedded samples. Furthermore, the 10 nm SiC nanoparticle-embedded sample shows higher photoabsorption in the UV to visible spectra region at wavelengths of 340–490 nm and the visible region at a wavelength of 541 nm to the IR region with a wavelength of 1015 nm. The 50 nm SiC-embedded sample shows low PR in the IR region compared to the sample embedded with 7 and 20 nm SiC. However, the reference sample shows the lowest PR at the longer IR spectral region. Among the SiC-embedded samples, the sample embedded with 50 nm SiC nanoparticles showed the lowest PR, indicating that smaller SiC nanoparticles have less contribution in the IR region above 1200 nm.
The red shift in PR with increasing the size from 7 to 50 nm is similar to the optical absorption in metal nanoparticles . However, for the photoluminescence of SiC nanoparticles, the blue shift of light emission happens as decreasing the size of nanoparticles with 3–5 nm indicating the quantum size effect . All samples show significant light absorption in the IR region at the wavelength of 1015 nm compared to the UV and visible region, which is related to the band gap property of Si. The very low PR from the visible to IR region with wavelengths of 540–1015 nm from the 7 nm SiC nanoparticle-embedded sample may occur due to the formed Si nanocrystals surrounded by SiC nanoparticles. However, in the same region, the sample embedded with 50 nm SiC nanoparticles shows a lower PR than the 7 and 20 nm SiC-embedded samples because of the mixed Si nanocrystals and nanoclusters. However, the 20 nm SiC nanoparticle-embedded sample shows the highest PR above the 668 nm wavelength compared to all of the samples, including the reference, which may be due to the silicon nanoclusters . However, the sample embedded with 7 nm SiC nanoparticles shows a lower PR than the 20 nm SiC-embedded sample at wavelengths of 603–751 nm, which indicates that the Si microcrystals absorb light better than the Si nanoclusters in that region.
The photoabsorption in the higher UV region depends on the 7, 10, and 50 nm SiC nanoparticles; however, the sample embedded with 20 nm SiC nanoparticles shows the greatest photoabsorption in the UV spectral region. The aberrant behaviour may be correlated with the thin film property shown in the Raman analysis, where the sample with the 20 nm SiC nanoparticles provides a highly crystalline phase without an amorphous phase, as shown in Figure 7. In comparison, the PR was reduced by 30% for the microtextured sample compared to the flat sample; however, the PR is more reduced in the UV/Vis wavelength than that of the reference sample for both cases. Therefore, the SiC nanoparticles play an important role in photoabsorption from the UV to visible spectral region compared to the conventional microtextured Si solar cell sample and are related to the spectral dependence on PR and the deposited Si thin film with Si nanocrystals that enhanced the photoabsorption in the IR region. Furthermore, in the same wavelength region, the PR of the Si/SiC/Si solar cell samples was reduced by more than 10% compared to that of only the SiC/Si cells, which may have occurred due to the Si nanocrystals . The PR in the UV spectral region is governed by the size of the nanoparticles; that is, the PR increased with an increase in nanoparticle size . The performance of the solar cells can be improved by these SiC nanoparticles with enhanced photoelectron generation due to their high permittivity and low dissipation energy level .
Various 3C-SiC nanoparticles sizes were sprayed onto Si solar cells surfaces and were embedded in Si thin film by PECVD. The deposited Si thin films showed the formation of micro- and nanocrystallites on the SiC nanoparticle sites, which play an important role of a heating block in the form of a nanosubstrate or a plasma-heated nanofurnace. The surface structure of all samples depends on the density of the corresponding SiC nanoparticles, and the thin films showed a mixed phase of amorphous and nanocrystalline Si in the Raman spectra. The nanoparticles showed reduced photoreflectance in the UV spectral region. The lowest PR was observed for the sample with the 20 nm SiC nanoparticles, which corresponds to only the nanocrystalline peak without the amorphous phase. The Si thin film samples showed very high PRs in the IR region. Therefore, the size-dependent 3C-SiC nanoparticles played an important role in photoabsorption in the UV to visible spectral regions.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.
This research was supported by the Basic Science Research Program through the National Research Foundation of Korea (NRF) funded by the Ministry of Education, Science and Technology (NRF (2010-0025598)).
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