A. K. Singh
*ab,
S. K. Singh
c and
S. B. Rai
a
aDepartment of Physics, Banaras Hindu University, Varanasi-221005, India. E-mail: akhilesh_singh343@yahoo.com
bInstituto de Ciencias Físicas, Universidad Nacional Autónoma de México, Cuernavaca, Morelos C.P. 62210, México
cDepartment of Physics, Indian Institute of Technology (Banaras Hindu University), Varanasi-221005, India
First published on 29th April 2014
Lanthanide based materials are preferred over other luminescent materials for various applications. Current focus in this area is to exploit the unique luminescence features of lanthanide-based materials for multidisciplinary research and novel applications. Furthermore, efforts are going on to enhance the luminescence of lanthanide ions for better performance. In a broader sense, there are two ways to enhance the luminescence of lanthanide ions. The first is to use a suitable sensitizer, which can absorb excitation energy efficiently, and can transfer it to the lanthanide ions. This method has been known for a long time and is well documented in the literature. The second way is to modify host matrices in such a way that it favors radiative transitions. It is widely reported in the literature that the presence of alkali ions, particularly Li+ ions, in a matrix enhances the luminescence of lanthanide ions significantly. But there are no comprehensive reports available in the literature that summarize how alkali ions help in the luminescence enhancement of lanthanide ions in various host matrices. The prime objective of this review is to highlight various contributing factors that help in the luminescence enhancement of lanthanide ions in the presence of alkali ions.
In recent years, research of lanthanide-based luminescence materials has been focused to exploit the unique features of lanthanides in various other novel applications, viz. for multimodal emission (downconversion (DC)/quantum-cutting (QC), down-shifting (DS) and upconversion (UC) processes) based imaging, in increasing the efficiency of solar cells (by using an additional DC/UC layer in the solar cell to minimize the thermal and sub-bandgap losses), as contrast agents in magnetic resonance imaging, various biological applications, etc.31–35 The pragmatic implication of luminescence materials for these applications demands efficient materials in many ways, including an increase in the emission intensity. Therefore, continuous active research effort in this field is desirable to enhance the luminescence intensity of the lanthanide ions.
There are two fundamental ways to enhance the luminescence intensity of the lanthanide ions in a given host. The first is to use a suitable sensitizer, which can absorb UV and/or NIR radiation effectively and can transfer the energy to the central lanthanide ions.1–3,36–42 In the literature, different sensitization strategies are reported for increasing the luminescence of lanthanide ions, viz. by forming lanthanide ion complexes with organic ligands, which can strongly absorb UV radiation and transfer efficiently to the central lanthanide ion; by excited state energy transfer from the charge transfer band to the lanthanide ion; by using co-dopant and thereby energy transfer among lanthanide themselves, etc.24,38,41 The second way to enhance the luminescence of lanthanide ions is to modify the host matrices in such a way that it favors transitions of lanthanide ions. Due to its smaller ionic radius alkali ions, the Li+ ion in particular is very frequently used nowadays for this purpose.7–19,56–142 Li+ ions are easily accommodated in host matrices, which tailors the local crystal field around the lanthanide ions.
Recently, our group has also worked in this area and shown that the use of Li+ ion enhances the photoluminescence (PL) of lanthanide ions in YPO4 and Y2O3 hosts.74,81,84 In the literature, several models have been proposed by different groups to explain the luminescence enhancement in the lanthanide ions in different host matrices.56–142 However, to the best of our knowledge, there is no review article that summarizes a comprehensive view of how the alkali ion modifies a host matrix resulting in enhanced luminescence. The prime objective of this review is to fill this gap and highlight various contributing factors that contribute towards luminescence enhancement. Along with this, since different types of host matrices have been reviewed individually through the previous literature, the present article could also be very useful in studying/visualizing the role of the matrix on the luminescence intensity of lanthanide ions in general. This review is written in such a way that it could be useful for a broad audience of chemists/biochemists and materials scientists as well.
The promotion of a 4f electron into the 5d sub-shell in lanthanide ions is allowed by the parity rule. These transitions are quite energetic and observed only in Ce3+, Pr3+ and Tb3+ ions. Since the 5d orbitals are external and interact directly with the ligand orbitals, their energy largely depends on the metal environment.7–19 In Ce3+ ions, luminescence is observed from 2D3/2 levels to 2F5/2, 2F7/2, whereas 2D5/2 lies at high energy and luminescence from this level is not generally observed. The luminescence in Ce3+ can be tuned from about 290 to 450 nm, depending on the matrix into which the metal ion is inserted. The charge transfer transition in lanthanide ions is also allowed by Laporte's selection rule. The other and most studied transition in lanthanides is the 4f–4f transition. According to Laporte's rule, electric dipole transitions with the same parity are not allowed. By virtue of that, the 4f–4f transition in lanthanides is forbidden.5,6 However, when these ions are doped in a suitable host matrix, due to influence of the ligand-field, non-centrosymmetric interactions, a mixing of the wavefunctions of the states of opposite parity with 4f-wavefunctions, takes place. This relaxes somewhat the parity selection rule and 4f–4f transitions become partially allowed.5,6 Furthermore, the crystal field destroys the degeneracy of its energy levels. In fact, the ligand/crystal generates a ligand/crystal electrostatic field which, in turn, interacts with the 4f electrons of the lanthanide ions generating a ligand field/crystal field (or Stark) splitting of the spectroscopic levels.5,6 The 4f orbitals of the lanthanide ions remain shielded by 5s and 5p orbitals, and therefore promotion of an electron into a 4f sub-orbital of higher energy does not change the binding pattern significantly. Thus, the inter-nuclear distance remains almost unchanged in the excited state, which produces narrow emission lines. The long lifetime is because of the fact that the 4f–4f transitions in the lanthanide ions are parity forbidden.5,6 Table 1 summarizes the energy of principal 4f–4f transitions of lanthanide ions coming through DS, QC and UC processes.
Ln | Transition | Emission wavelength (nm) | Remarks |
---|---|---|---|
a QC – quantum-cutting, DS – down-shift, UC – upconversion, NIR – near-infrared, P – phosphoresce, F – fluorescence. Most of the data presented are taken from ref. 31 and 52. | |||
Pr | 3P2 → 3H4 | 440 | Weak, QC |
3P0 → 3H4 | 480 | Strong, UC and QC | |
1D2 → 3F4 | 1037 (P, NIR) | Medium, UC and QC | |
Nd | 2P3/2 → 4I11/2 | 410 | Strong, UC and QC |
2P3/2 → 4I13/2 | 452 | Strong, UC and QC | |
4F3/2 → 4I11/2 | 1064 (F, NIR) | Strong, QC and DS | |
Sm | 4G5/2 → 6H7/2 | 601 (P, orange) | Strong, DS |
Eu | 5D0 → 7F0,1,2,3,4 | 570–720 (P, orange) | Strong, UC and DS |
Tb | 5D4 → 7F6,5,4,3 | 480–650 (P, green) | Strong, UC, DS and QC |
Dy | 4F9/2 → 6H15/2 | 486 | Medium, DS and QC |
4F9/2 → 6H13/2 | 575 (P, yellow-orange) | Strong, DS and QC | |
Ho | 5S2, 5F4 → 5I8 | 540 (F, green) | Strong, UC and QC |
5F5 → 5I8 | 644 (F, red) | Strong, UC and QC | |
5I6 → 5I8 | 1180 (NIR) | Strong, QC | |
Er | 4S3/2 → 4I15/2 | 545 (F, green) | Strong, UC and QC |
4F9/2 → 4I15/2 | 665 (F, red) | Strong, UC and QC | |
4I13/2 → 4I15/2 | 1540 (NIR) | Strong, QC | |
Tm | 1D2 → 3F4 | 450 (blue) | Medium, UC and QC |
3H4 → 3H6 | 800 (NIR) | Strong, UC and QC | |
Yb | 2F5/2 → 2F7/2 | 980 (F, NIR) | Strong, UC, QC and DS |
The 4f–4f transition in lanthanide ions facilitates UC and DC/QC as well as DS processes, which may allow for facile photon management.43–51 In the DC/QC process, an incident higher-energy photon splits into two (or more) lower energy photons with a conversion efficiency of more than 100%.46–49 DS is similar to QC but it is a single photon process that involves the transformation of one absorbed high-energy photon into one low-energy photon and so its conversion efficiency does not exceed 100%.50,51 Meanwhile, on the other hand, UC is a nonlinear process that involves two or more low energy photons (usually NIR) to emit a single photon of higher energy (usually visible or ultraviolet).43–45 To generate practically useful UC emission, the energy difference between each excited level and its lower-lying intermediate level (ground level) should be close enough to facilitate photon absorption and energy transfer steps involved in UC processes. Er3+, Tm3+, and Ho3+ typically feature such ladder-like arranged energy levels and are thus frequently used activators for UC.
Selection of an appropriate host matrix for the preparation of a lanthanide-based luminescence material is an essential requirement. As the luminescence of lanthanide ions is very sensitive to the local crystal field environment, the host matrix should have close lattice matches to the dopant ions.52–54 Failing to achieve this can create a large distortion in the matrix, which strongly influences the luminescence of lanthanide ions. In particular, the 5d–4f transitions of the lanthanide ions are strongly influenced (both position and intensity) by the crystal field of the matrix.7–19 Since the lanthanide(III) ions exhibit similar ionic size and chemical properties their inorganic compounds are ideal hosts for lanthanide ion doping. In addition, alkaline earth ions (Sr2+, Ca2+, and Ba2+) and some transition metal ions (Zr4+ and Ti4+) also exhibit close ionic size to lanthanide ions and are frequently used as host materials for lanthanide ion doping. Further, the ideal host matrix should also have low lattice phonon energies, to minimize non-radiative loss and maximize the radiative emission. The dopant concentration, which determines the average distance between neighboring dopant ions, has a strong influence on the optical properties of the lanthanide-based luminescence materials.52–54 In certain host matrices, luminescence of lanthanide ions increases appreciably with increasing crystallinity. This is because of the fact that as the crystallinity increases, the particle size also increases, which reduces surface quenching centers (surface to volume ratio decreases). The increased particle size is not required in many technological applications, which have been prompted due to the advancement in nanotechnology; therefore, researchers usually like to use a passive layer, by forming a core–shell structure, to reduce the surface quenching centers.54 The co-doping of alkali ions in the matrix strongly affects the crystal structure, crystallinity, grain size, surface morphology, quenching centers (OH−, NO3−, etc.) and create distortion in the matrix.56–142 Therefore, it would be interesting to study the effect of alkali ions, particularly the Li+ ion, on the luminescence properties of lanthanide ions doped in various matrices and try to find out some meaningful information to understand the underlying mechanism, and also to explore the future possibilities. The following sections aim to investigate these aspects in detail.
