# Influence of Buffer Agent Concentration on the Optical Properties from CdS Nanocrystals on Silicon Nanoporous Pillar Array

Authors: Peng Fei Ji; Wei Fen Jiang; Yong Li; Yue Li Song; Ming Li Wan; Feng Qun Zhou
Journal: Journal of Nanotechnology
 (2015)

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## Abstract

The chemical bath deposition (CBD) method is very crucial to the reaction rate. Generally, the rate can be controlled through tuning buffer agent concentration. CdS nanocrystals on the silicon nanoporous pillar array (CdS/Si-NPA) have been prepared through the CBD method. By varying the buffer agent concentration, the reaction rates can be tuned. The diffraction peaks of hexagonal CdS and Cd can be observed due to the reduction of Cd2+ caused by the silicon nanoporous pillar array. The average size of CdS nanocrystals is decreased with the increasing buffer agent concentration and the optical band gaps from CdS nanocrystals are increased. From the photoluminescence of CdS/Si-NPA, it can be observed that the blue emissions are independent of the buffer agent concentration and the green emissions show blue shift with the increasing buffer agent concentration.


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## Body

## 1. Introduction

Nanocrystal semiconductors have been a subject of more attention due to their important physical and chemical properties compared to the bulks. Current research on nanocrystals is focused on the fabrication method, the origins of photoluminescence, and the tune of band gaps [1, 2]. According to the quantum size effect, the band gap is dependent on the size of nanocrystals below certain size [3, 4]. Through varying the growth condition and environment, the size of nanocrystals can be controlled and then the optical properties can be tuned.CdS is an important semiconductor with a direct band gap of ~2.40 eV at room temperature, which can be fabricated through the solvothermal, hydrothermal, and physical/chemical vapor deposition and chemical bath deposition (CBD) methods [5–9]. Based on high sensitivity and effect photophysical properties, CdS is suitable for the applications in the fields of photodetectors, light-emitting diodes, lasers, and solar cells [10–12]. In our previous works, we have synthesized CdS nanocrystals on the silicon nanoporous pillar array (CdS/Si-NPA) by the CBD method. Based on CdS/Si-NPA, light-emitting diodes and photovoltaic devices have been investigated [13, 14]. However, the low quantum efficiency and energy conversion efficiency can be observed. For these devices a detailed knowledge of the defects and band gap for CdS nanocrystals is essential. Generally photoluminescence (PL) experiments have been utilized to investigate the defects and band gap in the field of nanocrystals semiconductors.In this paper, CdS/Si-NPA has been fabricated through the CBD method. To investigate the evolution of size and optical properties, the buffer agent with difference concentration, respectively, has been added to the reaction solution. With the increasing buffer agent concentration, Cd nanocrystals have been observed. The optical properties from CdS/Si-NPA with the increasing buffer agent concentration have been discussed in detail.


## 2. Experiments

Si-NPA was prepared by hydrothermally etching (111) oriented, p-type single crystal silicon (sc-Si) wafers in the aqueous solution of hydrofluoric acid containing ferric nitrate, the procedure and conditions of which have been described in detail elsewhere [15]. The CdS thin film was deposited on Si-NPA by a CBD method and the preparing procedures were described as follows. The bath solution was prepared by mixing the solutions of cadmium chloride (0.04 mol L−1, 75 mL) and aqueous ammonia (25–28%, 15 mL). The solution was kept at 80°C for 60 minutes under continuous magnetic agitation to homogenize the mixture. Subsequently, 5 mL thiourea (2.0 mol L−1) was added to the mixed solution. Five minutes later, Si-NPA substrate was immersed in the solution for 40 min to grow CdS thin films. Then the sample was taken out of the solution, washed with deionized water and ethanol in turn, and dried in the nitrogen flow.In the above experiment process, after the thiourea was added to the solution the yellow flocculent precipitate can be seen by naked eyes. The faster reaction process introduced a large number of defects into the CdS nanocrystals [16] and decreased the physical properties of the devices based on these CdS nanocrystals [17]. To increase the quality of CdS nanocrystals, the reaction process must be slowed. In the chemical reaction process, ammonium chloride (NH4Cl) was used as a buffering agent to slow down the chemical reaction rate. So, we added 5 mL 0.05 mol/L, 0.1 mol/L, and 0.15 mol/L ammonium chloride to the solution before the thiourea was added, respectively. The other processes were the same as the above ones.The morphology and structures of as-prepared CdS/Si-NPA were characterized by a field-emission scanning electron microscope (FE-SEM, JSM 6700F) and a powder X-ray diffractometer (XRD, Panalytical X′Pert Pro) using CuKα as the X-ray source (λ=1.5046 Å), respectively. The integral diffuse reflection spectra of CdS/Si-NPA were measured with UV-vis-IR spectrophotometer (Shimadzu, UV-3150) equipped with an integrating sphere. The room-temperature PL was measured using a double grating spectrofluorometer (HORIBA Jobin Yvon, FL3-22) with Xe lamp as an excitation source.


