# Electron Microscopy and Optical Characterization of Cadmium Sulphide Nanocrystals Deposited on the Patterned Surface of Diatom Biosilica

Authors: Timothy Gutu; Debra K. Gale; Clayton Jeffryes; Wei Wang; Chih-hung Chang; Gregory L. Rorrer; Jun Jiao
Journal: Journal of Nanomaterials
 (2009)

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## Abstract

Intricately patterned biosilica obtained from the shell of unicellular algae called diatoms serve as novel templates for fabrication of optoelectronic nanostructures. In this study, the surface of diatom frustules that possessed hierarchical architecture ordered at the micro and nanoscale was coated with a nanostructured polycrystalline cadmium sulphide (CdS) thin film using a chemical bath deposition technique. The CdS thin film was composed of spherical nanoparticles with a diameter of about 75 nm. The CdS nanoparticle thin film imparted new photoluminescent properties to the intricately patterned diatom nanostructure. The imparted photoluminescent properties were dependent on the CdS coverage onto the frustules surface. The intrinsic photoluminescent properties of the frustules were strongly quenched by the deposited CdS. The origin of PL spectra was discussed on the basis of the band theory and native defects.


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## Body

## 1. Introduction

The fabrication of nanomaterials with well-defined and controllable micro-to nanoscale features has been of great interest for chemical, optical, electronic, catalytic, environmental, and medical applications [1–3]. While bottom-up and top-down approaches have been extensively used to fabricate two-dimensional structures and devices, there is a need for inexpensive methods to  mass-produce complex micro-to nanoscale structures with a variety of three-dimensional (3D) morphologies at high degrees of precision, reproducibility, and chemical tailorability [4, 5] Nature is one inspirational source of nanostructures that can potentially meet this demand. For instance, diatoms are unicellular microalgae that form microscale silica cell walls called “frustules” which possess complex, intricately designed two- and three, dimensional nanopatterns.  These patterns are species-specific and are faithfully reproduced upon cellular reproduction [1, 6–8].The dielectric nature of the amorphous biosilica frustule has limited the use of these ornate nanostructures for optoelectronic device applications. Consequently, appreciable efforts have recently been underway to modify the silica, SiO2, into technologically more suitable functional materials while preserving the frustule shapes and morphologies. The frustule composition have been altered to or by functional materials such as TiO2, BaTiO3, SrTiO3, MgO, NiSO4, Zn2SiO4 : Mn,  Y2SiO5 : Eu3+, and silicon-germanium nanocomposites. Diatom frustules have also been chemically modified for the attachment of antibodies for medical applications. Sol-gel process, atomic layer deposition, chemical bath deposition, inkjet printing process, biosynthesis and low-temperature magnesiothermic reaction are some of the methods that have been used to modify the chemical composition of the frustules [9–16]. In this investigation, we explored a simple approach that utilized a scalable, low-cost chemical bath deposition (CBD) technique to coat the diatom biosilica frustule surface with a semiconductor thin film while preserving its shape and morphology [17]. Specifically, a cadmium sulphide (CdS) thin film was deposited, for the first time, onto the biosilica surface to impart optoelectronic properties to the frustule.  CdS is a direct band gap II–VI semiconductor with an average band gap of 2.42 eV at room temperature. It is widely used in photodetectors, solar cells, and many other optoelectronic device applications. The CdS/diatom biosilica nanocomposite structures, which consist of two-dimensional pore arrays ordered at the nano and submicron scales, may find potential application as sensors, photonic band gap materials, and a variety of other optoelectronic devices. A wide diversity in diatom species, each with a unique shape, size, pore size, and architecture, offers a huge selection for device and device applications [18, 19].


