Advances in Optical Technologies

Advances in Optical Technologies / 2012 / Article

Research Article | Open Access

Volume 2012 |Article ID 814745 |

Fumitaka Yoshimura, Mika Ishizaki, Fumihiro Wakai, Masahiko Hara, Osamu Odawara, Hiroyuki Wada, "Optical Properties of Afterglow Nanoparticles S r 2 M g S i 2 O 7 : E u 2 + , D y 3 + Capped with Polyethylene Glycol", Advances in Optical Technologies, vol. 2012, Article ID 814745, 6 pages, 2012.

Optical Properties of Afterglow Nanoparticles S r 2 M g S i 2 O 7 : E u 2 + , D y 3 + Capped with Polyethylene Glycol

Academic Editor: Siu-Fung Yu
Received24 Mar 2011
Accepted18 May 2011
Published14 Jul 2011


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).

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.

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.

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.

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).

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).

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.


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.


  1. E. O. Knutson and K. T. Whitby, “Aerosol classification by electric mobility: apparatus, theory, and applications,” Journal of Aerosol Science, vol. 6, no. 6, pp. 443–451, 1975. View at: Google Scholar
  2. R. G. Osifchin, W. J. Mahoney, J. D. Bielefeld, R. P. Andres, J. I. Henderson, and C. P. Kubiak, “Synthesis of a quantum dot superlattice using molecularly linked metal clusters,” Superlattices and Microstructures, vol. 18, no. 4, p. 283, 1995. View at: Publisher Site | Google Scholar
  3. J. R. Darwent and G. Porter, “Photochemical hydrogen production using cadmium sulphide suspensions in aerated water,” Journal of the Chemical Society, Chemical Communications, no. 4, pp. 145–146, 1981. View at: Google Scholar
  4. C. B. Murray, D. J. Norris, and M. G. Bawendi, “Synthesis and characterization of nearly monodisperse CdE (E = S, Se, Te) semiconductor nanocrystallites,” Journal of the American Chemical Society, vol. 115, no. 19, pp. 8706–8715, 1993. View at: Google Scholar
  5. F. Mafuné, J. Y. Kohno, Y. Takeda, T. Kondow, and H. Sawabe, “Structure and stability of silver nanoparticles in aqueous solution produced by laser ablation,” The Journal of Physical Chemistry B, vol. 104, no. 35, pp. 8336–8337, 2000. View at: Google Scholar
  6. Y. Tamaki, T. Asahi, and H. Masuhara, “Tailoring nanoparticles of aromatic and dye molecules by excimer laser irradiation,” Applied Surface Science, vol. 168, no. 1–4, pp. 85–88, 2000. View at: Publisher Site | Google Scholar
  7. T. Tsuji, K. Iryo, N. Watanabe, and M. Tsuji, “Preparation of silver nanoparticles by laser ablation in solution: influence of laser wavelength on particle size,” Applied Surface Science, vol. 202, no. 1-2, pp. 80–85, 2002. View at: Publisher Site | Google Scholar
  8. C. Liang, Y. Shimizu, T. Sasaki, and N. Koshizaki, “Synthesis, characterization, and phase stability of ultrafine TiO2 nanoparticles by pulsed laser ablation in liquid media,” Journal of Materials Research, vol. 19, no. 5, pp. 1551–1557, 2004. View at: Publisher Site | Google Scholar
  9. K. Sasaki and N. Takada, “Liquid-phase laser ablation,” Pure and Applied Chemistry, vol. 82, no. 6, pp. 1317–1327, 2010. View at: Publisher Site | Google Scholar
  10. F. Brech and L. Cross, “Optical micromission stimulated by a ruby maser,” Applied Spectroscopy, vol. 16, no. 2, p. 59, 1962. View at: Google Scholar
  11. J. Neddersen, G. Chumanov, and T. Cotton, “Laser ablation of metals: a new method for preparing SERS active colloids,” Applied Spectroscopy, vol. 47, no. 12, pp. 1959–1964, 1993. View at: Google Scholar
  12. A. Fojtik and A. Henglein, “Laser ablation of films and suspended particles in a solvent: formation of cluster and colloid solutions,” Berichte der Bunsen-Gesellschaft. Physical Chemistry, Chemical Physics, vol. 97, no. 2, pp. 252–254, 1993. View at: Google Scholar
  13. F. Yoshimura, K. Nakamura, F. Wakai et al., “Preparation of long-afterglow colloidal solution of Sr2MgSi2O7: Eu2+, Dy3+ by laser ablation in liquid,” Applied Surface Science, vol. 257, no. 6, pp. 2170–2175, 2011. View at: Publisher Site | Google Scholar
  14. T. Matsuzawa, Y. Aoki, N. Takeuchi, and Y. Murayama, “A new long phosphorescent phosphor with high brightness, Sr2MgSi2O4: Eu2+, Dy3+,” Journal of the Electrochemical Society, vol. 143, no. 8, pp. 2670–2673, 1996. View at: Google Scholar
  15. N. Kodama, T. Takahashi, M. Yamaga, Y. Tanii, J. Qiu, and K. Hirao, “Long-lasting phosphorescence in Ce3+-doped Ca2Al2SiO7 and CaYAl3O7 crystals,” Applied Physics Letters, vol. 75, no. 12, pp. 1715–1717, 1999. View at: Google Scholar
