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Advances in Optical Technologies
Volume 2012 (2012), Article ID 814745, 6 pages
http://dx.doi.org/10.1155/2012/814745
Research Article

Optical Properties of Afterglow Nanoparticles : , Capped with Polyethylene Glycol

Tokyo Institute of Technology, 4259 Nagatsuda, Midori-ku, Yokohama 226-8503, Japan

Received 24 March 2011; Accepted 18 May 2011

Academic Editor: Siu-Fung Yu

Copyright © 2012 Fumitaka Yoshimura 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.

Abstract

The optical properties of afterglow nanoparticles were successfully improved by the addition of polyethylene glycol (PEG) to an afterglow colloidal solution. Afterglow nanoparticles—: , —were prepared by laser ablation in liquid. The quantum yields and the decay curves were measured by a fluorescence spectrophotometer. An increase in the amount of PEG added to the solution increased the quantum yield of the nanoparticles and improved the afterglow property in the initial portion of the decay curve. However, the afterglow property did not change after a substantial amount of time had passed. The afterglow nanoparticles were capped with PEG molecules, and surface defects of the nanoparticles were passivated, which decreased the optical properties.

1. Introduction

In the past several years, there has been increasing interest in nanoparticles due to their unique properties and various applications in research fields, such as biotechnology and electronics. There are many methods available to create nanoparticles, such as gas-phase preparation [1, 2] and liquid-phase preparation [3, 4]. One of the liquid-phase preparation methods is laser ablation in liquid, which has recently been studied extensively [59]. While laser ablation in the gas phase, such as under vacuum and in argon, has been used for various research purposes [10], laser ablation, in liquid, has been investigated more recently [11, 12]. In the case of laser ablation in liquid, the target material in the liquid is irradiated with a focused, pulsed laser beam without using a chamber. Precipitation methods, such as the sol-gel method, are well known as synthesis methods for nanoparticles. However, it is difficult to prepare multielement nanoparticles with these techniques. In the case of the trioctylphosphine oxide (TOPO) method [4], the popular synthesis method used to create quantum dots, coating materials are limited to specific surfactants, such as TOPO. In contrast, in the case of laser ablation in liquid, multielement nanoparticles can be easily prepared. By using laser ablation in liquid, surfactant-free nanoparticles can be prepared, and/or a desirable coating material can be selected.

We prepared functionalized multielement nanoparticles with afterglow properties by using laser ablation in liquid [13]. Afterglow is a promising optical property for various fields because of the long emitting time (e.g., several hours) after the excitation is blocked. In the case of normal fluorescence, materials emit during excitation but do not emit after the excitation is blocked. On the contrary, in the case of afterglow, materials emit both during excitation and after the excitation is blocked. The long-afterglow material SrAl2O4: Eu2+, Dy3+ was discovered by Matuzawa in 1996 [14]. However, it is water soluble. Sr2MgSi2O7: Eu2+, Dy3+, a water-insoluble afterglow material, was recently proposed by numerous research groups [1518]. If these afterglow materials can be nanosized, they would be very useful in many fields. One example is as a marker for bioimaging. This system would resolve the existing problem of autofluorescence in which the excitation of markers also excites fluorescent materials, such as NADH and tryptophan, which exist in living cells. Ideally, only the marker would emit when afterglow nanoparticles were used as markers, and the excitation light was blocked.

Capping nanoparticles with polymer molecules has been studied previously. The advantages of capping are as follows: ( 1 ) the passivation of surface defects, which decreases the nonradiative recombination center and increases fluorescence intensity [1921]; ( 2 ) the aggregation inhibition of nanoparticles by steric rather than electrostatic effects; ( 3 ) the ability to utilize nanoparticles for a drug delivery system (DDS) because of the improvement in immunoaffinity, especially in the case of capping nanoparticles with polyethylene glycol (PEG).

In this study, the optical properties of afterglow nanoparticles capped with PEG were investigated. We prepared the afterglow nanoparticles by laser ablation in liquid. However, the reduction in particle size decreased the optical properties. The probability of an increase in the optical properties of nanoparticles was examined by the addition of PEG to the colloidal liquid.