Sample | Change in luminescence properties | Remarks |
---|---|---|
CaBr:Eu2+,Li+ (ref. 7) | Improves radiation hardness | By reducing the X-ray induced vacancy centers |
Li2CaSiO4:Eu2+ (ref. 8a) | Small Stokes shift | Smaller ionic radius of Li+ constrains the distortion of the excited state |
CaS:Ce3+,Pr3+,Li+ (ref. 9) | 3 fold enhanced afterglow intensity and 4 fold enhancement in afterglow time | New cation vacancy formed, which works as an electron trap center |
CaO:Ce3+,Li+ (ref. 10) | 1.88 fold enhancement in luminescence intensity | Increased absorbance to the excitation photons |
SrAl2O4:Eu2+,Ce3+,Li+ (ref. 11) | Enhanced luminescence of Eu2+ | Charge compensation |
NaCaPO4:Eu2+,Li+ (ref. 12) | Enhanced luminescence of Eu2+ | Change in spin–orbit coupling and coordination of Eu2+ ions |
Sr2–2xLiSiO4F:xCe3+,xLi+ (ref. 13) | Shift in peak position | Ce3+ occupying different Sr2+ site |
Sr3SiO5:Ba2+,Ce3+,Li+ (ref. 14) | Li+ co-doping helps to incorporate Ce3+ ions on Sr2+ site | By charge compensation |
Lu2SiO5:Ce3+,Li+ (ref. 15) | 2.2 fold enhancement in luminescence intensity | Change in crystal field around Ce3+ ions |
Sr3Si2O4N2:Eu2+,Li+ (ref. 19) | Red shift in emission band | Re-absorption in Eu2+ ions |
Sr3Si2O4N2:Ce3+,Li+ (ref. 19) | No prominent red shift |
Grandhe et al.12 investigated the effect of Li+ ions on the emission characteristics of Eu2+ emission in phosphate matrix (Na1−yLiyCa1−xPO4:xEu2+) synthesized by a conventional solid state reaction method. The excitation spectra of NaCaPO4:Eu2+ phosphors revealed a broad excitation band ranging from 250 to 450 nm with a maximum intensity at 373 nm. Upon 373 nm excitation, the phosphor exhibits an intense bluish-green emission band centered at 505 nm. Fig. 1(b) shows that the Na1−yLiyCa0.99PO4:0.01Eu2+ phosphor containing 4 mol% of Li+ ions (y = 0.04) exhibits maximum luminescence intensity. It is suggested that the difference in the ionic radii probably gives rise to diversity in the crystal lattice around the luminescence center. This may in turn influence the spin–orbit coupling and the crystal field around the Eu2+ ions. Liu et al.8 have synthesized the Li2CaSiO4:Eu2+ phosphor by a conventional solid state reaction method and found that the Li+ ion changes the excitation and emission characteristics of Eu2+ effectively in silicate matrix also. It was again concluded to be due to the change in host lattice/crystal field due to the involvement of Li+ ions in the crystal structure. They proposed that the Eu2+ ions go to distorted dodecahedral Ca sites, which causes strong crystal field splitting leading to a broad excitation band extending from the UV to visible regions. Also, the high concentration of Li+ ions in the structure constrained the distortion of the emission center (Li+ ions, which are behind the oxygen ions surrounding the emission centers, will restrict the expansion of the emission centers), which results in a smaller Stokes shift.
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Fig. 1 (a) CIE coordinates of Ca0.98SiN2−2δ/3Oδ:0.01Ce3+/0.01Li+ and photos of the powder samples under daylight and 365 nm UV excitation. (b) PL emission spectra of Na1−yLiyCa0.99PO4:Eu0.01 phosphors sintered in argon initially and later in N2H2 atmosphere with varying lithium ion concentrations. (c) PL spectra of CaO:Ce3+ and CaO:Ce3+,Li+. The inset presents a histogram of the integrated PL intensity, where the intensity of CaO:Ce3+ is normalized. Photographs of: (d) an as-prepared CdSe QD- and Sr3SiO5:Ce3+,Li+ phosphor-based white LED and (e) the same white light-emitting LED operated at 5 mA. (a) Reproduced from ref. 17 with permission from The Royal Society of Chemistry. (b) Reprinted (adapted) with permission from ref. 12. Copyright © 2012 Elsevier B. V. All rights reserved. (c) Reprinted (adapted) with permission from ref. 10. Copyright © 2013 Elsevier B. V. All rights reserved. (d and e) Reprinted (adapted) with permission from ref. 18. Copyright © 2008 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim. |
A similar study for Ce3+ doped into a silicate matrix has also been presented by Zhu et al.16 The authors prepared a Sr3SiO5:Ce3+,Li+ phosphor, by a solid state reaction method, and showed that under near-UV excitation at 415 nm, the phosphor emits a bright greenish-yellow color centered at 532 nm (originating from the 5d to 4f (2F7/2 and 2F5/2) transition of Ce3+). Upon substitution of Sr2+ ions with Mg2+ (smaller ionic radius than Sr2+) and Ba2+ (larger ionic radius than Sr2+) ions, the peak position of the PL spectrum shifts towards higher and lower energy, respectively. This is because of the fact that as Mg2+ ions substitute Sr2+ ions the degree of covalence in the Ce–O bonds is decreased, and consequently less negative charge transfers to Ce3+ ions, thus increasing the difference between the 4f and 5d levels (causes blue-shift in the emission band). In contrast, the substitution of Sr2+ with the larger Ba2+ increases the degree of covalence in the Ce–O bonds, which causes red-shift in the emission band. Thus, the emission color of Sr3SiO5:Ce3+,Li+ can be tuned by partial replacement of Sr2+ with Mg2+ or Ba2+, which makes it applicable to a variety of LEDs (from 410–450 nm chips). In another similar article by Shen et al.,14 the role of Li+ has been proposed in the same host in more detail, and explores that the Li+ codoping compensates the charge difference between the Ce3+ and Sr2+ ions and thus helps to incorporate the Ce3+ into Sr2+ sites. The phosphor (Sr3SiO5:Ce3+,Li+) shows high luminous efficiency under near-UV/blue light excitation, and the obtained emission is comparatively broader than that of the Eu2+-activated yellow phosphor. To improve the color rendering properties of the Sr3SiO5:Ce3+,Li+ phosphor, Jang et al.18 have used additional Pr3+ ions (to enhance the red-emitting component) along with Ce3+ ions. Under blue light excitation, energy transfer from Ce3+ to Pr3+ ions takes place, which gives a shoulder at 619 nm (of Pr3+ ions) in the PL spectrum of Sr3SiO5:Ce3+,Pr3+,Li+. The energy transfer has been proved by steady-state and time domain luminescence measurements. Further, by making use of monodisperse CdSe QDs and the phosphor on a blue LED chip, they produced white LEDs with excellent color rendering properties (see Fig. 1(d) and (e)).
Wang et al.17 have prepared CaSiN2 powders at 1550 °C in a N2/H2 (6%) atmosphere by the solid-state reaction method using Ca3N2 and Si3N4 as the starting materials. The luminescence measurements on Ce3+/Li+ co-doped CaSiN2−2δ/3Oδ shows a broad yellow band peaking at 530 nm. The maximum PL intensity was attained for the sample with the Ce3+ composition x = 0.01, above this concentration quenching occurs. The oxygen content in the sample was analyzed and is found to be δ ≈ 0.2. Further, the chromaticity coordinates (0.362, 0.571) also demonstrate that CaSiN2−2δ/3Oδ:Ce3+/Li+ is a good yellow phosphor (see Fig. 1(a)). Hao et al.10 studied the PL properties of the CaO:Ce3+,Li+ phosphor. It is found that, upon 474 nm excitation, the Li+ ion co-doped phosphor shows a 1.88 fold enhancement in PL intensity (see Fig. 1(c)). The XRD results show the presence of a small amount of CeO2, a starting material, in the CaO:Ce3+ phosphor, which suggests low solubility of Ce3+ in CaO. Upon Li+ ion co-doping the intensity of this peak decreases, indicating that more CeO2 is converted to Ce3+ ions for effective doping into the CaO host lattice. This results in increased absorption of the excitation photons in CaO:Ce3+,Li+ causing PL enhancement. This might be because of the charge compensation due to the presence of Li+ ions and the effect of Li+ as a flux to increase diffusivity of the raw materials, which causes more Ce3+ ions to go into CaO lattice. Jia et al.15 have prepared the Lu2SiO5:Ce3+,Li+ phosphor by Pechini sol–gel chemistry. They optimized the concentration of Ce3+ and Li+ ions, which was found to be 0.006 wt% and 0.02 wt%, respectively. The PL intensity of 0.006 wt% Ce3+, 0.02 wt% Li+ co-doped phosphor sample was 2.2 times higher than the 0.006 wt% Ce3+ doped phosphor. It is suggested that the Ce3+ ions occupy two different crystallographic sites (with coordination number 6 or 7) in the monoclinic lattice (space group C2/c) of Lu2SiO5.143 This causes two luminescence centers Ce1 and Ce2 in this host. The peaks at 3.16 and 2.95 eV originate from the emission of the Ce1 center, while another peak at 2.74 eV corresponds to the Ce2 center. With the increase of Li+ ion co-doping concentration, initially the intensity of the Ce1 emission increases and then decreases, while the Ce2 emission intensity always decreases. This suggests energy transfer from Ce2 to Ce1 centers, which was demonstrated by time-domain measurements. Thus the enhanced luminescence of Lu2SiO5:Ce3+ phosphors by Li+ ion co-doping is mainly regarded as the result of the production of the local distortion in host lattice, which alters the crystal field around activator and results in the energy transfer from Ce2 to Ce1 centers.15
The effects of Li+ ions have also been investigated for persistent/afterglow emission. Kojima et al.9 have studied the afterglow luminescence properties of green emitting Ce3+ and Pr3+ co-doped CaS phosphors. The afterglow time of CaS:Ce3+,Pr3+ was relatively short (about 10 min). When Li+ is introduced in the matrix, the afterglow intensity and afterglow time of CaS:Ce3+,Pr3+ both increase, by three and four fold, respectively. It is shown that the Li+ ions go to the interstitial spaces in the crystal lattice and increase the lattice constant. When a Li+ ion is incorporated into the crystal lattice of CaS, a new cation vacancy is formed for the charge compensation in the Ca2+ site, which increases the lattice strain. This cation vacancy working as an electron trap can capture some of the excited electrons and thereby increase the charging process. Chen et al.11 have prepared SrAl2O4:Eu2+,Ce3+,Li+, another persistent luminescence material, by a solid-state reaction method using H3BO3 as flux. Li+ ions compensate the charge defects caused by the non-equivalent substitution of Sr2+ with Ce3+. Thus, the luminescence intensity of SrAl2O4:Eu2+ is significantly enhanced when Ce3+ and Li+ both are present in the sample.