## 2. Experimental

Intact diatom biosilica was isolated from cell cultures of diatomPinnularia sp.using aqueous hydrogen peroxide treatment as previously described [8]. A CBD batch reactor with a bath solution of 600 mL was used to coat CdS onto the surface of the intact diatom biosilica frustules.  The bath solution contained cadmium chloride (CdCl2, 0.004 mol/L) as a source of cadmium ions, ammonium chloride (NH4Cl, 0.04 mol/L) buffer, thiourea ((NH2)2CS, 0.04 mol/L) as source of sulphide ions, and (29.3 wt %) ammonium hydroxide (NH4OH, 0.4 mol/L), to maintain the pH at 11. The precursor solutions were prepared separately as described by Chang [17]. The diatom frustule powder was added to the bath just after the addition of NH4OH, which initiated the chemical bath deposition reaction. The temperature of the bath was maintained at 80ºC. After 10 minutes of deposition, the batch reactor was removed from the heat source and the bath solution was diluted with 800 mL of de-ionized water to quench the reaction.  The supernatant was removed after about 10 minutes and the diatom frustules were washed with DI water and then stored in methanol. The chemical bath deposition of CdS thin film is based on the controlled precipitation of CdS in the bath. The slow release of the sulphide ions via the controlled hydrolysis of thiourea into the alkaline solution controls the precipitation reaction. When the ionic product, [Cd2+][S2−], exceeds the solubility product of CdS (≈10−25), the CdS precipitates at the surface of the substrate (frustules in this case) or in the solution according to the following reaction:(1)Cd2++S2-→CdS(s)The overall reaction is given by:(2)Cd(NH3)42++SC(NH2)2+2OH-→CdS+CH2N2+4NH3+2H2O.The surface morphology of the as-deposited CdS was analyzed using an FEI Sirion Field Emission Scanning Electron Microscope (FESEM). To prepare FESEM samples, one or two drops of diatom frustules dispersed in methanol were placed onto an ITO glass substrate, which was then fixed onto an Al stub. An accelerating voltage of 5 kV was used for imaging. An FEI Tecnai F20 Transmission Electron Microscope (TEM) was used to characterize the structure and elemental composition of the CdS coating. To make the diatom frustules electron transparent for the TEM characterization, the CdS-coated diatom frustules were ultrasonicated for about 30 minutes to break them up into smaller fragments.For photoluminescence (PL) measurements, the frustules were fixed onto a glass substrate by oxygen plasma treatment prior to CBD. Diatom frustules, dispersed in methanol, were placed onto a 2 cm× 1 cm glass slide using a pipette and then air dried. SEM was used to ensure that the glass substrate was completely covered with diatom frustules. The frustules on glass were then subjected to oxygen plasma in FISCHIONE model 1020 plasma cleaner for about 1.5 hours to allow the diatom frustules to form chemical bonds with the glass substrate. The glass substrate containing the adhered diatom frustules was then placed vertically in the bath solution. After deposition, any homogeneously formed CdS nanoparticles were flushed out by washing with DI water. These procedures ensured that only the PL of the heterogeneously deposited CdS film itself was measured. The excitation source for photoluminescence measurements was a 337 nm N2UV laser. All PL measurements were carried out at room temperature.


