Abstract:In this article we describe the redshift of the charge transfer band of nanosized cubic (Y 1−x Eu x ) 2 O 3 upon increasing the Eu 3+ concentration. This redshift amounts to 0.43 eV (25 nm) in going from 0.1 Mol % Eu 3+ to 100 Mol % (which is pure Eu 2 O 3 ). The charge transfer band consists of two broad sub-bands; both shift almost parallel with the Eu 3+ concentration and are related to the two symmetry sites for the cation, C 2 and C 3i , in the bixbyite-type lattice. The area ratio of the bands is 3:1 and… Show more
“…Due to fundamental and technological importance, the charge-transfer (CT) phenomenon has been a key area of research. − For technologically important rare-earth ions like Eu 3+ , which inherently have poor excitation efficiency, charge transfer plays a central role in governing their luminescent properties . CTB is useful for sensitization of Eu 3+ luminescence, because it can act as an antenna to absorb incoming light and then transfer excitation energy to the Eu 3+ ion, in a way similar to sensitization by organic chromophores. − Common Eu 3+ phosphors have broad CTB of O 2– → Eu 3+ originating due to transfers of an electron from a neighboring oxygen 2p orbital to an empty 4f orbital of Eu 3+ ion. ,, Previously, many attempts have been made to find factors influencing CT energy (i.e., the position of CTB in the excitation spectra) both qualitatively and quantitatively. ,− In these investigations, CTB has been found to be dependent on host structure, sites occupied by Eu 3+ ion in the host matrix, ionicity/covalency of Eu–O bond, position of the valence band/electronic structure, etc.…”
The dominant intensity of parity-forbidden intra-4f transitions of europium(III) over O → Eu charge-transfer band (CTB) intensity is against common perceptions, yet this trend is observed in many germanate hosts and has not been rationalized so far. In search of a plausible explanation for this unusual trend, present work reports an experimental and theoretical investigations in conjunction on two sibling germanate host, namely, Y 2 GeO 5 and Y 2 Ge 2 O 7 having dopant Eu 3+ in their respective YO 7 polyhedra. Whereas for Y 2 GeO 5 :Eu 3+ , the CTB is more intense than the intra-4f transitions in the excitation spectrum, in the case of Y 2 Ge 2 O 7 :Eu 3+ , the relative intensities of CTB and intra-4f transitions are reversed. Comparative structural analysis reveals that Eu 3+ present in YO 7 of Y 2 GeO 5 has a greater number of tetra-coordinated oxygen (O tetra ) and yttrium atom as first and second neighbors, respectively (Eu 3+ −O tetra −Y 3+ linkages). Conversely, in Y 2 Ge 2 O 7 host, the Eu 3+ ion mostly has tricoordinated oxygen (O tri ) as its nearest neighbor and germanium ions next to O tri (Eu 3+ −O tri −Ge 4+ linkage). Theoretical calculations reveal that while Y 2 GeO 5 :Eu has O tetra (4Y) dominating at the Fermi level and the 4f state of Eu 3+ remains inert toward mixing, in Y 2 Ge 2 O 7 :Eu, the Fermi level has major contribution from O tri (2Y + 1Ge) with significant mixing with 4f states of Eu. The dominant control of Eu 3+ −O tri −Ge 4+ linkages in geometrical and electronic structure of Y 2 Ge 2 O 7 :Eu owing to the GeO 4 surrounding has been attributed to relative poor intensity of O → Eu CTB. Siege of Eu 3+ by GeO 4 and subsequent occurrence of Eu 3+ −O tri −Ge 4+ linkages play a dual role: First, it induces electronic rigidity to hinder excitation of electron at bridging (O tri ) oxygen by highly charged small Ge 4+ cation; second, the covalent character in Eu−O bond is achieved by intermixing of Eu's 4f and O tri 2p orbital which facilitates relaxing of the parity-selection rule thus enhancing the probability of intra-4f transitions. The inferences drawn remain valid when extrapolated to other inorganic oxides having EuO x polyhedra surrounded by covalent units like PO 4 , SiO 4 , etc. and have a prevailing number of low-coordinated oxygen atoms and highly charged small cation in the first and second coordination shells, respectively. The optical basicity concept is also found to endorse our explanation. These remarkable generic inferences will pave the rational way for designing efficient phosphors for solidstate lighting.