Recently, several research groups, including our own, have used Li+ ions to further enhance the luminescence of lanthanide ions doped in this matrix.56–74 Table 3 summarizes the concentrations of different activator (lanthanide) ions and Li+ ions to obtain the optimum luminescence. The table also describes the mode of luminescence measurement (e.g. DS, UC), quantitative information about luminescence enhancement and the explanation given by different research groups for the luminescence enhancement. It is evident from the Table 3 that different research groups have proposed different mechanisms for luminescence enhancement of lanthanide activator ions in presence of Li+ ions. A detailed description of the work done so far and their salient features are summarized below, including a detailed description of the representative works in the area concerned.
Sample | DS/UC | Luminescence enhancement | Remarks |
---|---|---|---|
Gd1.84Li0.08Eu0.08O3 (ref. 56) | DS | 2.3 fold (PL) | Improved crystallinity, higher surface roughness and increased optical phonon energy |
Y1.9Li0.05Eu0.05O3 (ref. 57) | DS | 2.5 fold (CL) | Charge compensation |
Gd1.92Li0.03Eu0.05O3 (ref. 57) | DS | 3 fold (PL) | Lowering of local symmetry |
Gd1.9Li0.06Eu0.04O3 (ref. 58) | DS | 4 fold (PL) | Charge compensation and lowering of local symmetry |
Gd1.84Li0.08Eu0.08O3 (ref. 59) | DS | 2.3 fold (PL) | Improved crystallinity and higher surface roughness |
Gd1.87Li0.06Yb0.06Tm0.01O3 (ref. 60) | UC | 10 fold (PL) | Lowering of symmetry around Tm3+ and decrease in OH concentration |
Gd1.935Li0.04Yb0.02Ho0.005O3 (ref. 61) | UC | 10 fold (PL) | Lowering of symmetry around Ho3+ |
Y1.935Li0.05Nd0.015O3 (ref. 62) | UC | 2 fold (PL) | Changed morphology, modification of local symmetry and decrease in OH concentration |
Y1.92Li0.05Yb0.02Er0.01O3 (ref. 63) | UC | 30 fold (PL) | Prolong lifetime of their intermediate states |
Y1.92Li0.05Yb0.02Er0.01O3 (ref. 64) | UC | 25 fold (PL) | Change in crystal field, prolong lifetime of intermediate states, increased optical active sites and dissociation of clusters |
Y1.94Li0.04Er0.02O3 (ref. 65) | UC | 10 fold (PL) | Change in crystal field and dissociation of clustering. |
Y1.94Li0.05Er0.01O3 (ref. 66) | UC | 45 fold (PL) | Tailored lifetime of intermediate levels, suppressed cross relaxation and enlarged particle size |
Y1.94Li0.05Er0.01O3 (ref. 67) | UC | 45 fold (PL) | Tailored lifetime of intermediate levels |
Y1.84Li0.08Eu0.08O3 (ref. 68) | DS | 1.2 fold (EL) | Improved crystallinity and higher surface roughness |
Y1.70Li0.1Eu0.2O3−δ (ref. 69) | DS | 1.2 fold (PL) | Improved morphology |
Y1.9455Li0.05Yb0.05Tm0.0025O3 (ref. 71) | UC | 15 fold (PL) | Change in crystal field, decrease in OH concentration and dissociation of clusters |
Y1.9Li0.05Yb0.05O3 (ref. 72) | DS | 12 fold (PL) | Change in crystal field |
Y1.93Li0.05Tm0.02O3 (ref. 73) | UC | 19 fold (PL) | Increase in lifetime of intermediate levels |
Y1.917Li0.05Yb0.03Er0.003O3 (ref. 74) | UC | 3 fold (PL) | Change in crystal field and decrease in OH concentration |
Dhananjaya et al.58 studied the effect of Li+ ions on the PL of Eu3+ in Gd2O3 host. They proposed that when the concentration of Li+ ions in the Gd2O3 host is low (<4 mol%), substitution of Gd3+ ions with Li+ ions induces oxygen vacancies. This causes a crystal field distortion around the activator ions (Eu3+), which results in increased PL. The oxygen vacancies also act as a sensitizer for activator lanthanide ions, by the involvement of an effective energy transfer from the strong charge transfer states (which come into picture due to the vacancy itself) to lanthanide ions. Further, they explore that as the Li+ concentration increases, along with substitutional Li+ sites, interstitial sites of Li+ ions are also present, which cause Gd3+ ion vacancies. This as a result produces more defects around the activator lanthanide ions. In this case the Stark level in the emission spectrum shows larger splitting. In a similar study, Shin et al.57 have monitored cathodoluminescence (CL) of Eu3+ ions in Gd2O3 and Y2O3 as host matrices in the presence of Li+ ions, and they also proposed the charge compensation mechanism for CL enhancement of Eu3+ ions in both hosts, while for the case of Gd2O3 host the group additionally put forward other mechanisms also described in the subsequent paragraph.
Along with charge compensation mechanisms, several other mechanisms for the luminescence enhancement have also been reported. The cubic structure of Y2O3 and Gd2O3 offers two different crystallographic sites for activator lanthanide ions: one with C2 (without center of inversion) and the other with S6 (with center of inversion (C3i)) symmetry.57 The transitions in the lanthanide ions are affected effectively, as far as the intensity and splitting is concerned, by the symmetry of the crystal field of the host. For example, when a Eu3+ ion occupies S6 symmetry, the magnetic dipole transition 5D0 → 7F1 is the dominant one. In case of Eu3+ doped material the occupancy ratio of two different sites (ORS) i.e. local symmetry around Eu3+ ion, can be easily obtained by taking the intensity ratio of 5D0 → 7F2 (∼611 nm) to 5D0 → 7F1 (∼590 nm) transitions.57 Ionic radii of Y3+, Gd3+ and Li+ ions are 0.89, 0.94 and 0.76 Å, respectively.57,58 Thus, Li+ ion substitution deforms the Gd2O3 lattice more as compared to Y2O3 lattice, and the statistical distribution of lanthanide (Eu3+) and Li+ ions at the C2 and S6 sites in the Gd2O3 lattice becomes more intricate. Shin et al.57 have also reported that changes in ORS after Li+ ion incorporation is larger in Eu3+ doped Gd2O3 than the Y2O3 matrix. Based on this information, Shin et al. proposed that the mechanism of luminescence enhancement in Li+ ion doped Gd2O3 might be different to that in the Y2O3 host. X-ray diffraction (XRD) patterns (shown in Fig. 2) recorded by Shin et al.57 reveal that Y1.95−xLixO3:Eu0.05 phosphor samples have cubic structure even at higher doping concentration of Li+ ions. In contrast, Gd1.95−xLixO3:Eu0.05 phosphor samples show monoclinic to cubic transformation as the doping concentration of Li+ increased. This gradual change from monoclinic to cubic lattice is also confirmed by Dhananjaya et al.58 This change from monoclinic to cubic lattice in Gd2O3 host is also one of the reasons for increased luminescence.57,58
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Fig. 2 X-ray diffraction (XRD) patterns of Y1.95−xLixO3:Eu0.05 and Gd1.95−xLixO3:Eu0.05 phosphor. Reprinted (adapted) with permission from ref. 57 Copyright © 2005 Elsevier B. V. All rights reserved. |
Fan et al.62 have reported the effect of Li+ ion in enhancing the PL of Nd3+ ions doped into Y2O3 samples. They proposed that among two different crystallographic sites (C2 and C3i symmetry, the ratio of C2 to C3i sites is 3:
1) of cubic Y2O3, electric dipole transitions of lanthanide ions are forbidden for C3i sites. Thus, when Li+ ions occupy the C3i sites, it destroys the inversion symmetry and the forbidden electric dipole transitions of lanthanide ions (Nd3+) become partially allowed. Further, when Li+ ions occupy the C2 sites with higher population in the lattice, the reduced symmetry of these sites again results in the enhancement of PL of lanthanide ions (Nd3+). Thus, in both cases enhanced PL is observed. When the Li+ ion concentration is too high it might cause a large local distortion around optically active centers (lanthanide ions), which can lead to the PL quenching.
