Jing
Cuan
and
Bing
Yan
*
Department of Chemistry, Tongji University, State Key Lab of Water Pollution and Resource Reuse, Siping Road 1239, Shanghai 200092, China. E-mail: byan@tongji.edu.cn; Fax: +86-21-65981097; Tel: +86-21-65984663
First published on 5th November 2013
This paper is focused on the preparation and characterization of luminescent hybrid materials of zirconia (alumina, titania) xerogels encapsulated with high luminescent lanthanide polyoxometalates via a sol–gel process. Firstly, liquid compound 1-methyl-3-propionyloxy imidazolium bromide (IM+Br−) is assembled with lanthanide polyoxometalates (NaLnW10O36·32H2O, abbreviated as LnW10, Ln = Eu, Tb, Sm, Dy) through the ion exchange reaction, resulting in Ln-IL, Then Ln-IL is connected to zirconia (alumina/titania) by the chelating reaction between a propionyloxy group of the IM+ component and metallic alkoxides (Zr(OCH2CH2CH2CH3)4, Ti(OCH(CH3)2)4, Al(OCH(CH3)2)3) under mild conditions after hydrolysis and condensation. These hybrid materials are characterized by Fourier transform infrared spectroscopy, wide angle X-ray diffraction, thermogravimetric analysis, as well as luminescence. The above measurements indicate that they possess high thermal-stability, amorphous structure features and especially favorable luminescent performances such as long luminescent decay lifetime, high quantum yield. It is found that alumina and zirconia are superior matrices to titania for the luminescence of lanthanide polyoxometalates, and close white-light integration can be realized for hybrids of titania gels.
Lanthanide polyoxometalates (Ln-POMs) are a class of compounds built by inorganic metal–oxygen cluster with lanthanide ions. Ln-POMs exhibit wealthy properties such as topologies and physical (optical, electrical, and magnetic) properties,9 which have potential application in the fields of optics,10 catalysis, biology, material and medical science.11 Among Ln-POMs, lanthanide decatungstates (Na9LnW10O36·36H2O) possess outstanding luminous natures such as long emission lifetime scale (from μs to ms) and high quantum yields, which is a favorable photoactive species for lanthanide hybrid material. Naturally, Ln-POMs anions can be easily to assemble with ionic liquid compounds through electrostatic force between cations and anions, which are promising luminescent soft materials.12 Simple carboxylate ligands are known to support mononuclear TiIV structures, so carboxyl functional groups of task-specified ionic liquid (TSIL) can graft on the transition metal (zirconium, titanium, aluminum) skeleton by chelating bonds.13
Ionic liquid compounds are entirely constructed by inorganic anions with large blocks of organic counterions like phosphonium, quaternary ammonium, imidazolium or pyridinium.14 They are applied to the fields of solvents, synthesis, catalysis, separations, electrochemistry owing to their environment friendly property, wide electrochemical window, low vapor pressure and tunable physicochemical properties.14,15 It needs to refer that some ionic liquid derivatives can be expected to behave chemical linkage to construct functional hybrids. Lately, some reports are focused on luminescent soft hybrid materials centered with lanthanide complexes dispersed into ionic liquids or chemically bonded with host through ionic liquids as linkage.16,17 These soft hybrid systems present excellent luminescent performance such as high quantum yield and superior photostability.18 In the hybrid system, lanthanide ions still keep the coordination environment in the crystal framework of polyoxometalates.12,19,20 Especially decatungstoeuropate anion EuW10O369− has been discovered by Peacock and Weakley and shows the best luminescent performance.21
In our work, lanthanide polyoxometalate Na9LnW10O36·36H2O, abbreviated as LnW10, Ln = Eu, Tb, Sm, Dy are embedded into the titania (zirconia, alumina) matrices through special carboxylic derived ionic liquid 1-methyl-3-propionyloxy imidazolium bromide. The physical characterization and especially the photophysical properties of these hybrid materials are studied in details.
