Peculiarities of Photoluminescence in Porous Silicon Prepared by Metal-Assisted Chemical Etching

Iatsunskyi, Igor; Smyntyna, Valentin; Pavlenko, Nykolai; Sviridova, Olga

doi:https://doi.org/10.5402/2012/958412

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Research Article | Open Access

Volume 2012 | Article ID 958412 | https://doi.org/10.5402/2012/958412

Peculiarities of Photoluminescence in Porous Silicon Prepared by Metal-Assisted Chemical Etching

Igor Iatsunskyi,¹Valentin Smyntyna,¹Nykolai Pavlenko,¹and Olga Sviridova¹

Academic Editor: L. R. P. Kassab, Y. S. Kivshar

Received16 Aug 2012

Accepted24 Sept 2012

Published01 Nov 2012

Abstract

Photoluminescent (PL) porous layers were formed on p-type silicon by a metal-assisted chemical etching method using H₂O₂ as an oxidizing agent. Silver particles were deposited on the (100) Si surface prior to immersion in a solution of HF and H₂O₂. The morphology of the porous silicon (PS) layer formed by this method was investigated by atomic force microscopy (AFM). Depending on the metal-assisted chemical etching conditions, the macro- or microporous structures could be formed. Luminescence from metal-assisted chemically etched layers was measured. It was found that the PL intensity increases with increasing etching time. This behaviour is attributed to increase of the density of the silicon nanostructure. It was found the shift of PL peak to a green region with increasing of deposition time can be attributed to the change in porous morphology. Finally, the PL spectra of samples formed by high concentrated solution of AgNO₃ showed two narrow peaks of emission at 520 and 550 nm. These peaks can be attributed to formation of AgF and AgF₂ on a silicon surface.

1. Introduction

The indirect band-gap structure of silicon strongly restricts its application in the area of optoelectronics. The indirect transition that requires the participation of phonons leads to the low radiative recombination efficiency and the poor luminescence property. Many efforts have been carried out to solve this physical inability. One of the possible candidate systems is silicon nanostructures such as porous silicon (PS) [1, 2], silicon nanocrystallines (SiNCs) [3–5], and silicon nanowires (SiNWs) [6, 7]. The remarkable characteristics of visible photoluminescence (PL) in porous silicon at room temperature have given great impulse to these material studies [8–10].

PL from porous silicon is observable at wavelengths ranging from ultraviolet to the infrared. PS prepared using the electrochemical method shows strong visible emission, which is considered to originate from the quantum wires in the samples. The color of luminescence light could be well controlled by the variation of the size of the SiNCs. Various mechanisms, such as quantum confinement effect, surface state, and defect-center luminescence, were proposed to uncover the luminescence origins of PS and SiNCs. It is now generally agreed that various mechanisms are responsible for the different PL bands [11, 12].

Recently, a new method, termed metal-assisted chemical etching, has been developed, which is relatively simple compared to the electrochemical method. The method does not need an external bias and enables a formation of uniform PS layers more rapidly than the conventional stain etching method. Thin metallic films or particles (Au, Pt, Al, Pd, etc.) are generally deposited directly on a silicon surface prior to immersion in an etchant composed of HF and an oxidizing agent [13, 14]. Metal-assisted chemical etching is essentially a wet etching method yet produces anisotropic high aspect ratio semiconductor micro and nanostructures without incurring lattice damage. These high aspect ratio structures can potentially be used for the formation of periodic nanostructures for photonic crystals, light-trapping structures for LEDs and solar cells with better absorption and collection efficiency, and in other applications.

In present paper, we report on the formation of visible-light-emitting layers on porous p-type silicon using H₂O₂ as an oxidizing agent and silver (Ag) as deposited metal. We discuss the etching time dependence on the morphology of PS layers and the PL peak intensity. The changes in the PL spectrum are attributed to the structural modifications of PS layers caused by etching procedure. Besides, we have observed two narrow PL peaks, which can be associated with formation of new phase or material.

2. Experimental Procedure

Metal-assisted chemical etching (MaCE) is fundamentally a wet etch technique. MaCE was first used as an electroless etching technique to produce porous Si and porous III–V compound semiconductor by Li et al. in 2000 and 2002, respectively [15, 16], in contrast to the conventional anodic etching method for porous semiconductor formation. Details on the MaCE mechanism and development can be found elsewhere [17, 18].