In similar context, several studies have also been reported for the enhancement of UC emission. A study by Sun et al.60 reports the UC phenomenon in a silica coated Tm3+/Yb3+/Li+ ion doped Gd2O3 matrix, and found ∼10 fold enhancement of UC emission in the sample doped with 6 mol% of Li+. They have suggested that the enhancement in PL is due to a change in the local asymmetry around Tm3+ ions. On further increasing the Li+ ion concentration (up to 10 mol%) the UC emission decreases substantially. They have reported that at higher Li+ ion concentrations, the local crystal field around Tm3+ ions yet again becomes symmetric, which is unfavorable for UC emission. Chen et al.64 (Yb3+/Er3+), Bai et al.65 (Yb3+/Er3+), Li et al.71 (Yb3+/Er3+), Fan et al.72 (Yb3+) and Mishra et al.74 (Yb3+/Er3+) have also studied the effect of Li+ ions on the enhancement of UC/PL of lanthanide ions in Y2O3 and Gd2O3 host matrices and suggested the change in crystal symmetry around the lanthanide ions as one of the reasons for PL enhancement.
The other contributing factors in the PL enhancement of lanthanide ions in these hosts are change in morphology, crystallinity and grain size of materials.56,59,68,69 Atomic force microscopy (AFM), which is used to study the surface morphology, results reported by Jeong et al.56 shows that Li+ ion doping increases the grain size and roughness of the Gd2O3:Eu3+ films. Larger grain size reduces the density of the grain boundaries, which in turn might be responsible for reduced adsorption and/or scattered light generated inside the film, which favors PL enhancement. Furthermore, increased crystallinity due to Li+ ion doping in samples causes higher oscillating strength for optical transitions, which also favors PL enhancement.56 Yi et al.59 (Gd2O3:Eu3+), Fan et al.62 (Y2O3:Nd3+), Yi et al.68 (Y2O3:Eu3+) and Sun et al.69 (Y2O3:Eu3+) have also proposed that increased grain size, roughness and crystallinity of materials, in the presence of Li+ doping, is among one of the potential reasons for luminescence enhancement of lanthanide ions.
Time-domain studies have also been exploited to search for the possible reasons behind the enhancement of PL/UC emission. It has been observed that changes in lifetime of intermediate state/states participating in energy transfer process also play a crucial role. Chen et al.64 suggested that due to changes in the local crystal field of the Y2O3 matrix around the lanthanide ions, observed lifetimes of intermediate states, 4I11/2 (Er3+) and 2F5/2 (Yb3+), can change. This can also modify the theoretical lifetimes of lanthanide ions by slightly changing their wavefunctions. They monitored decay profiles of 4I11/2 → 4I15/2 transitions of Er3+ ions (at 1015 nm) in Y2O3 nanocrystals in the presence of 0–15 mol% Li+ ions (see Fig. 3(d)).66,67 The lifetime of the intermediate state 4I11/2 was found to be 0.8(2) ms and 2.7(3) ms for 0 and 3 mol% Li+ ions, respectively, and it is about 3.4(3) ms for higher Li+ ions concentrations (5–15 mol%). This suggest that the local crystal field around Er3+ ions is gradually tailored for lower doping concentration of Li+ ions (0–5 mol%) and becomes nearly constant for higher Li+ ion concentrations. The enhancement in UC emission has the same trend as the lifetime increases. Fig. 3(a) and (b) show UC emission spectra of Er3+ doped Y2O3 in the absence and presence of Li+ ions. In an another work, Fan et al.73 monitored the decay profiles of 4I13/2 → 4I15/2 transition (at 1530 nm) of Er3+ ions in Y2O3 matrix in the presence of 0–6 mol% of Li+ ions under 976 nm excitation. They also observed an increase in the lifetime with increasing concentration of doped Li+ ions; the lifetime varies from 3.14 ms to 3.28 ms for 5 mol% Li+ ions. The study concludes and proposes that the Li+ ion tailors the local crystal field around the Er3+ ion, and therefore modifies the theoretical lifetime by slightly changing the wavefunction, somewhat similar to the earlier reports.
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Fig. 3 Upconversion emission in (a) ultraviolet-blue, and (b) green-red regions in Y2O3 nanocrystals doped with 1 mol% Er3+ ions and co-doped with 0 or 5 mol% Li+ under 970 nm diode laser excitation. (c) Fourier transform infrared spectra of Er3+/Yb3+:Y2O3 doped with 0 or 5 mol% Li+ ions. (d) Decay profiles of the 4I11/2 → 4I15/2 transition of Er3+ in Y2O3 nanocrystals doped with 1 mol% Er3+ ions and 0, 3, 5, 7, 10, or 15 mol% Li+ ions. The inset shows the fluorescence spectrum of the 4I11/2 → 4I15/2 transition in the range of 1000–1050 nm under 970 nm diode laser excitation. (a) and (b) Reprinted (adapted) with permission from ref. 67. Copyright © 2008 Elsevier Ltd. All rights reserved. (c) Reprinted (adapted) with permission from ref. 74. Copyright © 2013 Elsevier Ltd. All rights reserved. (d) Reprinted with permission from ref. 66. Copyright© 2008, AIP Publishing LLC. |
Furthermore, some of the studies interestingly report that the doping of Li+ ions suppresses the PL quenching entities e.g. molecules with OH−, NO3−, COx, etc. groups having high vibrational frequencies. During phosphor synthesis by chemical routes (viz. combustion, sol–gel methods) incomplete combustion of organic fuel introduces luminescence quenching centers, which decrease the PL intensity. Sun et al.60 (Gd2O3:Tm3+/Yb3+), Fan et al.62 (Y2O3:Nd3+), Li et al.71 (Y2O3:Tm3+/Yb3+) and Mishra et al.74 recorded FTIR (Fourier transform infrared) spectra of phosphor materials without and with Li+ ion doping in various hosts and found that the broad absorption bands peaking at 1626 and 3454 cm−1, owing to vibrational features of O–H groups, are suppressed significantly in the presence of Li+ ions (see Fig. 3(c)).74 In addition, Mishra et al.74 have also reported that the broad peak at ∼1369 cm−1, due to stretching vibrations of NO in surface-adsorbed NO3− groups, is also suppressed in presence of Li+. This might be due to the fact that the Li+ ion neutralizes the hydroxyl (and other) groups present in the phosphor. Thus, the addition of Li+ ions reduces the non-radiative transition probability and hence enhances the PL efficiency.
Thus in summary, Li+ ion doping in Gd2O3 and Y2O3 hosts significantly affects both the structural and optical parameters such as charge compensation, change in crystal symmetry around activator ions, increased crystallinity, increased grain size, change in morphology (higher surface roughness), increase of lifetime of intermediate levels of activator ions, decrease in non-radiative channels (OH−, NO2− concentrations), etc., which altogether enhances the optical emission of lanthanide ions.
Sample | DS/UC | Luminescence enhancement | Remarks |
---|---|---|---|
Ca0.8Li0.1Er0.02Yb0.08MoO4 (ref. 76) | UC | 83 fold (PL) | Local crystal field distortion around Er3+ ion |
Ca0.95MoO4:0.05Dy3+,0.05Li+ (ref. 77) | DS | 1.3 fold (PL) | Charge compensation |
Ca0.95MoO4:0.05Tb3+,0.05Li+ (ref. 78) | DS | — (PL) | Oxygen vacancy |
Li0.05Eu0.05La0.9PO4 (ref. 79) | DS | 2 fold (PL) | Decrease in interstitial oxygen and reduced internal reflections |
La0.93Eu0.07VO4:0.25 wt% Li+ (ref. 80) | DS | — (PL) | Oxygen vacancy, increased grain size |
YPO4:2 at% Dy,7 at% Li+ (ref. 81) | DS | — (PL) | Improved crystallinity |
YPO4:5% Eu3+,5% Li+ (ref. 82) | DS | 2.5 fold (PL) | Increased crystallinity and grain size |
YPO4:5% Eu3+,3% Li+ (ref. 83–85) | DS | — (PL) | Increased crystallinity |
YVO4:0.03% Eu3+,2% Li+ (ref. 86) | DS | 1.43 (PL) | Increased crystallinity and surface roughness |
YVO4:0.03% Eu3+,1% Li+ (ref. 87) | DS | 1.7 (PL) | Increased crystallinity and surface roughness |
Compounds in this family usually have relatively larger phonon cutoff ranges (∼800 cm−1) than Y2O3 and Gd2O3 host matrices, and therefore, for achieving efficient UC emission, sensitization becomes utmost essential. Chung et al.76 have studied the role of Li+ ions on UC emission of the Er3+/Yb3+ doped CaMoO4 phosphor. They observed ∼83 fold enhancement in the green emission of Er3+ ions in the presence of 10 mol% of Li+ ion (see Fig. 4(b)). They attributed it as being due to a favorable structural modification (change in local crystal field symmetry) in the host lattice. The XRD patterns reveal that CaMoO4 phosphor samples containing 2 mol% Er3+, 8 mol%Yb3+ and 0–15 mol% Li+ ion do not show any secondary phases. The diffraction peak (112) shifts gradually toward higher angle up to 5 mol% Li+ ion doping; however contrary to this, upon further increasing Li+ ion concentration it shifts toward smaller angles (see Fig. 4(a)). The gradual peak shift toward higher angle below 5 mol% suggests that the Li+ ions occupy the Ca2+ sites in lattice. However, upon further increasing the concentration of Li+ ions, the ions go to interstitial sites. This leads to the expansion of lattice. The occupation of Li+ ions in the interstitial sites distorts the local crystal field around Er3+ ions, and plays an important role in the enhancement of UC emission.