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Fig. 1 The composition and the predicted structure of Eu–IL–Ti hybrids, for Ln–IL–Al and Ln–IL–Zr hybrids, they show the similar composition except for titania is replaced by zirconia and alumina. |
Materials | LnW10 (mol %) | τ a/ms | η b/% |
---|---|---|---|
a The error for decay time is ±10%. b The error for quantum yield is ±10%. | |||
Eu–IL–Al | 9.5 | 2.93 | 96 |
Eu–IL–Ti | 3.1 | 2.30 | 11 |
Eu–IL–Zr | 8.5 | 2.84 | 89 |
Tb–IL–Al | 8.8 | 0.84 | 13 |
Tb–IL–Ti | 2.6 | 0.70 | 1.1 |
Tb–IL–Zr | 7.0 | 0.81 | 4.5 |
Sm–IL–Al | 8.3 | 0.091 | 10 |
Sm–IL–Ti | 2.2 | 0.082 | 0.61 |
Sm–IL–Zr | 7.0 | 0.090 | 6.3 |
Dy–IL–Al | 9.0 | 0.083 | 47 |
Dy–IL–Ti | 2.9 | 0.059 | 1.3 |
Dy–IL–Zr | 8.5 | 0.076 | 35 |
Fig. 2 shows the FT-IR information of the 1-methyl-3-propionyloxy imidazolium bromide (IM+Br−) and four obtained luminescent materials Ln (Eu, Tb, Sm, Dy)–IL–Al. As shown in Fig. 2(a), the vibration bands centered about 3100 cm−1 can be reckoned as the C–H stretching vibration of the ring and of the aliphatic chain. The peaks whose absorption bands locating at 1633, 1570, 1455 cm−1 are ascribed to ring stretching of the imidazolium ring. The bands corresponding to the v(C–O, CO) for COOH of IM+Br− are situated at 1168 and 1730 cm−1 respectively.21,23 However, in Fig. 2(b) these two bands disappear and 1636, 1558 cm−1 are observed in these twelve materials which can be assigned to the asymmetric stretching vibration of carboxylate group. The result is caused by the coordination reaction between –COOH group grafted on the ionic liquid and metal alkoxides. The same phenomena are observed in the FTIR spectra (shown in Fig. S1†) of other eight hybrid materials of zirconia (alumina, titania) xerogels. This indicates the formation of chelating bonds between the carboxyl group of the ionic liquid IM+Br− and metal oxide networkds of zirconium, titanium and aluminum ions.
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Fig. 2 The Fourier transform infrared spectra of 1-methyl-3-propionyloxy imidazolium bromide (IM+Br−) (a) and selected Ln–IL–Al hybrid xerogels (Ln = Eu, Tb, Sm, Dy) (b). |
The representative XRD patterns for the samples are shown in Fig. 3. As displayed from the XRD pattern (Fig. 3a), the samples Eu–IL–Al, Tb–IL–Al, Sm–IL–Al, Dy–IL–Al exhibits four broad diffraction peaks with low intensity, suggesting that amorphous Al2O3 phase was formed. Fig. 3(b) depicts the wide angle X-ray diffraction patterns of four lanthanide polyoxometalates hybrids based on the matrix of zirconia. The previous works done by Zhang et al.24 pointed out that the transition temperature of ZrO2 from amorphous to tetragonal phase begin above 400 °C. The annealed ZrO2 powder will show obvious peaks at 2θ = 30.2, 50.3 and 60.2° which can be assigned to the (0 1 1), (1 1 2), (1 2 1) reflections of tetragonal ZrO2 respectively. In our work, the reaction temperature is below 100 °C and can't generate the phase of calcined tetragonal ZrO2. The uncalcined matrix ZrO2 still demonstrates a weak broad peak centered at 30°, which indicate the homogenous amorphous phase of ZrO2. The results are consistent with that of Eu–IL–Ti, Tb–IL–Ti, Sm–IL–Ti and Dy–IL–Ti (shown in Fig. S2†). The lack of crystalline peaks in these obtained samples indicates the presence of organic chains in the inorganic framework and suggests that no free lanthanide polyoxometalates salts exist.