## 3. Results and Discussion

### 3.1. Morphology and Structure

Figure1 shows FESEM images for the typical surface morphology of intact frustule biosilica isolated from the diatom Pinnularia sp. Figures 1(a)–1(c) as well as intact diatom biosilica coated with CdS using the chemical bath deposition technique Figures 1(d)–1(i). Figures 1(d)–1(g) shows that the as-deposited CdS coating was dense and replicated the shape of the diatom frustule. Furthermore, there were no pinholes on the film, and the substrate surface coverage was compact, complete, granulated, and nanostructured.  There are three known modes of heteroepitaxial growth, namely, the Frank-van der Merwe (or layer-by-layer), the Stranski-Krastanow (or island growth) and combination of the two called layer-by-layer plus island. In the layer-by-layer growth mode, the particles are more strongly bound to the substrate than to each other and in the island growth mode, the particles are strongly bonded to each other than to the substrate [20].SEM images (a) Intact diatom Pinnularia sp., (b) Fine structures within pores are visible, (c) High resolution image of pore array with no fine structures, (d) Intact diatom coated with CdS, (e) CdS coating on a diatom with fine structures within the pores (f) CdS spherical particles clearly visible, (g)–(i) CdS deposited under different conditions (g) Precursor concentration of 1/16 the initial concentration, (h) Bath temperature at 70ºC and (i) CdS deposited on diatom fixed onto a glass substrate.
(a)(b)(c)(d)(e)(f)(g)(h)(i)It was assumed that the growth of the film occurred by a layer-by-layer growth mode where the smallest stable nuclei condense and extend the deposit in two dimensions across a surface. Figure1 showed that the CdS nanoparticles formed a two dimensional monolayer (thin film). This suggested that the CdS spherical nanoparticles were more strongly bound to the silica than to each other causing them to form a 2D structure (thin film due to layer-by-layer growth mode) instead of islands (3D structure due to island growth mode). Two experimental observations testify to the tight adherence of the CdS nanoparticles to the surface of the diatom frustules. Firstly, the CdS nanoparticles on the surface of the frustules remained intact after being subjected to high intensity ultrasonication for 30 minutes as previously mentioned in the experimental section. Secondly, the self-assembling or growth mode of the CdS particles (clusters) on the diatom surface also provides information on the adherence of the particles to the frustules and between the particles.  In Figures 1(c) and 1(h) the fine structures within the diatom pores are absent. This is not unexpected because some fine structures may fall off during the removal of organic matter on the diatom cell mass by oxidation with aqueous hydrogen peroxide. Though the removal of organic matter from the diatom cell mass by hydrogen peroxide is a gentile process, some small features of the frustules may be damaged or removed during the oxidation process. However, most frustules retained the fine structures during the oxidation process. The fine structures are preserved during the deposition of CdS on the frustules by the CBD method (Figures 1(g) and 1(i)).The optoelectronic, chemical and structural properties of nanomaterials are size-dependent. For instance, the absorption edge of CdS nanocrystals exhibits a blue shift due to quantum confinement effect [21]. The nanostructured CdS thin film was composed of spherical nanoparticles with a narrow particle size distribution (Figure 2). The particle size was measured using analySIS ® software. The average nanoparticle (cluster) size was 72 ± 6 nm. A few particles formed by a homogeneous precipitation reaction in the solution also adsorbed randomly onto the growing CdS thin film (shown by red arrow in Figure 1(g)). These particles were much larger than the nanoparticles heterogeneously formed on the diatom biosilica frustule surface.Figure 2