The metal-assisted chemical etching processes were applied to p-type Si wafers Czochralski-grown (100) 100 Ohmcm. After standard RCA cleaning, the wafers were cleaned with acetone and deionized water via ultrasonic cleaning. A thin oxide layer was formed, and the surface became hydrophilic. This oxide layer was removed by dipping the samples into a dilute HF solution. The silver particles, which act as catalysts to assist the etching of silicon, were deposited on Si samples by immersion in 0.23 M HF and 5 × 10⁻⁵ M AgNO₃ (samples series no. 1) and in 0.23 M HF and 10⁻³ M AgNO₃ (samples series no. 2) metallization aqueous solutions. The time of immersion was varied between 0.5 to 30 minutes. After the electroless metallization, the wafers were etched in aqueous solutions containing HF (40%), H₂O₂ (30%), and ultrapure H₂O at different concentration ratios and for etching times varied from 1 to 30 minutes. After etching, the samples were rinsed with deionized water. The etching and immersion procedures were performed at room temperature.

Structural properties of porous silicon prepared by metal-assisted chemical etching have been investigated by Atomic Force Microscope (AFM) NT-206. AFM studies were done at atmospheric conditions. Using AFM, we could characterize the shape and sizes of isolated particles, their distribution depending on the chemicals conditions.

The luminescence was stimulated by UV laser LCS-DTL-374QT with excitation wavelength nm. The emission spectra were amplified and recorded in the wavelength range 400–900 nm. The PL spectra were measured at room temperature.

3. Results and Discussion

3.1. AFM Studies of Porous Silicon

During the experiment, we obtained samples with different surface morphology. Figure 1 displays an AFM image of the porous silicon surface (samples series no. 1). At a low concentration of oxidizing agent—H₂O₂ (H₂O₂/H₂O/HF = 10/80/40), as seen from this image, there were pores that had a conical form, like a crater, having approximately the same size and uniformly distributed over its surface. The approximate diameter of pores ranged from 1 to 1.6 um in diameter. This morphology is quite different from that observed on metal-assisted chemically etched PS obtained on high-resistivity silicon with 22.5 M HF-0.05 M Na₂S₂O₈-H₂O solution [19].

In the case of low deposition times, the Ag particles were deposited nonuniformly. Distribution of pores on the surface and form are not orderly, as evident in the AFM image shown in Figure 2.

The next step was to figure out how the increasing of oxidant concentration affects surface morphology. The increase of oxidant concentration (H₂O₂/H₂O/HF = 25/80/40) leads to a change in the surface structure of silicon from microporous to highly porous structure. We have observed highly porous structure with the dimensions of the pores having an approximate size of 50–200 nm depending on the deposition time (Figure 3). For both concentrations of H₂O₂, the prolonged etching time induces an increase of pore depth. The changing of surface morphology due to increasing of H₂O₂ concentration could be explained by the theory proposed by Chartier et al. [20]. Charties et al. have shown that as the composition varies from high to low HF/H₂O₂ ratio, mesopores, cone-shaped macropores, craters could be obtained. This change occurred because of fast dissolving of the silicon surface.

For samples series no. 2, that had higher concentration of AgNO₃ in immersion solution (10⁻³ M), we have obtained more remarkable experimental results. The color of the silicon surface after etching has been almost black (1–15 minutes of immersion time) or light brown (15–30 minutes of immersion time) depending on the immersion time. First, we supposed that it is similar to “black” silicon havinga needle-shaped surface structure where needles are made ofsingle-crystal siliconand have a height above 10 microns and diameter less than 1 micron [21]. However, AFM investigation showed an absolutely other morphology (Figure 4) having macropores.

The macropores grow parallel and perpendicular to the surface, a result similar to that generally observed on p-type highly resistive silicon electrochemically etched [22]. It is remarkable that as the concentration of AgNO₃ increases the diameter of pores is increased. An intensive process of silver particle deposition can explain this phenomenon. As far as the surface color, the formation of new compounds like AgF (silver fluoride) and AgF₂ (silver difluoride) on the surface with appropriate colors—AgF (light brown), AgF₂ (dark brown) can explain given experimental observations. We have found these compounds onto the surface using XFS measurement (not shown here). Following reactions show how the compound’s formation could occur:

It was obvious that the transition of morphology from microporous to macroporous structure would modify the optical properties of the silicon surface. It was indeed observed in luminescence properties of silicon porous structure.

3.2. PL Characteristics of Porous Silicon

Figure 5 shows PL spectra from samples series no. 1 etched for 6 minutes in the concentration etchant (H₂O₂/H₂O/HF = 10/80/40). The deposition time varied from 1 to 10 minutes. There was a correlation between PL spectra and the metal-assisted chemical etching conditions. The PL could not be observed if the deposition time was less than 1 minute. The PL spectra had approximately Gaussian line shapes. The PL intensity is significantly increased by surface etching and deposition time, while the PL spectrum remains almost unchanged. This fact can be related to the increase of the silicon porous density, that is, of radiative recombination centers. The PL spectra present emission peaks centered at approximately 680–700 nm (corresponding energies 1.77–1.82 eV). These peaks correspond to emission in the red region.