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Fig. 3 The wide angle X-ray diffraction patterns of hybrid xerogels Ln–IL–Al (a) and Ln–IL–Zr (b) (Ln = Eu, Tb, Sm, Dy). |
To investigate the thermal stabilities of the obtained materials, the thermogravimetric (TG) and differential thermogravimetry (DTG) are measured. Fig. 4(a) and (b) present the TG–DTG curves of Eu–IL–Al and Eu–IL–Ti hybrid xerogels, respectively. The TG curves of Eu–IL–Zr are shown in Fig. S3.† In Fig. 4(a), the selected TG curve of Eu–IL–Al hybrids is shown and three main distinct thermal weight loss processes are pointed out. The first weight loss (about 8.7%) from 30 to 230.5 °C is attributed to the evaporation of absorbed water and residual organics from the preparation.18 The second weight loss of 10.8% in the temperature range of 230–439.7 °C is ascribed to the decomposition of 1-methyl-3-propionyloxy imidazolium skeleton, with the destruction of chemical bonds.25 At last, the slowest weight loss of 7.9% from 439.7 to 1000 °C is corresponding to the degradation of remaining organic groups, and the final residues is metal oxides (Al2O3, POM). Fig. 4(b) gives the representative thermal information of Eu–IL–Ti, and includes three mass changes in the temperature range from 30–1000 °C. The first weight loss of 9.3% below 238 °C is caused by the evaporation of physically absorbed water and crystal water in POMs and residual organics during preparation. The second weight loss from 238 to 585 °C is ascribed to the decomposition of ionic liquid and some of the organic groups, at last followed by the last mass change of 5.4% above 585 °C which is caused by the burning of residual organic components. Fig. S3† shows three similar weight loss process of Eu–IL–Zr as the above two materials. The weight loss happened from 90 °C and completed at 1000 °C. The remainder of the solid is mainly ZrO2 and EuW10. From the thermal analysis data, we conclude that the thermal stability of the luminous sphere Ln-POMs is improved on a large scale by embedding in matrices of the ionic liquid and metal oxide.
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Fig. 4 The thermogravimetric and differential thermogravimetry curves of Eu–IL–Al (a) and Eu–IL–Ti (b). |
The excitation and emission spectra of the hybrid materials are shown in Fig. 5. Fig. S4(a)† depicts the excitation spectra of the parent lanthanide polyoxometalates EuW10. The excitation spectrum of EuW10 is monitored within 614 nm of the 5D0 → 7F2 transition at room temperature. The broad band centered at 325 nm is ascribed to the O → W charge transfer (CT) states.26 The charge transfer band plays an important part in the luminescence of EuW10. Excitation of LMCT brings energy transfer from [W5O18]6− to Eu3+ which lead to series of Eu3+ characteristic emission. The series of lines in the excitation spectra are caused by the intra-4f6 transitions and the characteristic peaks of Eu3+ situate at 362 (7F0 → 5D4), 374 (7F0 → 5G4), 381 (7F0 → 5G3), 384 (7F0 → 5G2) and 394 (7F0 → 5L6), respectively.27 The 7F0 → 5L6 transition at 394 nm and 7F0 → 5D2 transition at 465 nm are the strongest intensity of excitation bands. This indicates that intra 4f6 lines show higher intensity than intensity of the LMCT states. Thus, for this compound of EuW10, direct excitation into the Eu3+ levels is comparable to the sensitization process via the LMCT states. Other excitation spectra of TbW10, SmW10, DyW10 are shown in Fig. S4(b) and S5(a) and (b)† resemble that of EuW10, also displaying broad peaks centered at 325 nm in 250–350 nm region and series of lanthanide inner electron transitions. The differences exist in the relative intensity about LMCT states and characteristic excitation lines of lanthanide ions. In EuW10, TbW10, the intensity of characteristic excitation lines of lanthanide ions is stronger than LMCT states, whereas comparisons of the relative intensity of the latter two polyoxometalates are opposite. The reason may be due to that Eu/Tb ions belong to a pair of conjugate elements on the both sides of Gd while Sm/Dy ions are another pair of conjugate elements. In the tungstate matrix, conjugate elements with the similar inner electron configuration present analogous luminescent behaviors.