Bar graph showing nanoparticles size distribution.The physical  properties of the CdS thin film depended upon the chemical bath deposition conditions, including precursor concentration, bath temperature, and deposition time. Figure1(g) shows that the size of the spherical CdS nanoparticles decreased with decreasing cadmium chloride precursor concentration in the chemical deposition bath.  Most likely, increasing the cadmium precursor concentration increased the extent of adsorption of the chemical bath reagents and their complexes onto the frustule surface. This lead to an increase in the heterogeneous precipitation of CdS onto the surface, and was accompanied by a subsequent increase in particle size.  Furthermore, the  appearance of the CdS films changed as the precursor solution concentration increased, from a pale yellow color for the as-grown layer prepared with a low precursor concentration of 0.00 025 mol/L of CdCl2, to a strong orange color for films prepared with a high precursor concentration of 0.004 mol/L of CdCl2(16x initial precursor concentration). This change in color was attributed to the change in the size of the CdS nanoparticles.It was also found that the solution bath temperature and deposition time affected the CdS particle size and frustule surface coverage. Frustule surface coverage by CdS was incomplete at temperatures at or below 70ºC, even for an extended deposition time of 5 hours (Figure 1(h)). However, temperatures above 70ºC increased the extent of CdS deposition. The frustule surface coverage was incomplete for short deposition times of about 7 minutes or less. The particle size was found to decrease slightly with decreasing temperature and short deposition times.In order to achieve a more direct insight into the internal structural properties of the CdS thin film, TEM analysis was performed. Figure3 shows TEM images of the typical fine structure of the frustule biosilica from the diatom Pinnularia sp before and after the CBD process.  A TEM image of the diatom frustule microstructure before CBD is presented in Figure 3(a). As shown in Figure 3(b), after the CBD of CdS, the entire frustule microstructure is coated with spherical nanoparticles compactly deposited onto the frustule surface. In Figure 3(c), the randomly oriented crystal grains show that the CdS thin film is polycrystalline. A polycrystalline material is made up of grains of crystalline material where the grains are randomly oriented relative to each other. In HRTEM (Figures 3(c)–3(d)), grains appear as a regions with lattice fringes oriented in a random directions.  A region with lattice fringes in a particular direction is a grain. The average grain size is about 3 ± 1 nm. Fringe spacing of CdS obtained from Figure 3(c) are 0.367 nm in the [110] direction and 0.378 nm at 120º to the [110] direction.TEM images (a) Intact diatom frustule with no CdS coating, (b)–(d) CdS coated frustule; (a) Microstructure, (c) Nanostructure shows lattice fringes; insert shows the corresponding diffraction pattern, and (d) Stacking faults near the grain boundary.
(a)(b)(c)(d)The diffraction pattern (Figure3(c) insert) is composed of sharp, spotty, discontinuous rings which corroborates that the thin film is polycrystalline with well-defined crystalline grains. The (100), (002) or (111), (110), (200), (201), (203), (300) or (422), and (213) planes were observed in the SAD pattern which largely confirms that the CdS thin film was hexagonal. The interplanar distances (d) for the (hkl) planes were calculated using the relation d = Lλ/R where L is the camera constant, λ is the electron wavelength (=0.00 251 nm) and R is the radius of the diffracted ring. The interplanar distances calculated from diffraction patterns were 0.3526 nm, 0.3383 nm, 0.2077 nm, 0.1791 nm, 0.1730 nm, 0.1381 nm and 0.1195 nm and 0.1169 nm. Planar defects are also observed in the CdS thin film. Figure 3(d) shows the stacking faults near grain boundary of the (001) plane and the subsequent lattice structure distortions. In Figures 3(c) and 3(d), the abrupt changes in crystallographic direction of the lattice are clearly visible. The chemical composition of a CdS-coated frustule is shown by the TEM EDX spectrum in Figure 4. Si and O are from the diatom biosilica whereas Cd and S and are from the deposited CdS thin film.Figure 4
TEM EDX spectrum details the chemical composition of the CdS-coated frustule shown in the insert. The red dot is the spot where the chemical composition was taken.  The Cu peak is an artifact of the TEM grid.