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Fig. 4 (a) X-ray diffraction patterns of Li+/Er3+/Yb3+ tri-doped CaMoO4 upconversion phosphors (2 mol% of Er3+ and 8 mol% of Yb3+ and 0–15 mol% Li+) near 2Θ = 29° for (112) peak. (b) Photoluminescence spectra of CaMoO4 phosphors fixed values of 2 mol% of Er3+ and 8 mol% of Yb3+ with various Li+ concentrations from 0 to 15 mol%. A comparison of the room temperature (c) photoluminescence excitation (PLE) and (d) PL spectra of YVO4:Eu3+ ceramics with different Li+ ion content. (e) High resolution transmission electron microscopy image of the 500 °C annealed sample of 5 at% Li+ co-doped YPO4:5Eu. (a) and (b) Reprinted (adapted) with permission from ref. 76. Copyright © 2012 Elsevier B. V. All rights reserved. (c) and (d) were published in ref. 86 and are reprinted with permission. Copyright © 2010 Elsevier Masson SAS. All rights reserved. (e) is taken from ref. 84; used in accordance with the Creative Commons Attribution 3.0 Unported License. |
Li et al.77,78 have also studied the effect of Li+ ions in the same host, CaMoO4, but they have used Dy3+ and Tb3+ as the activator ions instead of Er3+. To explain the PL enhancement for Dy3+ doped CaMoO4 in the presence of Li+ ions, they proposed that as the ionic radius in the case of the Dy3+ ion (0.091 nm) is similar to that of the Ca2+ ion (0.099 nm), it can easily be accommodated into the Ca2+ site. However, the Li+ ion, which has a considerably small radius (0.076 nm), will prefer to go into the interstitial spaces. The replacement of divalent calcium by trivalent dysprosium creates charge imbalance, and this imbalance is compensated by Li+ ion co-doping, which enhanced the PL intensity significantly. Further, in another work, Li et al.78 extend their observation for the effect of Li+, Na+ and K+ on the PL enhancement of Tb3+ co-doped CaMoO4 phosphors. A remarkable increase not only in PL, but also for X-ray excited luminescence is also attained for all three alkalis. The maximum PL was observed for 5 mol% Tb3+ and Na+ doped phosphor. The study proposes that the enhanced PL is due to the creation of oxygen vacancies after the occupation of Ca2+ sites by alkali ions.
Phosphor samples (LaVO4:Eu3+) prepared by Park et al.80 have both tetragonal and monoclinic phases. Of these two, the tetragonal phase of LaVO4:Eu3+ showed higher PL than the monoclinic phase. Incorporation of Li+ (0.25 wt%) ions into the LaVO4:Eu3+ (0.07 mol%) phosphor increases the PL remarkably. This is due to the fact that the presence of Li+ ions helps in the monoclinic to tetragonal phase transformation, which causes effective energy transfer from VO43− to Eu3+. Yang et al.86,87 prepared Li-doped (0 to 3 mol%) YVO4:Eu3+ phosphors and observed that as the Li+ ion content increases from 0 to 2 wt%, the PL intensity was improved. The PL intensity of the 2 wt% Li-doped YVO4:Eu3+ phosphor is ∼1.43 times greater than that of YVO4:Eu3+ ceramic (see Fig. 4(c)). They proposed that the enhanced PL is due to improvement in crystallinity as well as due to the enhanced surface roughness.
Parchur et al.81,83–85 in our group have also studied the effect of Li+ ions on PL properties of Dy3+ and Eu3+ doped YPO4 phosphors. The Li+ ion co-doping improves the crystallinity of the material and reduces agglomeration among the particles. Upon addition of Li+ ions, the shift in the (200) diffraction peak towards a lower 2Θ value suggests that the Li+ ions occupy interstitial sites instead of Y3+/Eu3+ sites. Furthermore, the Li+ ion co-doping increases the crystallite size as well (crystallite size corresponding to Li+ = 0, 3, 5, 7 and 10 at% co-doped YPO4:Eu3+ are found to be 20, 23, 36, 42 and 60 nm, respectively). In the high resolution transmission electron microscopy (HRTEM) image (see Fig. 4(e)) of Li+ and Eu3+ co-doped YPO4 phosphor clear, damage free, visible lattice fringes indicate good crystallinity of the sample. This increased crystallinity and grain size causes significant enhancement in PL. Huang et al.82 have also proposed that the increased crystallinity is the main cause of PL enhancement in the Li+ and Eu3+ co-doped YPO4 phosphor (2.5 fold enhancement in 5% Li+ and 5% Eu3+ co-doped YPO4 compared with YPO4:5%Eu3+).
Thus in summary, in Li+ doped ABO4 type of compounds, the main mechanism involved in the PL enhancement is the change in local crystal field symmetry by modification of the crystal lattice, mostly due to interstitial occupancy of Li+ ions and development of vacancies. In addition to this, improvement in crystallinity, grain size, shape, etc. and energy transfer processes also have been accepted as potential mechanisms, as in other hosts too.
Recently, Guanghuan et al.89 studied the effect of alkali ions (Li+, Na+, K+) on PL characteristics (both steady state and time-domain studies) of Eu3+ doped in CaAl2O4 phosphors. Optimum emission was obtained for 3 mol% of Eu3+. Addition of alkali ions was found to enhance the PL intensity significantly. The hypersensitive transition 5D0 → 7F2 evolved as the most intense peak, which was explained as Eu3+ ions occupying a low symmetry site. Since the ionic radii of Eu3+ (0.095 nm) is closer to that of Ca2+ (0.099 nm) than Al3+ (0.051 nm), it prefers to occupy the Ca2+ site rather than Al3+ site. It is suggested that the co-doping of alkali ions works as a charge compensator, induces a lattice distortion and lowers the lattice symmetry, which altogether favors the enhanced emission intensity of the 5D0 → 7F2 transition. The luminescence decay analysis of the CaAl2O4:Eu3+,Li+ phosphor, monitored at 615 nm under 254 nm excitation, reveals a long decay time: luminescence lasts for over 10 ms. It is also noted that the emission intensity is gradually enhanced as the ionic radii of the alkali ion decreases, i.e. minimum for K+ and maximum for Li+ ion. This has been explained as being due to a change in ionic radii of the alkali ions that influence the local structure around the luminescent center ions. This also influences the spin–orbit couplings and crystal field around the Eu3+ ions. The excitation spectra of CaAl2O4:Eu3+,R+ (Li, Na and K) shown in Fig. 5(a)89 depict a broad band in the range of 200–300 nm, which is due to the charge transfer state from O2− to Eu3+ ions. The incorporation of alkali ions in the CaAl2O4:Eu3+ phosphor results in increased CTS band excitation, which might be due to change in Eu–O distances by alkali ion doping.
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Fig. 5 (a) Excitation and emission spectra of CaAl2O4:Eu3+,R+ (R = Li, Na, K) under 254 nm excitation and monitored at 615 nm. (b) Upconversion emission spectra of SrAl2O4:0.01Ho3+,0.20Yb3+,yLi+. Inset shows the picture of the emission of SrAl2O4:0.01Ho3+,0.20Yb3+,0.06Li+ ceramics under excitation wavelength 980 nm. (a) Reprinted (adapted) with permission from ref. 89. Copyright © 2010 Elsevier. All rights reserved. (b) Reprinted (adapted) with permission from ref. 90. Copyright © 2012 Elsevier B. V. All rights reserved. |
Tang et al.90 prepared Ho3+/Yb3+/Li+ co-doped SrAl2O4 phosphors and studied the effect of Li+ ion co-doping on the UC emission of Ho3+ ions. In the first step, the concentration of Yb3+ ions has been optimized to obtain maximum UC emission, and is found to be 0.20 mol fraction. It has been observed that a variation in Yb3+ content brings out significant structural changes in the host lattice. The XRD patterns reveal a pure monoclinic phase of SrAl2O4 for Yb3+ concentration <0.04 mol fraction, above which two new (minor) phases, namely YbAlO3 and Yb2O3, were also identified. Upon increasing the Yb3+ concentration further, the diffraction peaks of the SrAl2O4 lattice shift towards higher angle, which is attributed due to the substitution of Sr2+ (1.12 Å) by Yb3+ (0.86 Å) with a comparatively smaller ionic radius. The presence of Li+ in the next step enhances the UC emission intensity significantly. An enhancement in green UC of up to six fold emission was found for Li+ ion concentration 0.06 (see Fig. 5(b)). This has been proposed both due to charge compensation and grain growth. Due to the low melting point of the lithium compound (Li2CO3, 723 °C), it may work as a flux to accelerate grain growth in the SrAl2O4. In a similar study, Chen et al.91 have prepared a Ce3+, Eu2+, Li+ co-doped SrAl2O4 phosphor. They found that the doping of Ce3+ and Li+ ion enhances the PL intensity of SrAl2O4:Eu2+ significantly.