## 3. Results and Discussions

To investigate the structures of CdS/Si-NPA, the XRD spectra of the samples with the different concentration of buffer agent are shown in Figure1, respectively. The spectra are normalized according to the intensity of the strongest diffraction peak self. As can be seen from Figure 1, the XRD spectrum of CdS/Si-NPA with no buffer agent shows three stronger peaks, which are located at 26.65°, 44.16°, and 52.38°, that can be indexed to the reflections from the crystal family planes of hexagonal CdS (002), (110), and (112), respectively. To CdS/Si-NPA with the buffer agent, however, two sets of diffraction peaks can be observed in each spectrum, which are indexed to the diffractions from hexagonal CdS and hexagonal Cd, respectively. Obviously, the peaks located at 31.72°, 34.69°, and 38.39° can correspond to the reflections from the crystal family planes of Cd (002), (100), and (101), respectively.Figure 1
XRD patterns of CdS/Si-NPA with the buffer agent concentration of 0 mol L−1, 0.05 mol L−1, 0.10 mol L−1, and 0.15 mol L−1.From Figure1, it can be seen that the full width at half maximum (FWHM) of the (002) diffraction peaks for CdS nanocrystals is increased correspondingly with the increasing concentration of buffer agent. According to the principle of XRD, the increase of FWHM might reflect the decrease of the average size of nanocrystals [13]. Based on Scherrer’s formula [6] and the data corresponding to the (002) diffraction peaks, the average sizes of CdS nanocrystals with the different concentration of buffer agent are calculated as ~26.9 nm, ~19.2 nm, ~11.6 nm, and ~8.1 nm, respectively. Obviously, the average size of CdS nanocrystals is decreasing with the increasing concentration of buffer agent. As for the diffraction from Cd, it is easily found that its relative intensities gradually increase with the concentration of buffer agent. These can be explained from the increasing film thickness. As we know, CdS nanocrystals are located at the interface of nc-CdS and Si-NPA [9, 13, 14]. Then, the thicker CdS films impede the penetration of X-ray into nc-Cd and lead to the decrease of the diffraction peak intensity from Cd nanocrystallites.The surface of Si-NPA usually exhibits strong chemical reducibility and can directly reduce metal ions from their solution [18]. The similar reduction process might also occur to form Cd nanocrystals, as follows: Cd2+ + e− → Cd. With the increasing concentration of buffer agent, the reaction rate is more and more slower and the thickness of CdS films becomes more and more thinner at the same deposition time. So, the surface of Si-NPA will be insulated gradually from the cadmium ions in the solution and prevent further deposition or growing of Cd. Therefore, the growing of Cd is a self-limited process which mainly occurs at the initial stage of the CBD process.The morphologies of prepared CdS/Si-NPA with the different concentration of buffer agent are displayed in Figure2. Obviously, the characteristic of the regular array of Si-NPA is maintained in CdS/Si-NPA [15], and both the pillars and the valleys are covered by the CdS films. From Figure 2(a), some flocculation and big size particles can be observed and pell-mell pilled on the pillars and between the pillars and valleys. From the analysis of XRD data, it is known that the average sizes of CdS nanocrystals are in the range of 8.0 nm and 30 nm. Therefore, we think that the flocculation and big size particles should be the agglomerates of CdS nanocrystals. With increasing the buffer agent concentration, the flocculation is vanished and the size of the particles is decreasing. Under the buffer agent concentration of 0.10 mol L−1, the average size of particles is ~190 nm [13]. However, with the concentration of 0.15 mol L−1 the average size of particles is estimated to be ~110 nm and CdS thin films can be observed to be uniformly covered on the pillars and valleys.Figure 2
SEM images of CdS/Si-NPA, (a) 0 mol L−1, (b) 0.05 mol L−1, (c) 0.10 mol L−1, and (d) 0.15 mol L−1.
(a)
(b)
(c)