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Fig. 5 The excitation and emission spectra of Eu–IL–M (a) and Tb–IL–M (b) (M = Ti, Zr, Al) hybrid xerogels. |
Fig. S4 and S5† also show the information of emission spectra of four parent lanthanide polyoxometalates LnW10, (Ln = Eu, Tb, Sm, Dy). In the emission spectra of EuW10 (Fig. S4(a)†), there are four main sharp emission bands from 550 to 750 nm which exhibit the characteristic transitions of Eu3+ ions and they are attributed to 5D0 → 7F1 (589 nm), 5D0 → 7F2 (615 nm), 5D0 → 7F3 (652 nm), 5D0 → 7F4 (700 nm) respectively. As is known, red luminescence of 5D0 → 7F2 is assigned to the electric-dipole transition which is closely related with the europium coordination environment, and the orange luminescence of 5D0 → 7F1 transition is ascribed to magnetic-dipole type, which is independent of the surrounding coordination environment. The ratio (R/O) of relative intensity of 5D0→7F2 transition to 5D0 → 7F1 transition is the criterion to measure the symmetry of the europium coordination environment. The larger the value of R/O indicates the lower symmetry of europium site, demonstrating the stronger intensity of red luminescence in the whole material. Seen in the emission spectra of EuW10, the intensity of 5D0 → 7F2 transition is weaker than that of 5D0 → 7F1 transition, suggesting europium is located at a higher symmetry in the coordination environment. The reasons are reckoned as europium is coordinated by two [W5O18]6− segments, so the metal ions are completely hidden from interactions with solvent molecules.26a The introduction of tungstate changes the lanthanide ion local symmetry which brings different appealing properties and important modifications in the surroundings of Eu3+. The research of Ballardini and his coworkers discloses the photophysical properties of EuW10O369− and makes a conclusion that EuW10O369− is of D4d symmetry, in which Eu3+ is at a rather high symmetric site.28 Compared to the emission spectra of pure lanthanide salts, another difference can be observed from the spectra of parent lanthanide polyoxometalates. 5D0 → 7F4 transition is abnormally high compared with the ordinary hybrids doping europium nitrate. These abnormal phenomena are analyzed by Ferreira et al.26a In their research, the analysis about the abnormal 5D0 → 7F4 intensity as the consequence of the behavior of the Ωλ intensity parameters (calculated by γtP (ligand field parameters) and ΓtP (ligand polarizability-dependent term)) is valuable.
Other lanthanide polyoxometalates possess similar structures and their excitation spectra are alike. Their emission spectra are lanthanide ion typical emission without much discrepancy. In emission spectrum of TbW10 (Fig. S4(b)†), four sharp peaks in the range of 450–700 nm are due to f–f* transitions of Tb3+ and are ascribed to 5D4 → 7FJ (J = 6–3) transitions at about 489, 544, 582 and 621 nm respectively. Among these emission peaks, the prominent green luminescence 5D4 → 7F5 was observed in their emission spectra. The characteristic narrow emission bands of SmW10 in 550–750 nm range are clearly observed in Fig. S5(a). But the peaks split into some parallel shoulder peaks which centered about 567 (560), 607 (597), 652 (645), 702 nm. They are assigned to 4G5/2 → 6HJ (J = 5/2, 7/2, 9/2, 11/2) respectively. Among these peaks, the orange luminescence 4G5/2 → 6H7/2 is the strongest. Fig. S5(b)† shows the emission spectrum of DyW10. The typical transition of dysprosium is seen splitting at 479 (489) and 573 (585) nm which represent 7F9/2 → 6H15/2 (479 nm, blue luminescence) and 7F9/2 → 6H13/2 (573 nm, yellow luminescence) correspondingly. The blue emission is more efficient than the yellow emission by comparing their relative intensities.