Sample | DS/UC | Luminescence enhancement | Remarks |
---|---|---|---|
BaTiO3:2%Er3+,3%Li+ (ref. 92) | UC | 56 fold | Local crystal field distortion around Er3+, reduction in OH concentrations |
BaTiO3:1%Er3+,5%Yb3+,7%Li+ (ref. 93) | UC | 10 fold | Local crystal field distortion around Er3+ ions |
CaTiO3:Pr3+,1%Li+ (ref. 94 and 95) | UC | 3.5 fold | Improved crystallinity, increase in surface roughness |
CaZrO3:5%Eu3+,10%Li+ (ref. 96) | DS | 3 fold | Charge compensation |
SrZnO3:Eu3+,M+ (Li, Na, K)97 | DS | — | Charge compensation |
Sun et al.92 have prepared BaTiO3 nanocrystals doped with Er3+ ions, and the effect of Li+ ion co-doping to enhance the PL of Er3+ has been investigated. By using 3 mol% Li+ ions they observed a 56 fold enhancement (see Fig. 6(c)). The authors attributed this enhancement to a change in crystal field symmetry around the Er3+ ion, which has been established through XRD measurements. XRD peaks show a gradual shift with addition of Li+ ions up to 3 mol%, while above 3 mol% doping of Li+ ions a shift in XRD peak position is not observed. Authors suggest that since the Li+ ion has a small ionic radius, it can fit in any crystal site, such as substituting the Ba2+ ion or occupying the interstitial sites. Substitution of divalent Ba by Li+ induces an oxygen vacancy in the matrix. In both the cases it is apparent that the local crystal field around the Er3+ ion will be changed. Another possibility of the Li+ ion doping at the Ti4+ site has been discarded in the study because of the large charge difference between them. Furthermore, it has also been noted that the addition of Li+ ions neutralizes OH groups and so also decreases the non-radiative channels. Thus, the enhanced PL has been attributed to all these factors. In another work on Er3+/Yb3+ co-doped BaTiO3 by Chen et al.,93 time domain studies have also been included to understand the PL enhancement on Li+ ion co-doping. The decay profiles of the 4S3/2 → 4I15/2 (at 548 nm) and 4F9/2 → 4I15/2 (at 660 nm) transitions have been monitored in different compositions of the doped ions e.g. BaTiO3:1% Er3+ and 5%Yb3+ and BaTiO3:1% Er3+ and 5% Yb3+,7% Li+ nanocrystals (see Fig. 6(d)). They found that the lifetime of the 4S3/2 state of BaTiO3:1% Er3+ and 5% Yb3+,7% Li+ nanocrystals (104.4 μs) is longer than BaTiO3:1% Er3+ and 5% Yb3+ nanocrystals (97.5 μs). This has been attributed due to a decrease in non-radiative channels (OH group concentration) after Li+ ion doping.
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Fig. 6 (a) Excitation and (b) emission spectra of CaTiO3:Pr3+ with different concentrations (0.5, 1, 2, and 5 wt%) of Li+ ion co-doped CaTiO3:Pr3+ phosphors. (c) Upconversion emission spectra of BaTiO3:2Er3+ co-doped with 1–6 mol% Li+ ions, under 976 nm laser excitation. The inset shows integral intensity of green and red emission as a function of the concentration of Li+. (d) Decay profiles of the 4S3/2 → 4I15/2 and 4F9/2 → 4I15/2 transitions of Er3+ ions in BaTiO3:1% Er3+,5%Yb3+ and BaTiO3:1%Er3+,5%Yb3+,7%Li+ under 976 nm diode laser excitation. SEM images of (e) CaTiO3:Pr3+ (f) 0.5 wt%, (g) 1 wt%, and (h) 2 wt%, Li-doped CaTiO3:Pr3+ phosphors. (a and b) and (e–h) are published in ref. 94 and reprinted with permission. Copyright © 2011 Elsevier Masson SAS. All rights reserved. (c) Reprinted (adapted) with permission from ref. 92. Copyright © 2011 Elsevier B. V. All rights reserved. (d) Reprinted with permission from ref. 93. Copyright © 2010 Elsevier B. V. All rights reserved. |
Yang et al.94,95 prepared CaTiO3:Pr3+ phosphors with different concentrations of Li+ ions (0.5 to 5.0 wt%). The maximum PL enhancement (∼3.5 times) was observed for the 1.0 wt% Li+ co-doped CaTiO3:Pr3+ phosphor. The excitation spectrum observed by monitoring emission at 613 nm (see Fig. 6(a)) shows a band at 330 nm, which has been assigned as the transition from the valence band to the conduction band, O2− (2p) → Ti4+ (3d). The other band at 380 nm has been attributed to the charge transfer (CT) from Pr3+ to metal ions, Pr3+/Ti4+ ↔ Pr4+/Ti3+. The emission spectrum recorded upon excitation with the charge transfer (CT) band shows high brightness (see Fig. 6(b)). The PL brightness first increases up to 1.0 wt% of Li+ then starts to decrease. The reason behind this has been explored by using XRD and SEM characterization techniques. The XRD analysis reveals that upon addition of Li+ ions up to 1.0 wt%, crystallinity increases, while above this, it starts decreasing. Also, for Li+ concentration of more than 2 wt% some impurity phase was also detected. The SEM images (see Fig. 6(e)–(h)) of CaTiO3:Pr3+ doped with different concentrations of Li+ reveal that the grains of Li-doped CaTiO3:Pr3+ phosphors are highly packed and have larger grain sizes than CaTiO3:Pr3+. On the basis of these results, it has been concluded that the high density of packing and improved crystallinity leads to higher oscillating strengths for the optical transitions. Also, the addition of Li+ ions creates oxygen vacancies. Due to strong mixing of charge transfer states, the oxygen vacancies act as sensitizers for the energy transfer from host to Pr3+ ion. These factors together are responsible for enhanced photoluminescence of activator ions.
Du et al.96 prepared Eu3+ and Li+ co-doped CaZrO3 nanocrystals. The optimum doping level of Eu3+ is 5 mol%, above which the PL start decreasing due to concentration quenching. The closed packed structure of CaZrO3 does not have space to accommodate interstitial atoms. Eu3+ ions substitute at Ca2+ sites. Because of the substitution of Ca2+ by Eu3+ there would be some charge difference. The addition of 10 mol% of Li+ ion into the CaZrO3 lattice enhances the PL three fold and further increase in Li+ concentration decreases the PL intensity. The enhancement in the PL intensity has been attributed to the lattice distortion produced after Li+ ion doping. The lattice distortion reduces the symmetry around Eu3+ ions and increases the PL intensity of the 5D0 → 7F2 transition. Yu et al.97 have prepared a series of luminescent materials, SrZnO2:Eu3+,M+ (M = Li, Na, K). As the ionic radius of Eu3+ is closer to Sr2+ than Zn2+, it would prefer to occupy the Sr2+ site. The substitution of Eu3+ for Sr2+ results in charge imbalance. The incorporation of alkali metal ions enhanced the PL intensity, which has been attributed due to charge compensation.
Sample | DS/UC | Luminescence enhancement | Remarks |
---|---|---|---|
MgO:1.5%Dy3+,20%Li+ (ref. 98) | DS | 4 fold (PL) | Improved crystallinity, increased grain size, change in size, change in crystal field around Dy3+ ions |
SnO2:Eu3+,Li+ (ref. 99) | DS | 14 fold (PL) | Improved crystallinity, increased grain size, increased oxygen vacancies |
TiO2:Er3+,Yb3+,Li+ (ref. 101) | UC | 215 fold (PL) | Change in local crystal field around Er3+ ion |
ZnO:Er3+,Li+ (ref. 102) | UC | PL switching (red to green) | Change in local crystal field around Er3+ ion, increased crystallinity |
ZnO:Dy3+,Li+ (ref. 103) | DS | 10 fold (PL) | Radiative recombination of the large amount of trapped carriers excited from ZnO host, improved crystallinity |
ZnO:Er3+,Li+ (ref. 104) | UC | 120 fold (PL) | Change in local crystal field around ions, reduced OH group concentration |
ZrO2:Er3+,Yb3+,Li+ (ref. 105) | UC | 1.5 fold (PL) | Change in local crystal field around ions, increased grain size |
Gu et al.98 have prepared Dy3+ and Li+ co-doped MgO nanocrystals. Li+ ion co-doping enhances the emission of Dy3+ ions, which has been concluded to be due to improved crystallinity and grain size and a change in symmetry around Dy3+ ions. The first conclusion has been drawn on the basis of XRD and TEM measurements, while the ratio of intensity of the magnetic and electric dipole allowed transitions (4F9/2 → 6H15/2 and 4F9/2 → 6H13/2 transitions) of Dy3+ has been calculated to give an idea of the site symmetry around the dysprosium ions. The XRD studies reveal a pure cubic structure for MgO:Dy3+ and Li+ co-doped samples. The incorporation of Li+ ions increases the crystallinity of the MgO nanocrystals. TEM images of MgO crystals exhibit cuboid lamellar morphology with a mean particle size of ∼20 nm, which remains unchanged upon addition of Dy3+ ions. However, in presence of Li+ ions, the crystallite size increases to 30–40 nm. They proposed that during the combustion process Li2O may melt/or react with MgO and Dy2O3 and thus form a eutectic liquid, which helps to improve the crystallinity. The 4F9/2 → 6H15/2 and 4F9/2 → 6H13/2 transitions of Dy3+ ion are known as magnetically allowed (hardly vary with the crystal field strength around the dysprosium ion) and forced electric dipole transitions (being allowed only at low symmetries with no inversion center), respectively. The ratio of the intensities between the electric dipole and the magnetic dipole gives information about the site symmetry in which the dysprosium ion is situated. Under excitation at 273 nm, the asymmetry ratio of the Dy3+ doped MgO sample is 1.3, whereas for the 20% Li+ co-doped sample, it found to be 1.5 and also the PL increases four fold (see Fig. 7(a)). The variation of the asymmetry ratio indicates a change in symmetry and vibrational modes around the Dy3+ ions by Li+ ion doping.
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Fig. 7 (a) Emission spectra of SnO2:Eu and Sn0.8Li0.2O2−δ:Eu under the excitation wavelength of 300 nm. Room temperature upconversion spectra of (b) Er3+ doped and (c) Er3+–Li+ (1.0 mol%) co-doped ZnO nanoparticles under 980 nm diode laser excitation. (d) Powder X-ray diffraction patterns of Er3+:ZrO2 with and without Li+ ions and Er3+/Yb3+:ZrO2 with and without Li+ ions in the range of 27–33°. (e) UC emission spectra of ZrO2:Er3+/Li+ (0 or 5 mol%) nanocrystals under 976 nm excitation. The inset shows the ln–ln plot of intensity versus excitation power dependence of the green and red emissions. (a) Reprinted with permission from ref. 99. Copyright © 2005 Elsevier B. V. All rights reserved. (b) and (c) Reprinted with permission from ref. 102. Copyright © 2008 Elsevier B. V. All rights reserved. (d) and (e) Reprinted with permission from ref. 105. Copyright © 2011 Elsevier B. V. All rights reserved. |
Zhang et al.99 have prepared Eu3+ and Li+ co-doped SnO2 phosphors. SnO2 has a tetragonal structure (space group of P42/mnm), in which the Sn atom occupies a slightly distorted octahedral site. The Eu3+ ions go into the Sn4+ sites, therefore the local environment around Eu3+ ions should be of high symmetry, which weakens the 5D0 → 7F2 (613 nm) transition compared to 5D0 → 7F1 transition. Li+ doping increases the crystallinity and particle size (established through XRD measurements), which induces a remarkable increase in PL intensity. Further, the occupation of Sn4+ sites by Li+ ions would naturally give rise to a considerable number of vacant sites in the oxygen ion array and then expand the lattice to decrease crystal density, which may also promote increased PL.
