Abstract:The requirement of using ultraviolet light to stimulate afterglow luminescence has seriously restricted indoors/outdoors applications of most persistent materials developed hitherto. Herein, efficient blue‐light‐activated Ce3+, Pr3+: YAGG phosphors, showing optimized long‐persistent luminescence lasting for 1 h, were prepared and investigated in detail with the aid of X‐ray diffraction refinement, steady‐state/persistent photoluminescence spectra, room/low‐temperature persistent decay curves, and three‐dimensi… Show more
“…12. Previously reports on the persistent luminescence of YAG: Ce also confirms the existence of crystal defects4243. The decrease in the intensity of TSL suggests the decrease of the concentration of crystal defects; and the shift of TLS peak from high to low temperature indicates the decrease of the trap depth.…”
The deficiency of Y3Al5O12:Ce (YAG:Ce) luminescence in red component can be compensated by doping Gd3+, thus lead to it being widely used for packaging warm white light-emitting diode devices. This article presents a systematic study on the photoluminescence properties, crystal structures and electronic band structures of (Y1−xGdx)3Al5O12: Ce3+ using powerful experimental techniques of thermally stimulated luminescence, X-ray diffraction, X-ray absorption near edge structure (XANES), extended X-ray absorption fine structure (EXAFS) and ultraviolet photoelectron spectra (UPS) of the valence band, assisted with theoretical calculations on the band structure, density of states (DOS), and charge deformation density (CDD). A new interpretation from the viewpoint of compression deformation of electron cloud in a rigid structure by combining orbital hybridization with solid-state energy band theory together is put forward to illustrate the intrinsic mechanisms that cause the emission spectral shift, thermal quenching, and luminescence intensity decrease of YAG: Ce upon substitution of Y3+ by Gd3+, which are out of the explanation of the classic configuration coordinate model. The results indicate that in a rigid structure, the charge deformation provides an efficient way to tune chromaticity, but the band gaps and crystal defects must be controlled by comprehensively accounting for luminescence thermal stability and efficiency.
“…12. Previously reports on the persistent luminescence of YAG: Ce also confirms the existence of crystal defects4243. The decrease in the intensity of TSL suggests the decrease of the concentration of crystal defects; and the shift of TLS peak from high to low temperature indicates the decrease of the trap depth.…”
The deficiency of Y3Al5O12:Ce (YAG:Ce) luminescence in red component can be compensated by doping Gd3+, thus lead to it being widely used for packaging warm white light-emitting diode devices. This article presents a systematic study on the photoluminescence properties, crystal structures and electronic band structures of (Y1−xGdx)3Al5O12: Ce3+ using powerful experimental techniques of thermally stimulated luminescence, X-ray diffraction, X-ray absorption near edge structure (XANES), extended X-ray absorption fine structure (EXAFS) and ultraviolet photoelectron spectra (UPS) of the valence band, assisted with theoretical calculations on the band structure, density of states (DOS), and charge deformation density (CDD). A new interpretation from the viewpoint of compression deformation of electron cloud in a rigid structure by combining orbital hybridization with solid-state energy band theory together is put forward to illustrate the intrinsic mechanisms that cause the emission spectral shift, thermal quenching, and luminescence intensity decrease of YAG: Ce upon substitution of Y3+ by Gd3+, which are out of the explanation of the classic configuration coordinate model. The results indicate that in a rigid structure, the charge deformation provides an efficient way to tune chromaticity, but the band gaps and crystal defects must be controlled by comprehensively accounting for luminescence thermal stability and efficiency.
“…This green emitting phosphor shows afterglow for several hours after the excitation has stopped, and has been extensively investigated [3,4,5]. Two decades after the discovery by Matsuzawa et al, the list of afterglow phosphors has grown, and in addition to the alkaline earth aluminates it now also includes, among others, silicates and sulfides doped with a wide variety of activators, such as Eu [6], Ce [7,8] or transition metal ions [9]. An important class of these materials are the red- and infrared-emitting persistent phosphors, which are quite scarce compared to other classes, but are highly desired in diverse applications, such as bioimaging and safety signage.…”
The performance of a persistent phosphor is often determined by comparing luminance decay curves, expressed in cd/m2. However, these photometric units do not enable a straightforward, objective comparison between different phosphors in terms of the total number of emitted photons, as these units are dependent on the emission spectrum of the phosphor. This may lead to incorrect conclusions regarding the storage capacity of the phosphor. An alternative and convenient technique of characterizing the performance of a phosphor was developed on the basis of the absolute storage capacity of phosphors. In this technique, the phosphor is incorporated in a transparent polymer and the measured afterglow is converted into an absolute number of emitted photons, effectively quantifying the amount of energy that can be stored in the material. This method was applied to the benchmark phosphor SrAl2O4:Eu,Dy and to the nano-sized phosphor CaS:Eu. The results indicated that only a fraction of the Eu ions (around 1.6% in the case of SrAl2O4:Eu,Dy) participated in the energy storage process, which is in line with earlier reports based on X-ray absorption spectroscopy. These findings imply that there is still a significant margin for improving the storage capacity of persistent phosphors.
“…Thus, the temperature‐dependent intensity of LPL was employed to identify the distribution of traps indirectly for the restriction of measurement range of our instrument below room temperature. Additionally, the LPL luminous intensity reaches maximum at the peak of the TL curve was demonstrated in previous reports . Thus, the TL curve of CYA: Eu and CYA: Eu, Nd is obtained by fitting the intensity of LPL measured at different temperature below 300 K as shown in Figure C,D, respectively.…”
Fluorescent anti‐counterfeiting technologies have become indispensable by virtue of their high concealment properties. In this work, the observation of the characteristic emission originated from Eu2+ and Eu3+ ions in CaYAl3O7 realizes a dual‐mode anti‐counterfeiting strategy. The host matrix provides an environment, where blue and red emission could be manipulated with the introduction of Nd3+ ions for the reduced occupation of Eu3+ in the sites of Y3+ ions. Moreover, the photoluminescence spectra of these samples exhibit time and temperature‐dependent dynamic changes thanks to the capture and release of carriers in the reconstructed traps induced by Nd3+ ions. Herein, a multi‐stimuli responsive dynamic and static anti‐counterfeiting could be achieved in this work.
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