“…Due to fundamental and technological importance, the charge-transfer (CT) phenomenon has been a key area of research. − For technologically important rare-earth ions like Eu 3+ , which inherently have poor excitation efficiency, charge transfer plays a central role in governing their luminescent properties . CTB is useful for sensitization of Eu 3+ luminescence, because it can act as an antenna to absorb incoming light and then transfer excitation energy to the Eu 3+ ion, in a way similar to sensitization by organic chromophores. − Common Eu 3+ phosphors have broad CTB of O 2– → Eu 3+ originating due to transfers of an electron from a neighboring oxygen 2p orbital to an empty 4f orbital of Eu 3+ ion. ,, Previously, many attempts have been made to find factors influencing CT energy (i.e., the position of CTB in the excitation spectra) both qualitatively and quantitatively. ,− In these investigations, CTB has been found to be dependent on host structure, sites occupied by Eu 3+ ion in the host matrix, ionicity/covalency of Eu–O bond, position of the valence band/electronic structure, etc.…”
The dominant intensity of parity-forbidden intra-4f transitions of europium(III) over O → Eu charge-transfer band (CTB) intensity is against common perceptions, yet this trend is observed in many germanate hosts and has not been rationalized so far. In search of a plausible explanation for this unusual trend, present work reports an experimental and theoretical investigations in conjunction on two sibling germanate host, namely, Y 2 GeO 5 and Y 2 Ge 2 O 7 having dopant Eu 3+ in their respective YO 7 polyhedra. Whereas for Y 2 GeO 5 :Eu 3+ , the CTB is more intense than the intra-4f transitions in the excitation spectrum, in the case of Y 2 Ge 2 O 7 :Eu 3+ , the relative intensities of CTB and intra-4f transitions are reversed. Comparative structural analysis reveals that Eu 3+ present in YO 7 of Y 2 GeO 5 has a greater number of tetra-coordinated oxygen (O tetra ) and yttrium atom as first and second neighbors, respectively (Eu 3+ −O tetra −Y 3+ linkages). Conversely, in Y 2 Ge 2 O 7 host, the Eu 3+ ion mostly has tricoordinated oxygen (O tri ) as its nearest neighbor and germanium ions next to O tri (Eu 3+ −O tri −Ge 4+ linkage). Theoretical calculations reveal that while Y 2 GeO 5 :Eu has O tetra (4Y) dominating at the Fermi level and the 4f state of Eu 3+ remains inert toward mixing, in Y 2 Ge 2 O 7 :Eu, the Fermi level has major contribution from O tri (2Y + 1Ge) with significant mixing with 4f states of Eu. The dominant control of Eu 3+ −O tri −Ge 4+ linkages in geometrical and electronic structure of Y 2 Ge 2 O 7 :Eu owing to the GeO 4 surrounding has been attributed to relative poor intensity of O → Eu CTB. Siege of Eu 3+ by GeO 4 and subsequent occurrence of Eu 3+ −O tri −Ge 4+ linkages play a dual role: First, it induces electronic rigidity to hinder excitation of electron at bridging (O tri ) oxygen by highly charged small Ge 4+ cation; second, the covalent character in Eu−O bond is achieved by intermixing of Eu's 4f and O tri 2p orbital which facilitates relaxing of the parity-selection rule thus enhancing the probability of intra-4f transitions. The inferences drawn remain valid when extrapolated to other inorganic oxides having EuO x polyhedra surrounded by covalent units like PO 4 , SiO 4 , etc. and have a prevailing number of low-coordinated oxygen atoms and highly charged small cation in the first and second coordination shells, respectively. The optical basicity concept is also found to endorse our explanation. These remarkable generic inferences will pave the rational way for designing efficient phosphors for solidstate lighting.
“…On the other hand, amorphous local structures around Eu 3+ provide lower excitation energy in CTB around 250 nm due to longer EuO bonding length. 20)…”
In this study, Eu 3+-doped ZrO 2 nanophosphors were obtained by a solgel method with HNO 3 as a catalyst, which led to white powders of small ZrO 2 nanocrystals after low temperature calcination. However, exothermic reactions of NO 3 ¹ were observed during the heat-treatment leading to ZrO 2 crystallization. To avoid such reactions and to understand the initial crystallization of ZrO 2 doped with Eu 3+ ions, we developed an original route in which the xerogel powders were pre-washed in ethanol before immersing them in Eu 3+ solution to remove NO 3 ¹. The effects of heat-treatment on the Eu 3+ photoluminescence (PL), crystallization of ZrO 2 xerogels, and Eu 3+ localization were studied with PL spectroscopy, thermogravimetric analysis and powder X-ray diffraction. It was found that the amorphous ZrO 2 xerogels crystallized in a tetragonal structure, with a small amount of monoclinic ZrO 2 also being precipitated after longer calcination periods. Finally, the Eu 3+ ions on the surface of the ZrO 2 xerogels were found to diffuse into higher symmetric Zr substitutional sites in the tetragonal ZrO 2 matrix after heat-treatment.
“…In ref. 24 we have suggested that this could be caused by a difference in compressibility between the Y 2 O 2 S:Tb 3+ and the Gd 2 O 2 S:Tb 3+ lattices. In this reference we have already mentioned that the proposed electrostatic model in terms of the Madelung energy leads to a similar result as the chemical shi model proposed by Dorenbos.…”
Section: Redshi Of Ct-bandmentioning
confidence: 88%
“…Recently we have introduced an electrostatic model in terms of the Madelung energy of the transferred charge that could quantitatively describe the red shi of the CT-band in Y 2 O 3 :Eu 3+ . 24 This model will now be applied to the data presented in Fig. 6a 25 The charge transfer during excitation of a photon can be represented by the following reaction:…”
Section: Redshi Of Ct-bandmentioning
confidence: 99%
“…We have recently argued that red shi of the CT-band, represented by DE CT , can be described by the Madelung energy of the inserted eh-pair. 24 Eqn (5) implies that the Madelung energy of the insertion of 33 eh-pairs needs to be evaluated, in which a fraction of the electron is positioned at the Ln 3+ site and a (smaller) fraction of the hole at the O 2À and S 2À sites. The Madelung energy DEM eh (x) for inserting 33 eh pairs in the Ln 2 O 2 S lattice can be written as…”
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