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Communication

CdTe Quantum Dot Fluorescence Modulation by Spin Crossover

by
Olena Kraieva
1,†,
Iurii Suleimanov
1,2,†,
Gábor Molnár
1,†,
Lionel Salmon
1,* and
Azzedine Bousseksou
1,*
1
Laboratoire de Chimie de Coordination, CNRS 205 Route de Narbonne, Toulouse 31077, France
2
Department of Chemistry, National Taras Shevchenko University, 62a Volodymyrska street, Kyiv 01601, Ukraine
*
Authors to whom correspondence should be addressed.
†
These authors contributed equally to this work.
Magnetochemistry 2016, 2(1), 11; https://doi.org/10.3390/magnetochemistry2010011
Submission received: 10 November 2015 / Revised: 27 January 2016 / Accepted: 4 February 2016 / Published: 25 February 2016
(This article belongs to the Special Issue Spin Crossover (SCO) Research)
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Abstract

:
Nanocomposite materials containing Cadmium Telluride (CdTe) nanocrystals and [Fe(H-trz)2(trz)]BF4 nanoparticles were synthesized and investigated for the coupling between their photoluminescent and spin crossover properties. The bright CdTe emission around 550 nm was found to decrease reversibly when switching the ferrous complex from the high spin (HS) to the low spin (LS) state, which was attributed to the spectral overlap of the luminescence with the absorption of the complex in the latter electronic configuration. A significant irreversible change of the luminescence signal (photobleaching) was also observed both in emission intensity and lifetime measurements.

Graphical Abstract

1. Introduction

Recently, a series of hybrid or nanocomposite materials combining fluorescent and spin crossover (SCO) properties have been described in the literature [1,2,3,4,5,6,7,8,9,10,11,12,13,14,15,16,17,18,19,20,21,22,23,24,25,26,27,28]. The main appeal of these hybrid materials is related to the fact that—for an appropriate combination of the two constituents—the fluorescence intensity can be a sensitive probe of the spin-state of the system. There is also a fundamental interest in studying energy transfer mechanisms between fluorophores and transition metal complexes in their different spin states. In most cases, the luminescence intensity variation in response to the spin state switching was attributed to an efficient spectral overlap between the fluorophore emission and the absorption of the SCO complex in a given spin state, leading to enhanced excited state energy transfer from the luminophore to the complex in that spin state, i.e., to a decrease of the luminescence intensity. Depending on the spatial proximity of the luminescent and SCO centers, this energy transfer can be either radiative or resonant, but such mechanistic aspects have been scarcely investigated [2]. In a few cases, other mechanisms of luminescence modulation by SCO, related to structural instead of electronic changes, have been also proposed [14,22].
The vast majority of the reported hybrid fluorescent SCO systems are based on organic fluorophores. However, a serious drawback of organic dyes is their rather strong photobleaching. To overcome this problem we have recently elaborated [Fe(H-trz)2(trz)]BF4@SiO2 core-shell nanoparticles (H-trz = 1,2,4-triazole and trz = 1,2,4-triazolato), which we surface grafted with a rare-earth (Tb3+) containing fluorophore [24]. This lanthanide—SCO nanocomposite demonstrated high luminescence stability, i.e., a well reproducible modulation of the luminescence intensity by the spin-state switching. In this context, semiconductor nanocrystals (“quantum dots”) are a priori also very interesting candidates because of their bright luminescence [29,30]. In addition, they exhibit a short luminescence lifetime and are usually more stable than organic dyes. The electrons in quantum dots are confined in a small space and typically when the radii of the nanocrystal is smaller than the exciton Bohr radius, the luminescence emission wavelength becomes size dependent. This property has been exploited in different applications and it is also obviously very advantageous in the context of hybrid luminescent SCO materials as one can easily “size tune” the energy levels of the luminophore in order to reach an appropriate spectral overlap with the absorption of the SCO complex. Based on these ideas, in this paper we describe nanocomposite materials, consisting of CdTe nanocrystals and [Fe(H-trz)2(trz)]BF4 SCO particles, which display a coupling between the two electronic phenomena.