Kallel et al.100 have prepared Y3+ and Li+ co-doped TiO2 nanoparticles, which have rutile phase. Traces of Y2Ti2O7 anatase are also found for the Y3+ doped titania powder. PL studies reveal that incorporation of Li+ induces a long lived PL on the order of millisecond time range, with a maximum at 724 nm. As the Li+ and Y3+ concentration increases to 7% or 10%, an increase in emission intensity is observed. Cao et al.101 have investigated 1 mol% Er3+, 10 mol% Yb3+ and 0–20 mol% Li+ tri-doped TiO2 nanocrystals. The XRD pattern reveals that 1Er:TiO2 has tetragonal rutile phase of TiO2 with some impurity phase due to Er2Ti2O7. On addition of 10 mol% Yb3+ a new phase, Yb2Ti2O7, was observed along with rutile TiO2 and Er2Ti2O7 phases. From the shifts in XRD peak positions of TiO2, it is revealed that for low Li+ ion concentration (1–2 mol%), Li+ occupies Ti4+ sites, whereas for higher Li+ concentration (5–20 mol%) it goes to interstitial sites. Upon Yb3+ and Li+ co-doping, the intensity of green and red bands of Er3+ increases significantly. This has been attributed to the energy migration between the Er3+ and Yb3+, as well as the distortion of crystal field symmetry of Er3+ for lower concentrations of Li+, and phase transformation at higher Li+ concentration.
Han et al.102 have prepared Er3+ doped ZnO nanoparticles. Under 980 nm excitation, this produces strong red emission. Upon Li+ ion co-doping, a luminescent switching between the main red emission band and the green band of Er3+ is seen (see Fig. 7(b) and (c)). They proposed that the change in UC emission behavior is due to the modification of the local crystal field around the Er3+ ions due to the introduction of Li+ ions. Fig. 7(b) shows the XRD patterns of the as prepared and annealed Er3+ doped samples. Gu et al.103 have prepared Dy3+ doped ZnO nanocrystals. It is observed that the Li+ co-doping in ZnO:Dy3+ nanocrystals increases PL by 10 fold. They proposed that since the f–f absorption transitions in lanthanide ions are forbidden, the number of carriers excited through f–f transitions in Dy3+ ions is much less in comparison to those excited through band gap excitation of ZnO. Thus, the improvement in Dy3+ emission is mainly due to the radiative recombination of the large amount of trapped carriers excited from ZnO host. The increased recombination probability enhances the emission of Dy3+ by energy transfer process. In addition, the incorporation of Li+ ions can create oxygen vacancies, which might act as the sensitizer for the energy transfer to the rare earth ion due to the strong mixing of charge transfer states, resulting in the highly enhanced luminescence. Further, they have reported reduction of the asymmetry ratio, which suggests a change of symmetry and vibrational modes around the luminescent Dy3+ centers by Li+ doping. Bai et al.104 have also studied the role of Li+ ions on Er3+ doped ZnO nanocrystals. They have also observed enhanced UC emission intensity of Er3+ ions upon Li+ co-doping. Though the Li+ ion does not have enough energy to destroy the ErO6 structure, yet, it may alter the local structure around Er3+ which affects the 4f–4f transitions of Er3+ ion, which results in UC emission enhancement. Further, Li+ ion also reduces the OH− group concentration, which is another reason for the UC emission intensity enhancement.
Liu et al.105 have demonstrated the UC emission in Er3+, Yb3+ and Li+ tri-doped ZrO2 nanocrystals. The incorporation of Li+ ions increases the emission intensities of green and red bands of Er3+ by a factor of 1.93 and 1.65, respectively. The XRD pattern reveals that Er3+ doped ZrO2 samples have both tetragonal and monoclinic phases. Yb3+/Er3+ co-doping increases the formation of the tetragonal phase in the sample. Further, the incorporation of Li+ suppressed the tetragonal phase in the Yb3+/Er3+ doped ZrO2 sample (Fig. 7(d)). Further, upon Li+ doping the slope of the excitation power versus UC emission intensities curve decreases (see Fig. 7(e)), which suggests that Li+ ions can tailor the local structure of the host lattice and thus can improve energy transfer processes from Yb3+ to Er3+ ions.
Sample | Change in luminescence properties | Remarks |
---|---|---|
NaYF4:Yb3+/Er3+,K+/Li+ (ref. 107) | UC emission intensity decreases upon Li+ doping, whereas it increases upon K+ doping | Change in morphology and crystal structure upon Li+ doping and lowering of crystal symmetry around Er+ ions in K+ doping |
GdF3:Yb3+/Er3+,Li+ (ref. 108) | Change in UC emission color from yellow to red, red emission is 8 times higher than in NaGdF4:Yb3+/Er3+ | Change in crystal symmetry around Er3+ ions, back energy transfer |
NaYbF4:Yb3+/Er3+,Li+ (ref. 109) | UC color tunability | Change in crystal symmetry around Er3+ ions and weakened polarization effect |
NaYF4:Yb3+/Tm3+,K+/Li+ (ref. 110) | Decrease in concentration quenching | Crystal distortion and increased crystal size |
NaGdF4:Yb3+/Er3+,Li+ (ref. 111) | Enhanced UC luminescence (47 fold for green and 23 for ions, increased crystal size, increased red), increased paramagnetism lifetime of 4S3/2 state, decrease in distance between Gd3+ ions (for increased paramagnetism) | Change in crystal symmetry around Er3+ |
ErF3:Er3+,Li+ (ref. 112) | Four fold enhancement in UC emission | Change in crystal symmetry around Er3+ ions |
Lu6O5F8:Yb3+/Er3+,Li+ (ref. 113) | Increased UC emission | Change in crystal symmetry around Er3+ ions, increased crystallinity, reduced quenching centers (OH−) |
NaYF4:Yb3+/Er3+,K+/Li+ (ref. 114) | Color tunability of UC emission | Change in crystal structure and lowering of crystal symmetry around Er+ ions |
Mao et al.107 have studied the effect of alkali ions (Li+ and K+) on crystal structure and UC emission of NaYF4:Yb/Er crystals. It was observed that the Li+ ion co-doping in the NaYF4:Yb/Er crystals affects the morphologies to a greater extent and significant changes from rod-like shape to disk shape and finally to polyhedron structure is attained. However, K+ ion co-doped NaYF4:Yb/Er crystals do not show any change in morphology and they almost maintain the rod-like shape throughout (see schemes (a) and (c) in Fig. 8). The crystal structure analysis further reveal that not only the surface morphology, but also the phase transition from β-hexagonal to tetragonal (LiYF4) in LixNa1−xYF4 crystals is initiated at x = 0.5, whereas the phase of KyNa1−yYF4 remains stable up to y = 0.85. The UC emission studies show that as the Li+ content increases in the crystal, UC emission intensity decreases, whereas the UC emission intensity of NaYF4:Yb/Er crystals increases (K0.7Na0.3YF4:Yb, Er crystal shows 8 and 7 fold enhancement in green and red UC emission, respectively) when K+ ions are introduced into the crystal (see Fig. 8(b) and (d)). The change in UC emission is related to the change in crystal structure, surface morphology, and distance between alkali and fluorine atoms. In the Li+ doped crystal, the Li–F distance will be larger than the Na–F distance, which can intensify the interaction between F− and Er3+ in the crystal lattice, which may enhance the phonon energy of Er3+ ions. On the other hand, substitution of Na+ ions with K+ ions in the lattice reduces the inter-quenching of Er+ and decreases the local crystal field symmetry, which increases UC intensity. In a similar work, Dou and Zhang114 have also studied effect of Li+ and K+ ions doping on crystal structure and UC emission behavior of NaYF4:Yb/Er. The phase transition in NaYF4:Yb/Er crystal, has also been observed by Dou and Zhang114 upon Li+ ion doping, but instead of hexagonal to tetragonal phase transition, as observed by Mao et al.,107 they observed hexagonal to cubic phase transition. The UC studies reveal that the intensity ratios between the blue, green, and red emission peaks change upon Li+ and K+ doping in the crystal. They have proposed that the Li+ or K+ doping will slightly change the size of the unit cell in the crystal and then to change the Yb–Er distance, which can influence energy transfer process. On the other hand, the higher concentration of K+ ions in the crystal causes formation of a new K2NaYF6 phase. The coordination number of RE is 9 in hexagonal phase, 8 in cubic phase and 6 in K2NaYF6 phase. This suggests that the K2NaYF6 phase is less stable than the cubic and hexagonal phases. Further, Misiak et al.110 have shown that Li+ doping in the cubic NaYF4:Yb3+/Tm3+ colloidal crystals significantly reduces the concentration quenching. Interestingly, the initial UC emission intensity decreases at first, and then starts increasing. This might be due to the fact that initially Li+ ions substitute the Na+ ions in the lattice, while further increase in the Li+ ion concentration results in the occupancy of Li+ ions in the interstitial sites, which results in increase in the crystal size. Further, substitution of Na+ by Li+ introduces distortion in the lattice, which prevents concentration quenching.