Photoluminescence comparisons of polyoxometalates encapsulated hybrids in different inorganic matrices are discussed below. Fig. 5(a) shows the luminescence spectra of europium hybrid xerogels Eu–IL–Al, Eu–IL–Zr, Eu–IL–Ti. The excitation spectra of these three hybrids are obtained by monitoring the strongest emission band of the Eu3+ ion at 590 nm, also with large broad band ranging from 250–350 nm and in 350–500 nm range following the typical intra-4f6 lines of Eu3+ serial transitions. In the excitation spectra, the broad band is ascribed to the O → W charge transfer of the tungstate affected by ionic liquid and inorganic matrices. The center of broad band in Eu–IL–Al, Eu–IL–Zr, Eu–IL–Ti blue-shift to about 300 nm from the central 325 nm of the parent EuW10, and hybrids Eu–IL–Ti shifts farthest. And the excitation spectrum of Eu–IL–Ti showing characteristic peaks of Eu3+ is much stronger than the LMCT band. The differences of excitation spectra are probably caused by different environments around EuW10. In Fig. 5(a), the emission spectra of Eu–IL–Al, Eu–IL–Zr, and Eu–IL–Ti are obtained by monitoring their maximum excitation wavelength. The relative intensity of Eu–IL–Ti is expanded 10 times to match that of Eu–IL–Al, Eu–IL–Zr. The R/O of three EuW10-assembled hybrids Eu–IL–Al, Eu–IL–Zr, Eu–IL–Ti are 0.73, 1.04, 1.21 respectively compared with 0.68 of EuW10. This indicates the chemical environment of Eu3+ is affected to some degree and the red luminescence is changed by inorganic host through the IL linkage. The interaction between EuW10 and ionic liquid functionalized matrix probably has influence on EuW10 through the static electronic force. From the above discussion, it is found that zirconia and alumina matrices are more suitable matrices for the luminescence of EuW10 than titania. This is not only depends on the encapsulating content (as shown in Table 1 for mol% EuW10 in hybrids) of EuW10 but also is related to the different chemical environment of inorganic xerogels.
Fig. 5(b) is the photoluminescence spectra of terbium hybrid xerogels Tb–IL–Al, Tb–IL–Zr, Tb–IL–Ti. Their emission spectra are all excited by the maximum excitation wavelength of broad band O → W ligands–metal charge transfer transition and show Tb3+ characteristic emission peaks. The blue luminescence at 484–495 nm is ascribed to 5D4 → 7F6 transition and the most prominent peaks 545 nm is due to 5D4 → 7F5 transition. Two tiny peaks in the orange and red luminescence region at 583 nm and 621 nm are assigned to 5D4 → 7F4, 5D4 → 7F3 transition respectively. The relative intensity of both excitation and emission spectra of zirconia hosts are more intense than that of alumina and titania. This demonstrates zirconia is a more suitable matrix for TbW10 than alumina and titania. This is both related to the encapsulating content (as shown in Table 1 for mol% TbW10 in hybrids) of TbW10 but also is related to the different chemical environment of inorganic xerogels.