2. Experimental Methods

Figure 1 shows the equipment used for laser ablation in liquid. The target in DI water in a cell was irradiated with a focused, pulsed laser beam. The laser was a third-harmonic generation pulsed laser (JDS Uniphase Co., Model 210, THG, wavelength: 355 nm, pulse width: 50 ns, energy: 0.5 mJ/pulse, average energy density: 0.85 J/cm2). The target material Sr2MgSi2O7: Eu2+, Dy3+, which has afterglow properties, was purchased from the Mitsubishi Chemical Corporation. The target was fabricated by spark plasma sintering (SPS, SPS Syntex Inc., SPS-515S, pressure: 50 MPa, electric current: 540 A, voltage: 2.4 V, temperature: 1100°C, sintering time: 10 min, atmosphere: Ar).

814745.fig.001
Figure 1: Equipment for laser ablation in liquid.

The synthesized nanoparticles were identified by an X-ray diffractometer (XRD, PANalytical B.V. X’pert-PRO-MRD). The sample powder was obtained by centrifugation. The optical properties (fluorescence and afterglow) were measured by a fluorescence spectrophotometer (Hitachi High-Technologies Co., F-7000).

3. Results and Discussion

Figure 2 shows the optical properties of the target material. The PL spectrum (Figure 2(a)) with an excitation wavelength of 276 nm had a main, broad, blue-green peak at 466 nm, which was attributed to the f-d transitions of Eu2+ ions [22]. The strong peak at approximately 555 nm represents the second-order scattering of the excitation light. The PLE spectrum (Figure 2(b)) with an emission wavelength of 466 nm has 2 peaks at 275 nm and 361 nm. These peaks are due to defect levels of the host material; therefore, the peak shape is changed by the synthesis method [22]. The increase in absorbance less than 237 nm was probably caused by band-edge absorption of the host material, whose bandgap was 7.1 eV (175 nm) [23]. The strong peak at 232 nm was the second-order scattering of a 466-nm excitation wavelength.

fig2
Figure 2: Optical properties of Sr2MgSi2O7: Eu2+, Dy3+. (a) Photoluminescence spectrum (excitation wavelength: 276 nm). (b) Photoluminescence excitation spectrum (emission wavelength: 466 nm).

Figure 3 shows an XRD pattern of the synthesized nanoparticles prepared in DI water with an average energy density of 0.85 J/cm2. These data corresponded to the powder diffraction file data for Sr2MgSi2O7 (PDF-4 10753217), which was the target. Strontium carbonate was formed as a byproduct. The target material might react with carbonate, which is formed by the dissolution of carbon dioxide in DI water.

814745.fig.003
Figure 3: XRD pattern of the synthesized nanoparticles prepared by laser ablation in liquid (DI water, average energy density: 0.85 J/cm2).

Figure 4 shows PL spectra of the synthesized nanoparticles with the addition of PEG. The concentration of PEG was varied (a: 1 mM, b: 0.1 mM, c: 0 mM). The shape and peak wavelength of each spectrum were almost the same as those of the target material. In general, the fluorescence of Eu2+ is due to the transition from the 4f65d1 level, which causes a broad emission [24]. On the contrary, the fluorescence of Eu3+, whose 4f electrons are shielded from external electric fields by the outer 5s and 5p electrons, is sharp and appears at approximately 600 nm [24]. The wavelength of the fluorescence spectra of the f-d transitions of Eu2+ is sensitive to the crystal field, whereas that of the f-f transitions of Eu3+ is not affected because the 4f electrons are shielded by 5s and 5d electrons [24]. The PL spectra of nanoparticles prepared by laser ablation in liquid were the same as those of the target. Therefore, the luminescent center, Eu2+, and the host material were not transformed by the laser ablation in liquid and the addition of PEG, although Eu2+ was likely to be easily oxidized.

814745.fig.004
Figure 4: PL spectra of the synthesized nanoparticles with the addition of PEG. PEG concentration: (a) 1 mM, (b) 0.1 mM, and (c) 0 mM.

Figure 5 shows the quantum yield of nanoparticles as a function of the PEG concentration. A dotted line was added as a guide. An increase in the PEG concentration increased the quantum yield of the afterglow nanoparticles, although the increase rate was slightly low at a high PEG concentration. The reason for this increase would be as follows: PEG molecules would adhere to the nanoparticles, as shown in Figure 6, and passivate defect levels, which reduced the fluorescence intensity. The quantum yield was saturated at a high PEG concentration because passivation of the whole surface of the nanoparticle would be covered with the addition of enough PEG. In general, killer defects, which create surface levels, exist on the surface of particles. The reduction of particle size increases the specific surface area of the particle. Therefore, the florescence intensity and the quantum yield are decreased in the case of nanoparticles. There were many reports that passivation of fluorescent nanoparticles by polymers increased the fluorescence intensity [1921]. Capping nanoparticles with PEG is also important for minimizing the nonspecific adsorption of proteins related to the immune system [25, 26]. Therefore, PEG-capped nanoparticles are useful for bioimaging and drug delivery system (DDS).