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Fig. 8 (a) Schematic illustration of the formation process of LixNa1−xYF4 with various morphologies. (b) UC luminescence spectra of the as-prepared LixNa1−xYF4:Yb3+/Er3+ products under 980 nm excitation at room temperature (x = 0, 0.15, 0.30, 0.50, 0.70, 0.85 are denoted by S0 to S5). (c) Schematic illustration for the possible formation process of KyNa1−yYF4:Yb3+/Er3+ with various morphologies. (d) UC luminescence spectra of the as-prepared KyNa1−yYF4:Yb3+/Er3+ products under 980 nm excitation at room temperature (y = 0.15, 0.30, 0.50, 0.70, 0.85 are denoted by S6 to S10). The inset shows the integral intensity of green and red emission as a function of the concentration of K+ ions. Reprinted with permission from ref. 107 Copyright © 2013 Elsevier B. V. All rights reserved. |
Similar to NaYF4, co-doping of alkali Li+ brings out significant changes in crystal structure and the optical properties are greatly improved. Cheng et al.111 have studied the effect of Li+ ions on UC emission of β-NaGdF4:Yb3+/Er3+ nanoparticles. It is found that the presence Li+ ions in the crystal enhanced UC emission drastically (nanoparticles doped with 7 mol% Li+ ions show 47 and 23 fold enhancement in green and red UC emission peaks, respectively). The enhanced UC emission is attributed to the distortion of the local asymmetry around Er3+ ions. The presence of Li+ in the nanoparticles also helps in the growth of the crystals, which is proved by XRD studies. Another contributing factor to the enhanced UC is the increased lifetime of the 4S3/2 state of NaGdF4:Yb3+/Er3+ NPs in the Li+ ions doped crystals (see Fig. 9) which causes increased population in the 4S3/2 state, resulting in enhanced green emission. Furthermore, the presence of Li+ also increases paramagnetic behavior of the nanoparticles. This is attributed to the increase in Gd3+ molar concentration in NaGdF4 resulting due to introduction of Li+ ions. Zhang et al.109 have also studied the effect of Li+ ions on the UC emission behavior of NaYbF4:Er microcrystals. Interesting, they observed a blue shift in UC emission bands. The XRD studies show hexagonal to tetragonal phase transformation upon Li+ co-doping. In the LiYbF4 crystal, each Yb3+ ion is coordinated to eight F− ions (forming the YbF8 polyhedral units) and each Li+ ion is coordinated to four F− ions (forming the LiF4 tetrahedral units). The crystallographic point site symmetry with S4 symmetry in LiYbF4 is higher than that of NaYbF4 with D2d symmetry. This results in a more symmetrical distribution of electronic density and a weakened polarization effect of the local environment in LiYbF4 causes a blue shift in UC bands. Guo et al.113 have studied the effect of Li+ ions on the UC emission behavior of Lu6O5F8:Yb3+/Er3+ nanoparticles. They have studied UC, DC and CL properties of the materials and all these increases in the presence of Li+ ions. They proposed that increased luminescence properties are due to the increased crystallinity (by flux action of Li), decreased absorption bands of the surface contaminants (OH and CO groups) and distorted local symmetry around the Er3+ ions. Yin et al.108 have studied the effect of Li+ on UC emission behavior of GdF3:Yb,Er nanoparticles. In GdF3:Yb,Er nanoparticles, the intensity of UC emission in the red region is higher than that in the green region, which results in a bright yellow emission even observable by the naked eye. Upon Li+ doping (0 to 5, 10, and 25 mol%) the green emission intensity gradually decreases and the red emission is enhanced (see Fig. 9 (c)–(g)). This is attributed to the change in local crystal field around Er3+ ions in the presence of Li+ ions in the GdF3:Yb,Er host lattice.
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Fig. 9 (a) UC luminescence spectra of NaGdF4:Yb/Er/Li+ (0–15 mol%) nanoparticles under 980 nm excitation at room temperature. The inset shows the integral intensity of green and red emission as a function of the concentration of Li+ ions. (b) Decay profiles of the 4I11/2/4I13/2 transition in NaGdF4:Yb3+/Er3+ NPs with 0–15 mol% Li+ under 980 nm excitation. (c to f) Luminescence photographs of calcined GdF3:Yb,Er (20, 2 mol%) UCNPs (having 0, 5, 10 and 25 mol% of Li+) dispersed in deionized water. (g) Solid powder (0.20 g) of GdF3:Yb,Er,Li (25 mol%) UCNPs was placed into a quartz vessel and excited under a 980 nm laser to visually demonstrate the naked-eye-visible brilliant red light. (a and b) Reproduced from ref. 111 with permission from The Royal Society of Chemistry. (c–g) Reprinted with permission from ref. 108 Copyright © 2012 Wiley-VCH Verlag GmbH&Co. KGaA, Weinheim. |
Thus in summary, it is pointed out that alkalis in fluorides and similar hosts effectively modify the crystal structure and affect the surface morphology, phase, particle size, crystallinity, etc. In this way the crystal field around the lanthanide ion is favorably changed. Not only this, the doping of alkalis makes a significant change in critical separation between lanthanide ions, lanthanide-alkali ions, lanthanide-fluorine ions, lanthanide activator and sensitizers, etc., due to which energy transfer processes become effective, giving rise to an increase in the UC emission. A change in the different components of the emission viz. blue, green and red varies systematically, which creates opportunities for color tunability also. Above all this, a specific blue shift is also observed, which is peculiar in this host. Some interesting observations, although beyond the scope of this study, e.g. increase in the paramagnetic behavior, could be very useful for readers.
Sample | DS/UC | Luminescence enhancement | Remarks |
---|---|---|---|
Ba2GdNbO6:Eu3+/Dy3+,Li+ (ref. 115) | DS | — | Improved crystallinity, increased grain size |
BaZn2(PO4)2:Sm3+,R+ (Li, Na, K)116 | DS | — | Charge compensation |
Ca3B2O6:Dy3+,Li+ (ref. 117) | DS | — | Charge compensation, flux effect, change in local environment around Dy3+ ions |
CaSO4:Tm3+/Dy3+,Li+ (ref. 118) | TL | — | Creation of charge trap centers |
(Y, Gd)BO3:Tb3+,Li+ (ref. 119) | DS | — | Spherical and non-agglomerated, particles, strong lattice distortion |
YNbTiO6:Eu3+,Li+ (ref. 120) | DS | 3 fold | Improved crystallinity, increased grain size |
YBO3:Eu3+,Li+ (ref. 121) | DS | Improved crystallinity, increased grain size | |
Zn2SiO4:Yb3+,Er3+,Li+/Bi3+ (ref. 122) | UC | — | Change in local environment around Er3+ |
SrB4O7:Eu2+, Li+ (ref. 123) | DS | — | Change in electric field distribution in lattice structure |
Lu2SiO5:Ce,Li+ (ref. 125) | DS | 2.2 fold | Change in crystal field around Ce3+ |
Y2MoO6:Eu3+,Li+ (ref. 126) | DS | — | Improved crystallinity |
NaSrBO3:Tb3+,Li+ (ref. 127) | DS | — | Charge compensation |
Sr2SiO4:Eu3+,(Li+, Na+, K+)129 | DS | — | Charge compensation |
CaSnO3:Tb3+,(Li+, Na+, K+)131 | DS | — | Charge compensation |
Gd6MoO12:Li+/Ln3+ (ref. 132), (Ln3+ = Yb3+/Er3+/Tm3+) | UC | — | Change in crystal symmetry around Ln3+ |
Y2SiO5:Pr3+,Li+ (ref. 133) | UC | 9 fold | Change in crystal symmetry around lanthanide ions, reduction in activator ions clustering |
Y2Zr2O7:Dy3+,Li+ (ref. 134), (Ln3+ = Yb3+/Er3+/Tm3+) | UC | 2 fold | Improved crystallinity |
LixCa1−2xEuxSiyMo1−yO4 (ref. 136) | DS | — | Charge compensation |
Ca2BO3Cl:Sm3+(Li+, Na+, K+)139 | DS | — | Charge compensation |
CaSi2O2N2:Eu2+,Dy3+,Li+ (ref. 140) | DS | — | Charge compensation |
The possible explanation for the enhanced PL intensity of the lanthanide ions in the presence of Li+ ions can be summarized as follows. When Li+ ion is introduced into any matrix, because of its smaller ionic radius, it can either substitute the cation of the matrix or occupy interstitial sites of the matrix, which usually depends on the concentration of doped alkali. As the Li+ ion concentration increases, the possibility to occupy the interstitial sites increases, which distorts the matrix significantly. In a few hosts, changes even in the phase and crystal structure are also noted. The change in crystal structure can also change the occupancy site of the lanthanide ions. Also, due to the lower melting temperature of the Li, it can work as a flux and increase the crystallinity and the grain size of the materials. In addition, it is also found that Li+ ions decrease the concentration of the inorganic/organic groups that work as non-radiative channels and cause a decrease in the PL intensity. Further, when a trivalent lanthanide ion replaces a divalent cation it produces charge imbalance in the matrix that can be compensated by using alkali ions. All these factors favor luminescence enhancement of the lanthanide ions. In the case of Ce3+ and Eu2+ ions, by changing the local crystal fields around the activator ions, they can also be used for tuning the color of the luminescence materials. Furthermore, in fluoride host matrices, co-doping of Li+ causes a change in separation between lanthanide ions, lanthanide-alkali ions, lanthanide-fluorine ions, lanthanide activator and sensitizers, etc., which strongly influences the energy transfer processes. Thus, it can be concluded that the Li+ ions (alkali ions) modify host matrices in many ways, which favors radiative transitions, causing enhancement in the luminescence intensity. Since this review provides in-depth case studies for various hosts, and describes the effect of various matrix parameters (e.g. crystal structure, crystallinity, grain size, surface morphology, quenching entities, etc.) on PL, therefore, it could also be useful as input for designing various novel lanthanide doped luminescent materials.
The effects of co-doping with Li+ ions have been used for almost all different types of luminescence mechanisms including photoluminescence/downshifting, upconversion, thermo-luminescence/persistent emission, cathado-luminescence, etc. However, its use for one of the most important class of emissions, i.e. quantum-cutting, is still lagging and has strong scope for future studies.
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