We investigated the photoluminescence property of hybrid xerogels Sm–IL–Al, Sm–IL–Zr and Sm–IL–Ti. Fig. 6(a) shows their excitation spectra which are monitored at 597 nm and their emission spectra are measured by the excitation of LMCT at room temperature. All emission spectra show three bands of emission transitions as the result of the introduction of tungstate. Tungstate leads to the split of 4G5/2 → 6H5/2, 4G5/2 → 6H7/2, 4G5/2 → 6H9/2 transitions. The transition 4G5/2 → 6H5/2 at 570 nm divide from 561 to 570 nm, another transition 4G5/2 → 6H7/2 at 608 nm split from 597 nm to 608 nm and the last observed transition 4G5/2 → 6H9/2 at 653 nm break into emission region from 644 nm to 654 nm. This suggests the [W5O18]6− segment, IM+Br−, inorganic matrix have an important influence on width, position and shapes of the peaks. Among three emission bands, the transition 4G5/2 → 6H7/2 is of the highest intensity. These hybrid xerogels of SmW10 are weaker than other lanthanide system, which is due to the luminescence nature of Sm3+ itself. Because of the existence of internal energy level (6F11/2, 6F9/2, …6H11/2etc.) between the first excited state 4G5/2 and ground state 6H9/2 of Sm3+, the non-radiative energy transfer process takes place easily to loss the excited energy.
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Fig. 6 The excitation and emission spectra of Sm–IL–M (a) and Dy–IL–M (b) (M = Ti, Zr, Al) hybrid xerogels. |
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Fig. 7 The CIE chromaticity diagrams of lanthanide polyoxometalates and their twelve hybrid xerogels. |
The luminescence features of alumina, zirconia, and titania xerogels incorporating DyW10 are presented in Fig. 6(b). The excitation spectra are obtained by monitoring the 7F9/2 → 6H15/2 transition at 484 nm. In the excitation spectra of Dy–IL–Ti, the relative intensity of characteristic excitation lines of the Dy3+ f–f transitions is more intense than the O → W ligands–metal charge transfer transition. Whereas in excitation spectra of Dy–IL–Al, Dy–IL–Zr, the broad band of O → W ligands–metal charge transfer transition contributes more than lanthanide characteristic excitation lines, showing high intensity of the LMCT. Comparison about the intensities of excitation spectra suggests that zirconia is more advantageous in sensitizing the luminescence of DyW10 and in the longer wavelength region of Dy–IL–Zr, a broad band appears instead of lanthanide narrow excitation peaks in this region, which is not observed in pure DyW10. The appearance of such broad band around 390 nm may be probably related to a superposition with host broad emission. Their emission spectra assemble the characteristic emission of DyW10 in positions, shapes, width, with division peaks of 7F9/2 → 6H15/2, 7F9/2 → 6H13/2 transitions in the range of 479–489 nm, 573–585 nm, correspondingly. The blue luminescence is stronger than the yellow luminescence. The Y/B values (Y and B stand for the integrated intensities of the 7F9/2 → 6H15/2, 7F9/2 → 6H13/2 transitions) of Dy–IL–Al, Dy–IL–Zr, and Dy–IL–Ti are 0.76, 0.73 and 0.87 respectively, and the calculated Y/B value of parent DyW10 is 0.73. As is known, 7F9/2 → 6H13/2 transition is hypersensitive and changes with the influence of the external surrounding environments (alumina, zirconia and titania), resulting in the change of emission intensity ratio among emission spectra of three DyW10-incorporating hybrids. This is not only depends on the encapsulating content (as shown in Table 1 for mol % EuW10 in hybrids) of EuW10 but also is related to the different chemical environment of inorganic xerogels.