### 3.2. Photoluminescence

Figure5 shows the PL spectra of both the uncoated frustules (A) centered at 457 nm and the CdS-coated (Insert (B)) frustules. Non-coated diatom frustules (A) possess some intrinsic blue photoluminescence, which is attributed to a variety of surface defects [22]. The broad PL peak spans from about 370 nm to about 700 nm, which makes this material unsuitable for applications that require narrow emission and high sensitivity, such as photodetectors. However, when the frustules were coated with CdS, a much sharper PL yellow emission peak (560 nm to 620 nm) centered at 588 nm (2.11 eV) emerged (Figure 5b). This new peak is associated with radiative transitions from the donor levels, arising from Cd atoms located in interstitial sites, to the valence band [23]. A tiny peak centered at 665 nm (1.87 eV) was also observed on the CdS-coated diatom frustules. This red band is ascribed to either sulphur vacancy states or transition of bound electrons from surface states to the valence band [24]. The average particle diameter of the CdS nanoparticles for the PL samples used to obtain results in Figure 5 was about 35 ± 6 nm. The CdS nanoparticles deposited directly onto the glass substrate were smaller and less dense than the CdS nanoparticles on the diatoms. This suggests that precipitation of CdS on the frustules was more favored than the precipitation on the glass substrate. SEM analysis showed that the regions with CdS-coated frustules had a deeper color contrast than those with no or less frustules.  The CdS nanoparticle density onto the surface of the frustules for the specimen used to obtain the PL signal in Figure 5 (B) was less than 25% as shown in Figure 1(i) and did not have any considerable effect the 457 nm PL signal. However, a significant change in the frustules PL properties was observed when the CdS nanoparticle coverage onto the frustules’ surface was complete. The CdS frustule coverage was improved by either increasing the bath deposition temperature to about 100ºC or by doubling the precursor concentrations.Figure 5
Photoluminescence spectra of diatom frustules.  (A) refers to diatom biosilica before CdS deposition, (B) refers to diatom biosilica after CdS deposition.Figure6 showed that the intrinsic photoluminescence of the frustules were totally quenched as shown by the disappearance of the broad PL signal from the diatom silica which was centered at 457 nm. This suggests that the PL signals are coming solely from the CdS thin film deposited on the biosilica and can therefore be interpreted by considering PL properties of CdS thin films. This result is in agreement with results obtained by Andsager et al.  who showed how PL was affected by the deposition of metals upon silica [25]. Metals such as copper, silver and gold were found to quench the PL when deposited on luminescent porous silica.Figure 6
Photoluminescence spectrum of diatom frustules with complete CdS coverage onto the surface of the frustule.Figure7 shows the possible emission bands observed in the visible region for the as-deposited CdS thin films. Several interesting prominent PL peaks spanning the visible spectral region were observed. The green emission peak at about 495 nm (2.51 eV) corresponds to the CdS direct band gap. This was further confirmed by separate optical transmission experiments (results not included in this paper). There are three explanations about the origins of the green emission band, namely, recombination of trapped electrons from a donor level with free holes, or recombination of free electrons from the conduction band with holes in the acceptor levels and recombination of electrons from a donor level with holes trapped on the acceptor level [26, 27]. The green emission band peak at 545 nm (2.28 eV) is attributed to excitation from interstitial sulphur (IS) to conduction band.Figure 7
Schematic energy level diagram for the different electronic transitions observed in CdS deposited on diatom frustules.The yellow band emission peak at 588 nm, as previously explained, is due to transitions from the interstitial cadmium (ICd)donor level to the valence band. An orange band emission peak was observed at about 613 nm (2.02 eV). This peak is ascribed transitions of ICd donor level to acceptor levels. The intensity of the green (2.28 eV) and the orange emission peaks was much stronger than that of the yellow emission peak. Three prominent red emission peaks were observed at 708 nm (1.76 eV), 745 nm (1.67 eV) and 772 nm (1.61 eV). These are ascribed to sulphur vacancies (VS) or surface states as previously said. The surface states increases with improved CdS coverage onto the frustules and thus led to appearance of the red emission bands with enhanced intensity. The 665 nm peak was not observed for samples with complete biosilica (frustule) substrate coverage. It is important to note that increasing CdS coverage onto frustules by increasing deposition temperature or by increasing precursor concentrations also caused an increase in cluster size from about 35 nm to about 100 nm and hence increased CdS thin film thickness. Tsai et al showed that the peak positions of the red and yellow emission bands were blue-shifted as the CdS film become thinner [28]. He also reported that the intensity of the emissions peaks was affected by the grain size.