Figure 6 shows the PL spectra for three samples of porous silicon etched for 6 minutes, but prepared in a more concentrated solution of hydrogen peroxide etchant (H₂O₂/H₂O/HF = 25/80/40). The deposition time varied from 0.5 to 6 minutes. It can be noticed the shifting of luminescence peaks to shorter wavelengths of the spectrum (to be higher energies) due to increasing of deposition time. It is also seeing an increase in PL intensity. The PL spectra present emission peaks centered at 620, 610, and 560 nm (corresponding energies 1.99, 2.03, 2.21 eV), respectively.

Besides, it can be seen the complex shape of the PL curve. By Origin pro 8.5 software, the PL spectrum was split onto separate peaks (Figure 7). The PL peaks located at 480, 550, and 670 nm have been found. The full explanation of photoluminescence has not been done yet. The PL peak at the red region is well understood based on the quantum-confinement model [23]. The PL peak at green region is supposed associated with formation of AgF or AgF₂. The microscopic origin of the wide blue luminescence band in the given porous Si has to date not been convincingly established, and additional measurements will be performed in future works.

The next stage of the experiment was to investigate the photoluminescence spectra for samples series no. 2 ( M) etched for 6 minutes in the concentration etchant (H₂O₂/H₂O/HF = 15/80/40). The PL spectra present three emission peaks centered at 520, 550, and 710 nm, respectively (Figure 8). The first and second peaks are more intense and correspond to emission in the green region; on the other hand, the third peak situated in the red region is less powerful. The intensity of the two peaks intensity increases with etching time. Comparing the data with the energy band gap of fluoride and difluoride, silver (in the theoretical studies presented data are in the range 2–2.8 eV), we can assume that the peak falls at 550 nm corresponds to the silver difluoride, and the peak of 520 nm—silver fluoride [24–26].

The red peak in Figure 8, observed in sample series no. 1 as well, is associated with nanostructured silicon, the so-called S-band [27]. According to the quantum confinement model, the emission wavelength and the PL peak intensity are correlated to nanocrystallite size and the number (density) of nanocrystallites, respectively [28]. Thus, we can conclude that the sizes of nanocrystallites of the sample series no. 1 are smaller compared to those of samples series no. 2. It seems that when the silver concentration in immersion solution becomes lower the nanocrystallite size decreases leading to a shift of PL peak to the shorter wavelengths.

This result is very interesting, since it is difficult to form light-emitting porous layers on highly resistive silicon by the electrochemical method. Porous silicon layers exhibit strong red luminescence with PL peaks ranged within 630–680 nm, which are similar to those found for medium doped anodically etched silicon [1]. It is also important to note that the PL spectrum peaks of sample series no. 2 are not perfectly Gaussian. Since the visible luminescence spectra of common PS had a shape close to a Gaussian curve, the assumption that the luminescence spectrum, for these samples, can be fitted by addition of several Gaussian curves (peaks) is appropriate. Indeed, Figure 7 shows that it can be fitted by a sum of three Gaussian curves. These results differ from those found by Hadjersi et al., where only two PL peaks were centered at 617 and 646 nm [29]. This is most likely due to preparation conditions of samples that have produced a morphology different from that of our samples. Indeed, they used an etching solution of HF and Na₂S₂O₈. This confirms that different morphologies can be produced by varying the type of etchant solution. In addition, the significant result obtained is the observation of two narrow PL peaks centered at 520 and 550 nm. These peaks can be attributed to formation of AgF and AgF₂ on a silicon surface.

4. Conclusion

Photoluminescence and surface morphologies of nanostructured porous silicon prepared by metal-assisted chemical etching using H₂O₂ as an oxidizing agent have been studied. Depending on the metal-assisted chemical etching conditions, the macro- or microporous structures could be formed. Red band emissions were observed at 680–700 nm for silicon microporous structure. For highly porous silicon structures, we have observed PL peaks at 620, 610, and 560 nm. It was shown that the PL intensity increases with increasing etching time, which can be attributed to the increase of the silicon nanostructure density in agreement with the quantum confinement model prediction. It was found the shift of red PL peak to a green region with increasing of deposition time that can be attributed to the changing in porous morphology. The PL spectra of samples prepared with high concentrated solution of AgNO₃ present two narrow peaks centered at 520 and 550 nm. These peaks can be attributed to formation of AgF and AgF₂ on a silicon surface.

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Copyright © 2012 Igor Iatsunskyi 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.

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