Spectroscopic properties and simulation of white-light in Dy3+-doped silicate glass
Introduction
As a potential candidate for replacement conventional incandescent and fluorescent lamps, white-light emitting diodes (w-LEDs) has attracted intensive attention in recent years due to the advantages of long lifetime, saving energy, high efficiency, reliability, and its environmental-friendly characteristics [1], [2], [3]. At present, the common way for assemble w-LEDs is combining an ultraviolet (UV) or blue chip with down-converted phosphors [2]. The first w-LEDs was commercialized by combining a GaN-based blue chip with yellow YAG:Ce phosphors in 1996 [4]. However, the lack of red component in YAG:Ce phosphors leads to low color-redering index (CRI, Ra in the 60–75 range). As may be expected, red enhanced YAG:Ce or a small amount of red phosphors was introduced to improve the CRI to the acceptable range (Ra > 80) and increased the light conversion [5], [6]. In addition to the blue LEDs plus yellow approach, three-band w-LEDs were also proposed to achieve by the combination of the blue GaN-based LED with green and red emitted phosphors or the pumping of tri-color (red, green and blue) phosphors with ultraviolet (UV) or violet LED [3]. Three-band w-LEDs maintain a very high CRI (Ra > 90) and were believed to offer the greatest potential for high efficiency solid state light [7]. For excellent CRI, both methods need efficient red phosphors that should have the excitation wavelength matching with the emission wavelength of blue LEDs (440–470 nm) or the UV/violet LEDs (350–420 nm). So far, most of these w-LEDs were limited to use as back light sources of liquid crystals displays for handy phones or digital cameras in view of low luminous flux from one w-LED [8]. Up to now, many studies have been carried out to obtain enough brightness for general lighting, in which useful method is to increase output power of LED chips. However, this also increases the chip temperature, which may cause a deterioration of the resin, which is used to fix the powder phosphors onto the LED chip, and decrease the luminous efficiency and lifetime [9].
The versatility of glasses regarding the possibility of a wide doping concentration and the narrow lines emission spectra of the lanthanide ions could be considered as a promising alternative approach since the first simulation of white-light in borate glass [10]. Compared with phosphors, glasses have more advantages such as lower production cost, simpler manufacture procedure, and free from halo effect [10], [11], [12], [13], [14], [15], [16], [17], [18], [19]. On the other hand, the visible luminescence of Dy3+ (4f9) ion mainly consists of two intense bands in the blue (470–500 nm) and yellow (570–600 nm) regions, which are associated with the 4F9/2 → 6H15/2 and 4F9/2 → 6H15/2 transitions, respectively. The latter one is a hypersensitive transition, which is strongly influenced by the environment. At a suitable yellow to blue (Y/B) intensity ratio, Dy3+ ions will emit white-light. Thus, luminescent materials doped/codoped with Dy3+ ions are usually used to the generation of white-light both in glasses [11], [12], [13], [14], [15], [16] and phosphors [20], [21], [22]. These studies on glasses have emphasized on luminescent behavior and generation of white-light in Dy3+-doped, Dy–Ce-, Dy–Eu-, or Dy–Tm-codoped aluminasilicate [12], borosilicate [16], phosphate glass [11] and oxyfluoride [13], [14], [15] glasses. To the best of our knowledge, little work is reported in the conventional silicate glass. In the present work, spectroscopic properties and simulation of white-light in various concentrations Dy3+-doped silicate glasses were investigated in details, here silicate glass is chosen as the host glass because of its high chemical stability and low cost.
Section snippets
Experimental
Glass samples were prepared using high-purity grade oxide or salts including SiO2, BaCO3, Al2O3, R2CO3(R = Li, Na and K) and Re2O3 (Re = Dy, and Y) as the starting materials. The nominal composition of all glass samples are listed in Table 1. The glass samples were all made up to contain 12.37 wt% rare-earths in total. When the concentration of Dy2O3 was required to less than 12.37 wt%, the remainder of the 12.37 wt% was made up by the addition of an inert oxide such as Y2O3. This was done in order to
Spectroscopic properties
The excitation (monitor at 575 nm) and emission spectra (under the 349 nm excitation) of various concentrations Dy3+-doped silicate glasses are shown in Fig. 1, Fig. 2, respectively. All of the emissions in Fig. 2 are due to the 4f–4f transitions of Dy3+ ions. Under the excitation at 349 nm, blue-light emission peaking at 484 nm and yellow-light emission peaking at 575 nm as well as a rather weak emission peaking at 668 nm (plotted by a factor of 10 in the 640–690 nm range) were observed and can be
Conclusions
Various concentrations Dy3+-doped silicate glasses were prepared and characterized. The glass samples emit simultaneously visible blue and yellow lights as well as a weaker red emission by 349, 385 and 451 nm excitation, respectively. The quenching concentration was found to be 3.0 wt% and the electric dipole–dipole interaction mechanism was confirmed by Huang’s rule. With the elevated Dy3+ ions concentration, the Y/B intensity ratios of visible emissions increases over a wide range indicate the
Acknowledgments
This work was supported by National Natural Science Fund of China (Grant No. 10904114) and the Program for Young Excellent Doctors in Jinggangshan University.
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