## 3.1. Morphology and Structure

Figure1 shows FESEM images for the typical surface morphology of intact frustule biosilica isolated from the diatom Pinnularia sp. Figures 1(a)–1(c) as well as intact diatom biosilica coated with CdS using the chemical bath deposition technique Figures 1(d)–1(i). Figures 1(d)–1(g) shows that the as-deposited CdS coating was dense and replicated the shape of the diatom frustule. Furthermore, there were no pinholes on the film, and the substrate surface coverage was compact, complete, granulated, and nanostructured.  There are three known modes of heteroepitaxial growth, namely, the Frank-van der Merwe (or layer-by-layer), the Stranski-Krastanow (or island growth) and combination of the two called layer-by-layer plus island. In the layer-by-layer growth mode, the particles are more strongly bound to the substrate than to each other and in the island growth mode, the particles are strongly bonded to each other than to the substrate [20].SEM images (a) Intact diatom Pinnularia sp., (b) Fine structures within pores are visible, (c) High resolution image of pore array with no fine structures, (d) Intact diatom coated with CdS, (e) CdS coating on a diatom with fine structures within the pores (f) CdS spherical particles clearly visible, (g)–(i) CdS deposited under different conditions (g) Precursor concentration of 1/16 the initial concentration, (h) Bath temperature at 70ºC and (i) CdS deposited on diatom fixed onto a glass substrate.
(a)(b)(c)(d)(e)(f)(g)(h)(i)It was assumed that the growth of the film occurred by a layer-by-layer growth mode where the smallest stable nuclei condense and extend the deposit in two dimensions across a surface. Figure1 showed that the CdS nanoparticles formed a two dimensional monolayer (thin film). This suggested that the CdS spherical nanoparticles were more strongly bound to the silica than to each other causing them to form a 2D structure (thin film due to layer-by-layer growth mode) instead of islands (3D structure due to island growth mode). Two experimental observations testify to the tight adherence of the CdS nanoparticles to the surface of the diatom frustules. Firstly, the CdS nanoparticles on the surface of the frustules remained intact after being subjected to high intensity ultrasonication for 30 minutes as previously mentioned in the experimental section. Secondly, the self-assembling or growth mode of the CdS particles (clusters) on the diatom surface also provides information on the adherence of the particles to the frustules and between the particles.  In Figures 1(c) and 1(h) the fine structures within the diatom pores are absent. This is not unexpected because some fine structures may fall off during the removal of organic matter on the diatom cell mass by oxidation with aqueous hydrogen peroxide. Though the removal of organic matter from the diatom cell mass by hydrogen peroxide is a gentile process, some small features of the frustules may be damaged or removed during the oxidation process. However, most frustules retained the fine structures during the oxidation process. The fine structures are preserved during the deposition of CdS on the frustules by the CBD method (Figures 1(g) and 1(i)).The optoelectronic, chemical and structural properties of nanomaterials are size-dependent. For instance, the absorption edge of CdS nanocrystals exhibits a blue shift due to quantum confinement effect [21]. The nanostructured CdS thin film was composed of spherical nanoparticles with a narrow particle size distribution (Figure 2). The particle size was measured using analySIS ® software. The average nanoparticle (cluster) size was 72 ± 6 nm. A few particles formed by a homogeneous precipitation reaction in the solution also adsorbed randomly onto the growing CdS thin film (shown by red arrow in Figure 1(g)). These particles were much larger than the nanoparticles heterogeneously formed on the diatom biosilica frustule surface.Figure 2