Comparisons of fluorescence lifetimes and quantum yield about poloxometalates-incorporating alumina, zirconia and titania: to further investigate the influence of different inorganic host matrix on the luminescence properties of polyoxometalates, the typical decay curves of obtained hybrids are measured at room temperature. The decay times of excited states 5D0 (EuW10), 5D4 (TbW10), 4G5/2 (SmW10), 7F9/2 (DyW10) are measured on the basis of emission decay curves monitored with the more intense Eu3+ (5D0 → 7F1), Tb3+ (5D4 → 7F5), Sm3+ (4G5/2 → 6H7/2), Dy3+ (7F9/2 → 6H15/2) transitions, under the excitation at their maximum excitation wavelength, respectively. The luminescence decay time of EuW10-incorporating hybrids follows a single exponential function in the formula ln[S(t)/S0] = −k1τ = −t/τ, indicating that only one sort of Eu3+ center exist in these hybrids and Eu3+ occupies the same average coordination environment (see Table 1).29 Other obtained materials present similar properties.
The lifetimes of EuW10-incorporating alumina, zirconia, and titania can reach to millisecond time scale which is above 2 ms. At the same time, hybrids Eu–IL–Al, Eu–IL–Zr display longer decay lifetime than the Eu–IL–Ti, which is consistent with the analysis results of their emission spectra. Decay lifetime values of Tb–IL–Al, Tb–IL–Zr, and Tb–IL–Ti are 0.84 ms, 0.81 ms, 0.704 ms correspondingly. The values are lower than these inorganic host matrices encapsulating EuW10. The lifetime values of Sm–IL–Al, Sm–IL–Zr, Sm–IL–Ti, Dy–IL–Al, Dy–IL–Zr, and Dy–IL–Ti are 91, 90, 82, 83, 76, and 59 μs, respectively, far below the lifetime of EuW10 hybrids.
Moreover, the absolute luminescence quantum yield data are obtained with an integrating sphere and a calibrated detector setup for solid materials. The resulting absolute luminescence quantum yields are listed in Table 1. In parent lanthanide polyoxometalates, η of EuW10 is 45%. However, for Eu-IL–Ti, the quantum yield (η) of 5D0 emitting level is 10.7%. When EuW10 is encapsulated into matrices of alumina and zirconia, the values of η have increased significantly which can approach to 96%, 89% correspondingly. Considering the measurement error, these value are matchable to the parent EuW10 compound at the least, here we consider it may due to that the ionic liquid functionalized alumina and zirconia affect the chemical environment of EuW10, even Eu3+ ion, which further decreases the non-radiative energy loss to be benefit for the luminescence of Eu3+.
For TbW10-incorporating hybrids, the η value (1.1%) of Tb–IL–Ti is the smallest, less than that (4.5%) of Tb–IL–Zr and the η value (13%) of Tb–IL–Al presents the maximum. The η value of TbW10 is 5.9%, so by comparison, only when TbW10 is assembled in alumina, the quantum yield can be effectively improved. In SmW10 assembled hybrid system, it seems the overall quantum yield is not high. The pure lanthanide polyoxometalates SmW10 shows 3.1% quantum yield. The quantum yield η of Sm–IL–Al, Sm–IL–Zr, and Sm–IL–Ti are 10%, 6.3% and 0.61% respectively. Through the analysis of these data, we can presume zirconia and alumina is superior host matrices to titania for incorporating SmW10. The quantum yield η of Dy–IL–Al, Dy–IL–Zr, Dy–IL–Ti are 47%, 35, %, 1.3% comparing with the value 17% of parent lanthanide polyoxometalates DyW10. On the basis of the above discussion about these polyoxometalates assembled hybrids, we may conclude that the modifications with the alumina and zirconia matrix are beneficial for the luminescent performances of lanthanide polyoxometalates.
Furthermore, the CIE chromaticity diagrams of polyoxometalates, the derived hybrids are shown in Fig. 7 and their CIE coordinates are listed in Table S1.† Among the obtained materials, Eu–IL–Ti, Tb–IL–Zr, Tb–IL–Ti, Dy–IL–Ti, Dy–IL–Zr, Dy–IL–Al locate at warm white light regions, displaying favorable luminescent performance for practical applications.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: 10.1039/c3ra45281f |
This journal is © The Royal Society of Chemistry 2014 |