  16. Q. Fei, C. Chang, and D. Mao, “Luminescent properties of Sr2MgSi2O7 and Ca2MgSi2O7 long lasting phosphors activated by Eu2+, Dy3+,” Journal of Alloys and Compounds, vol. 390, no. 1-2, pp. 133–137, 2005. View at: Publisher Site | Google Scholar
  17. Y. Chen, B. Liu, M. Kirm et al., “Luminescent properties of blue-emitting long afterglow phosphors Sr2-xCaxMgSi2O7: Eu2+, Dy3+ (x=0,1),” Journal of Luminescence, vol. 118, no. 1, pp. 70–78, 2006. View at: Publisher Site | Google Scholar
  18. A. R. Mirhabibi, F. Moztarzadeh, A. A. Bazazi, M. Solati, A. Maghsoudipour, and M. H. Sarrafi, “Studies of luminescence property of long afterglow Eu2+, Dy3+ activated Sr2MgSi2O7 phosphor,” Pigment and Resin Technology, vol. 33, no. 4, pp. 220–225, 2004. View at: Publisher Site | Google Scholar
  19. J. I. Pankove, Optical Processes in Semiconductors, Dover, New York, NY, USA, 1971.
  20. O. I. Mićić, J. Sprague, Z. Lu, and A. J. Nozik, “Highly efficient band-edge emission from InP quantum dots,” Applied Physics Letters, vol. 68, no. 22, pp. 3150–3152, 1996. View at: Publisher Site | Google Scholar
  21. M. Kuno, J. K. Lee, B. O. Dabbousi, F. V. Mikulec, and M. G. Bawendi, “The band edge luminescence of surface modified CdSe nanocrystallites: probing the luminescing state,” Journal of Chemical Physics, vol. 106, no. 23, pp. 9869–9882, 1997. View at: Google Scholar
  22. F. Song, C. Donghua, and Y. Yuan, “Synthesis of Sr2MgSi2O7: Eu, Dy and Sr2MgSi2O7: Eu, Dy, Nd by a modified solid-state reaction and their luminescent properties,” Journal of Alloys and Compounds, vol. 458, no. 1-2, pp. 564–568, 2008. View at: Publisher Site | Google Scholar
  23. J. Hölsä, M. Kirm, T. Laamanen, M. Lastusaari, J. Niittykoski, and P. Novák, “Electronic structure of the Sr2MgSi2O7:Eu2+ persistent luminescence material,” Journal of Luminescence, vol. 129, no. 12, pp. 1560–1563, 2009. View at: Publisher Site | Google Scholar
  24. T. Kano, “Luminescence center of rare-earth ions,” in Phosphor Handbook, W. M. Yen, S. Shionoya, and H. Yamamoto, Eds., chapyer 3.3, CRC Press, Boca Raton, Fla, USA, 2206. View at: Google Scholar
  25. K. Uchida, H. Otsuka, M. Kaneko, K. Kataoka, and Y. Nagasaki, “A reactive poly(ethylene glycol) layer to achieve specific surface plasmon resonance sensing with a high S/N ratio: the substantial role of a short underbrushed PEG layer in minimizing nonspecific adsorption,” Analytical Chemistry, vol. 77, no. 4, pp. 1075–1080, 2005. View at: Publisher Site | Google Scholar
  26. J. Blümmel, N. Perschmann, D. Aydin et al., “Protein repellent properties of covalently attached PEG coatings on nanostructured SiO2-based interfaces,” Biomaterials, vol. 28, no. 32, pp. 4739–4747, 2007. View at: Publisher Site | Google Scholar
  27. A. A. Setlur, A. M. Srivastava, H. L. Pham, M. E. Hannah, and U. Happek, “Charge creation, trapping, and long phosphorescence in Sr2MgSi2O7: Eu2+, RE3+,” Journal of Applied Physics, vol. 103, no. 5, Article ID 053513, 2008. View at: Publisher Site | Google Scholar
  28. M. Yamaga, Y. Tanii, N. Kodama, T. Takahashi, and M. Honda, “Mechanism of long-lasting phosphorescence process of Ce3+-doped Ca2Al2SiO7 melilite crystals,” Physical Review B, vol. 65, no. 23, Article ID 235108, 2002. View at: Google Scholar
  29. T. Kinoshita, M. Yamazaki, H. Kawazoe, and H. Hosono, “Long lasting phosphorescence and photostimulated luminescence in Tb-ion-activated reduced calcium aluminate glasses,” Journal of Applied Physics, vol. 86, no. 7, pp. 3729–3733, 1999. View at: Google Scholar
  30. J. Qiu and A. Makishima, “Ultraviolet-radiation-induced structure and long-lasting phosphorescence in Sn2+-Cu2+ co-doped silicate glass,” Science and Technology of Advanced Materials, vol. 4, no. 1, pp. 35–38, 2003. View at: Publisher Site | Google Scholar
  31. M. Yamaga and N. Kodama, “Fluorescence of Ce3+ in fluorides and long-lasting phosphorescence of Ce3+ in oxides,” Journal of Alloys and Compounds, vol. 408–412, pp. 706–710, 2006. View at: Publisher Site | Google Scholar
  32. E. Nakazawa, “Transient characteristics of luminescence,” in Phosphor Handbook, W. M. Yen, S. Shionoya, and H. Yamamoto, Eds., chapter 2.7, CRC Press, Boca Raton, Fla, USA, 2006. View at: Google Scholar
  33. S. Tachikawa, A. Noguchi, M. Hara, O. Odawara, and H. Wada, Journal of Ceramic Processing Research, submitted.
  34. S. Tachikawa, A. Noguchi, M. Hara, O. Odawara, and H. Wada, “Optical properties of ZnO nanoparticles capped with polymers,” Materials, vol. 4, pp. 1132–1143, 2011. View at: Google Scholar

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.

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