Bar graph showing nanoparticles size distribution.The physical  properties of the CdS thin film depended upon the chemical bath deposition conditions, including precursor concentration, bath temperature, and deposition time. Figure1(g) shows that the size of the spherical CdS nanoparticles decreased with decreasing cadmium chloride precursor concentration in the chemical deposition bath.  Most likely, increasing the cadmium precursor concentration increased the extent of adsorption of the chemical bath reagents and their complexes onto the frustule surface. This lead to an increase in the heterogeneous precipitation of CdS onto the surface, and was accompanied by a subsequent increase in particle size.  Furthermore, the  appearance of the CdS films changed as the precursor solution concentration increased, from a pale yellow color for the as-grown layer prepared with a low precursor concentration of 0.00 025 mol/L of CdCl2, to a strong orange color for films prepared with a high precursor concentration of 0.004 mol/L of CdCl2(16x initial precursor concentration). This change in color was attributed to the change in the size of the CdS nanoparticles.It was also found that the solution bath temperature and deposition time affected the CdS particle size and frustule surface coverage. Frustule surface coverage by CdS was incomplete at temperatures at or below 70ºC, even for an extended deposition time of 5 hours (Figure 1(h)). However, temperatures above 70ºC increased the extent of CdS deposition. The frustule surface coverage was incomplete for short deposition times of about 7 minutes or less. The particle size was found to decrease slightly with decreasing temperature and short deposition times.In order to achieve a more direct insight into the internal structural properties of the CdS thin film, TEM analysis was performed. Figure3 shows TEM images of the typical fine structure of the frustule biosilica from the diatom Pinnularia sp before and after the CBD process.  A TEM image of the diatom frustule microstructure before CBD is presented in Figure 3(a). As shown in Figure 3(b), after the CBD of CdS, the entire frustule microstructure is coated with spherical nanoparticles compactly deposited onto the frustule surface. In Figure 3(c), the randomly oriented crystal grains show that the CdS thin film is polycrystalline. A polycrystalline material is made up of grains of crystalline material where the grains are randomly oriented relative to each other. In HRTEM (Figures 3(c)–3(d)), grains appear as a regions with lattice fringes oriented in a random directions.  A region with lattice fringes in a particular direction is a grain. The average grain size is about 3 ± 1 nm. Fringe spacing of CdS obtained from Figure 3(c) are 0.367 nm in the [110] direction and 0.378 nm at 120º to the [110] direction.TEM images (a) Intact diatom frustule with no CdS coating, (b)–(d) CdS coated frustule; (a) Microstructure, (c) Nanostructure shows lattice fringes; insert shows the corresponding diffraction pattern, and (d) Stacking faults near the grain boundary.
(a)(b)(c)(d)The diffraction pattern (Figure3(c) insert) is composed of sharp, spotty, discontinuous rings which corroborates that the thin film is polycrystalline with well-defined crystalline grains. The (100), (002) or (111), (110), (200), (201), (203), (300) or (422), and (213) planes were observed in the SAD pattern which largely confirms that the CdS thin film was hexagonal. The interplanar distances (d) for the (hkl) planes were calculated using the relation d = Lλ/R where L is the camera constant, λ is the electron wavelength (=0.00 251 nm) and R is the radius of the diffracted ring. The interplanar distances calculated from diffraction patterns were 0.3526 nm, 0.3383 nm, 0.2077 nm, 0.1791 nm, 0.1730 nm, 0.1381 nm and 0.1195 nm and 0.1169 nm. Planar defects are also observed in the CdS thin film. Figure 3(d) shows the stacking faults near grain boundary of the (001) plane and the subsequent lattice structure distortions. In Figures 3(c) and 3(d), the abrupt changes in crystallographic direction of the lattice are clearly visible. The chemical composition of a CdS-coated frustule is shown by the TEM EDX spectrum in Figure 4. Si and O are from the diatom biosilica whereas Cd and S and are from the deposited CdS thin film.Figure 4
TEM EDX spectrum details the chemical composition of the CdS-coated frustule shown in the insert. The red dot is the spot where the chemical composition was taken.  The Cu peak is an artifact of the TEM grid.