(d)The optical absorption of prepared CdS/Si-NPA with the different concentration for buffer agent is showed in Figure3(a). As can be seen, with the increasing concentration the absorption is increasing. It is obvious that the absorption spectra have the gradual variation of absorption edge between ~450 nm and ~590 nm, and the wider absorption bands indicate that the size distribution of CdS nanocrystals is much bigger. The value of optical band gap can be determined from the absorption using Tauc’s relation [19]: (1)αhνn=Bhν-Eg.Here, α is the absorption coefficient, B is the characteristic parameter independent of photon energy, hν is the incident photon energy, Eg is the optical band gap, and n is a constant which depends on the nature of the transition between the valance band and conduction band, for CdS n=2. The evolution of αhν2 versus hν is displayed in Figure 3(b), and the obtained optical band gaps are ~2.22 eV (~559 nm), ~2.37 eV (~523 nm), ~2.39 eV (~519 nm), and ~2.46 eV (~504 nm) for the buffer agent concentration of 0 mol L−1, 0.05 mol L−1, 0.10 mol L−1, and 0.15 mol L−1, respectively.Figure 3
(a) Absorption of CdS/Si-NPA, (b) the plots of(αhν)2 versus hν.
(a)
(b)In order to deeply understand the effect of buffer agent concentration for CdS/Si-NPA on the optical properties, the room temperature photoluminescence with the different concentration is shown in Figure4(a). The broad blue and green emission bands can be observed. With the increasing buffer agent concentration, the ratios of green versus blue emission intensity are ~3.57, ~1.25, ~0.93, and ~0.69, respectively. It can be seen from Figure 4(a) that the peaks of green emissions show blue shift. PL spectra can be decomposed into two peaks utilizing Gauss-Newton fitting method. The development of the blue and green energy with the increasing buffer agent concentration is shown in Figure 4(b). The blue emission energy is ~2.87 eV, ~2.73 eV, ~2.84 eV, and ~2.83 eV for the agent buffering concentration of 0 mol L−1, 0.05 mol L−1, 0.10 mol L−1, and 0.15 mol L−1, respectively. For the green emissions the peak energy is ~2.16 eV for 0 mol L−1, ~2.27 eV for 0.05 mol L−1, ~2.40 eV for 0.10 mol L−1, and ~2.44 eV for 0.15 mol L−1, respectively.Figure 4
(a) Photoluminescence of CdS/Si-NPA, (b) peak energy of blue and green emissions.
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(b)In the previous works, the blue emissions from CdS/Si-NPA can be ascribed to the luminescence of Si-NPA substrate [9, 20, 21], which originates from the silicon oxide layer [22]. The evolution of blue emission peaks is illustrated in Figure 4(b) and observed to be irregular. Through analyzing the data, a linear fit can be obtained with the tiny slop of ~−0.01 meV per mol L−1, which indicates that the peak energy of blue emissions is hardly dependent on the buffer agent concentration. The average peak energy is ~2.82 eV (~440 nm) which is consistent with the previous results [15]. The green emissions originate from the near band gap of CdS nanocrystals [9, 14, 23]. With the increasing buffer agent concentration, the peak energy of green emissions gradually increases. Namely, the green emissions show blue shift with the increasing buffer agent concentration. The variation of green emissions is consistent with the results from the absorption using Tauc’s relation. According to the quantum size effect, the smaller the CdS nanocrystals, the wider the band gap. It is indicated that with the increasing buffer agent concentration the average size of CdS nanocrystals is gradually decreased, and the band gap can be tuned. Therefore the idea through varying the concentration of buffer agent is an optional approach to tune the band gap and size of CdS nanocrystals grown by CBD method.


## 4. Conclusion

In summary, we have prepared CdS/Si-NPA with the buffer agent concentration of 0 mol L−1, 0.05 mol L−1, 0.10 mol L−1, and 0.15 mol L−1, respectively, through the CBD method. In the XRD spectra of CdS/Si-NPA with the buffer agent, the diffraction peaks of hexagonal CdS and Cd can be observed due to the reduction of Cd2+ caused by the Si-NPA. With the increasing buffer agent concentration, the average size of CdS nanocrystals is decreased and the optical band gaps are increased. The blue emissions of CdS/Si-NPA originate from the Si-NPA and are independent of the buffer agent concentration; however, the green emissions show blue shift with the increasing buffer agent concentration.



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*Source: 246086-2015-11-01.xml*