814745.fig.005
Figure 5: Quantum yield of the nanoparticles as a function of the PEG concentration.
814745.fig.006
Figure 6: Schematic of an afterglow nanoparticle and of PEG molecules. (a) An afterglow nanoparticle without the addition of PEG. (b) An afterglow nanoparticle capped with PEG molecules at a high PEG concentration.

Figure 7 shows decay curves of afterglow nanoparticles at each PEG concentration. Afterglow is caused by the recombination of the trapped carriers [14, 2731]. For example, trapped holes migrate to the valence band using the thermal energy available at room temperature. These holes result in luminescence through the radiative transition of recombination between electrons and holes. In the case of SrAl2O4: Eu2+, Dy3+, it has been suggested that holes are trapped at the energy level of Dy3+ ions [14]. In the case where the trapped carriers are electrons, equation (1) is applied to the decay curve. This formula can also be applied in the case of holes if the captured cross sections of the traps and the luminescent centers are almost the same [32]: where I(t) is the afterglow intensity, I0 is the initial value, t is time, N is the trap concentration, a is the probability that a trapped carrier will be thermally led into the band (given below by (3)), nt is the number of carriers per unit volume in the trap level, and n is approximately 0.5–2 where s is the frequency factor, Et is the energy between the conduction band and the trap level, k is the Boltzmann constant, and T is temperature. If t is much less than 1/γ (the initial period), γ is the dominant parameter compared with n. On the contrary, if t is much greater than 1/γ (the period after a substantial amount of time has passed), n is the dominant parameter. The values of n and γ can be obtained by the curve fitting of afterglow properties shown in Figure 7. The values of γ at each PEG concentration were as follows: at 1 mM, at 0.1 mM, and at 0 mM, respectively. Because these afterglow properties of nanoparticles in Figure 7 depended on the slopes in the initial period, the values of γ were important to identify the differences in the data. Figure 8 shows the value of γ as a function of the PEG concentration. A dotted line was added as a guide. Addition of PEG significantly reduced the value of γ. A small γ value indicates a significant improvement in the afterglow properties, as shown in (1).

814745.fig.007
Figure 7: Decay curves of afterglow nanoparticles at each PEG concentration.
814745.fig.008
Figure 8: Value of γ as a function of the PEG concentration.

The values of were almost the same at each PEG concentration. As indicated in the introduction, functionalized fluorescent nanoparticles, such as afterglow nanoparticles, are a promising type of material in various fields. However, as mentioned above, a reduction in the particle size decreases the afterglow properties. The reason for this is as follows: a reduction in the particle size increases the specific surface area of the particles. The increased specific surface area leads to the nonradiative transition of surface defects through the energy levels and to the vibration of water molecules, which decreases the afterglow property. The addition of PEG to the solution in which the nanoparticles were dispersed caused capping nanoparticles [33, 34]. Surface passivation by polymer coating would be effective to prevent such a reduction of afterglow properties [1921]. In this study, the addition of PEG increased the quantum yield, as shown in Figure 5. An increase in the PEG concentration increased the afterglow property, especially in the initial period shown in Figure 7, although the property had not changed significantly after a substantial amount of time had passed. We concluded that this improvement was due to the coating effect of PEG.

4. Conclusions

The addition of PEG to afterglow nanoparticle solutions prepared by laser ablation in liquid increased the quantum yield. PEG addition also improved the afterglow property of Sr2MgSi2O7: Eu2+, Dy3+ nanoparticles in the initial period. The afterglow property was not improved after a substantial amount of time had passed. Because the specific surface area of nanoparticles is large, nanoparticles have many surface defects, which decrease optical properties, such as photoluminescence and afterglow. In this study, these surface defects on afterglow nanoparticles were passivated by PEG molecules, and the optical properties improved. Improvement of the afterglow property is important for a wide range of applications.

Acknowledgments

The authors wish to thank Mr. H. Iida and Mr. Y. Suzuki of the Center for Advanced Materials Analysis (Tokyo Institute of Technology) for the XRD measurements.

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