## 3.2. Photoluminescence

Figure5 shows the PL spectra of both the uncoated frustules (A) centered at 457 nm and the CdS-coated (Insert (B)) frustules. Non-coated diatom frustules (A) possess some intrinsic blue photoluminescence, which is attributed to a variety of surface defects [22]. The broad PL peak spans from about 370 nm to about 700 nm, which makes this material unsuitable for applications that require narrow emission and high sensitivity, such as photodetectors. However, when the frustules were coated with CdS, a much sharper PL yellow emission peak (560 nm to 620 nm) centered at 588 nm (2.11 eV) emerged (Figure 5b). This new peak is associated with radiative transitions from the donor levels, arising from Cd atoms located in interstitial sites, to the valence band [23]. A tiny peak centered at 665 nm (1.87 eV) was also observed on the CdS-coated diatom frustules. This red band is ascribed to either sulphur vacancy states or transition of bound electrons from surface states to the valence band [24]. The average particle diameter of the CdS nanoparticles for the PL samples used to obtain results in Figure 5 was about 35 ± 6 nm. The CdS nanoparticles deposited directly onto the glass substrate were smaller and less dense than the CdS nanoparticles on the diatoms. This suggests that precipitation of CdS on the frustules was more favored than the precipitation on the glass substrate. SEM analysis showed that the regions with CdS-coated frustules had a deeper color contrast than those with no or less frustules.  The CdS nanoparticle density onto the surface of the frustules for the specimen used to obtain the PL signal in Figure 5 (B) was less than 25% as shown in Figure 1(i) and did not have any considerable effect the 457 nm PL signal. However, a significant change in the frustules PL properties was observed when the CdS nanoparticle coverage onto the frustules’ surface was complete. The CdS frustule coverage was improved by either increasing the bath deposition temperature to about 100ºC or by doubling the precursor concentrations.Figure 5
Photoluminescence spectra of diatom frustules.  (A) refers to diatom biosilica before CdS deposition, (B) refers to diatom biosilica after CdS deposition.Figure6 showed that the intrinsic photoluminescence of the frustules were totally quenched as shown by the disappearance of the broad PL signal from the diatom silica which was centered at 457 nm. This suggests that the PL signals are coming solely from the CdS thin film deposited on the biosilica and can therefore be interpreted by considering PL properties of CdS thin films. This result is in agreement with results obtained by Andsager et al.  who showed how PL was affected by the deposition of metals upon silica [25]. Metals such as copper, silver and gold were found to quench the PL when deposited on luminescent porous silica.Figure 6
Photoluminescence spectrum of diatom frustules with complete CdS coverage onto the surface of the frustule.Figure7 shows the possible emission bands observed in the visible region for the as-deposited CdS thin films. Several interesting prominent PL peaks spanning the visible spectral region were observed. The green emission peak at about 495 nm (2.51 eV) corresponds to the CdS direct band gap. This was further confirmed by separate optical transmission experiments (results not included in this paper). There are three explanations about the origins of the green emission band, namely, recombination of trapped electrons from a donor level with free holes, or recombination of free electrons from the conduction band with holes in the acceptor levels and recombination of electrons from a donor level with holes trapped on the acceptor level [26, 27]. The green emission band peak at 545 nm (2.28 eV) is attributed to excitation from interstitial sulphur (IS) to conduction band.Figure 7
Schematic energy level diagram for the different electronic transitions observed in CdS deposited on diatom frustules.The yellow band emission peak at 588 nm, as previously explained, is due to transitions from the interstitial cadmium (ICd)donor level to the valence band. An orange band emission peak was observed at about 613 nm (2.02 eV). This peak is ascribed transitions of ICd donor level to acceptor levels. The intensity of the green (2.28 eV) and the orange emission peaks was much stronger than that of the yellow emission peak. Three prominent red emission peaks were observed at 708 nm (1.76 eV), 745 nm (1.67 eV) and 772 nm (1.61 eV). These are ascribed to sulphur vacancies (VS) or surface states as previously said. The surface states increases with improved CdS coverage onto the frustules and thus led to appearance of the red emission bands with enhanced intensity. The 665 nm peak was not observed for samples with complete biosilica (frustule) substrate coverage. It is important to note that increasing CdS coverage onto frustules by increasing deposition temperature or by increasing precursor concentrations also caused an increase in cluster size from about 35 nm to about 100 nm and hence increased CdS thin film thickness. Tsai et al showed that the peak positions of the red and yellow emission bands were blue-shifted as the CdS film become thinner [28]. He also reported that the intensity of the emissions peaks was affected by the grain size.


## 4. Conclusion

In conclusion, this study shows that a simple and inexpensive chemical deposition process can be utilized to coat intricately patterned diatom frustules biosilica with optoelectronic semiconductor thin films. Specifically, biosilica frustules from the diatomPinnularia sp. were coated with a polycrystalline CdS thin film, and photoluminescence measurements showed that the highly ordered structure of the diatom frustules now possessed a sharp yellow emission band centered at 2.11 eV for CdS nanoparticles with a density of less than 25% on frustules surface. The photoluminescence was found to depend on the morphology and silica coverage of CdS onto the biosilica. Green, yellow, orange, and red emission bands were observed for high density of CdS nanoparticles on frustules’ surface. The origins of the photoluminescent spectra were explained successfully on the basis of the band theory and native defects. The study illustrates the exciting opportunities for manipulating the structure and properties of diatom frustules on a nanometer scale using chemical bath deposition techniques. The use of diatom frustules as biotemplates to produce micro-to nanostructures with controllable optoelectronic properties opens the possibility of fabricating tunable optoelectronic sensors and device.



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*Source: 860536-2009-05-07.xml*