2. Results and Discussion

The luminescence emission spectrum of the CdTe nanocrystals in solid state is shown in Figure 1a for selected temperatures between 298 K and 363 K. Before the measurements, the sample was annealed at 400 K to remove traces of solvents. At room temperature, the emission peak is centered at 555 nm and the peak width at half-maximum is ca. 40 nm. We observed this irreversible redshift and broadening of the emission (with respect to the as-received nanocrystals) systematically after the first heating of the sample. As it can be expected on heating, the luminescence peak exhibits a marked decrease of peak amplitude, an increase of the peak width and a small redshift. These changes were found only partially reversible (vide infra). Figure 1b shows the absorption (diffuse reflectance) spectra of the iron complex in the two spin states. While the compound is basically colorless in the HS (5T) state, its color turns pink-violet in the LS (1A) state due to the emergence of a broad absorption peak centered around 540 nm. Obviously, the spectral overlap between this metal-centered absorption and the CdTe emission is complete and one can thus expect a luminescence intensity decrease in the composites 1 and 2 when switching the complex from the HS to the LS state.
TEM images of 1 revealed rod-like nanoparticles with an average width of ca. 45 nm and a length of ca. 90 nm (Figure 2a) in agreement with the size and morphology already reported for similar syntheses [31]. For sample 2, smaller, nearly spherical and strongly aggregated nanoparticles with an average diameter of 40 nm were revealed by the TEM analysis (Figure 2b). HRTEM images and EDX analyses of the two samples indicate that the quantum dots are randomly distributed on the surface of the SCO nanoparticles in an amount of ca. 1%–2% CdTe/Fe (see Figure 2a and the Supplementary Materials Figures S1–S3).
Figure 2 shows also the normalized fluorescence intensity of the composites recorded at 550 nm as a function of the temperature over two complete heating–cooling cycles between 323 K and 403 K. For both nanocomposite samples, upon heating, the luminescence exhibits a linear decrease, which corresponds to the usual thermal quenching phenomenon due to the thermal activation of non-radiative decay channels. In addition, for both samples the thermal hysteresis associated with the spin transition is clearly discernible in the temperature dependence of the luminescence intensity. For sample 1, the LS to HS spin transition around 393 K leads to an abrupt increase of the luminescence intensity by only 0.03% (Figure 2c). In the cooling mode, the inverse process occurs, i.e., a linear increase of the luminescence intensity down to ca. 362 K followed by an abrupt drop, which corresponds to the HS to LS transition. The wide (ca. 35 K) thermal hysteresis associated with the spin transition is a well-known feature of the complex and corresponds to the magnetic measurements reported previously for the non-fluorescent nanoparticles [31]. At the end of the first thermal cycle, one can observe nearly 1% irreversible decrease of the luminescence intensity, which we attribute to a photobleaching process. Similar behavior was observed for sample 2, but, in this case, not only the first, but also the second thermal cycle, involves a ca. 2% irreversible decrease of the luminescence intensity (Figure 2d). Moreover, the LS to HS (HS to LS) spin transition is detected at 373 K (345 K) with a luminescence intensity change of ca. 5%. In comparison with sample 1, the observed shift of the hysteresis loop towards lower temperatures is probably related to the specific matrix effect of the BPEI shell [32]. On the other hand, the origin of the significant difference between the magnitudes of the luminescence modulation in the two samples remains unclear. It might be related to the particular distribution of CdTe nanocrystals within the composites even if the EDX analysis indicates rather random distributions and similar concentrations in both cases.
It is interesting to compare these curves with data previously published on analogous nanocomposite materials based on [Fe(H-trz)2(trz)]BF4@SiO2 core-shell nanoparticles and different luminophores. Titos-Padilla et al. [13,21] functionalized the silica shell with the organic fluorophore 3-(dansylamido)propyltrimethoxysilane exhibiting a broad luminescence emission centered around 490 nm at room temperature. They observed a marked luminescence intensity drop of ca. 80% when going from the HS to the LS state, which they attributed to a Förster type energy transfer process. This change was reproducible on the reverse transition, but, for each thermal cycle, an irreversible decrease of ca. 20% of the luminescence occurred as well, which was explained by the thermal decomposition of the luminophore at high temperatures (around 400 K). Interestingly, the emission peak maximum shifted also from ca. 490 nm (LS) to 500 nm (HS) upon the SCO. In our team we also grafted [Fe(H-trz)2(trz)]BF4@SiO2 particles with a pyrene-derivative fluorophore [22]. The fluorescent composites exhibited both pyrene monomer and excimer luminescence, centered around 430 and 605 nm, respectively. When switching the particles from the HS to the LS state the excimer luminescence intensity decreased by ca. 25%–45% (depending on the luminophore quantity) and the emission spectra were redshifted by ca. 15 nm, while the monomer emission exhibited negligible spin-state dependence. Variable temperature luminescence lifetime measurements revealed that the strong coupling of the pyrene excimers with the spin-state of the metal complex occurred via a non-radiative mechanism and it was suggested that the coupling was mediated primarily by the mechanical strain accompanying the SCO. Photobleaching of the luminophore was also observed. Alternatively, we also grafted a Tb3+ complex on the [Fe(H-trz)2(trz)]BF4@SiO2 particles [24]. We observed a relatively small (ca. 2%), but very well reproducible decrease of the most intense 5D4 → 7F5 transition (centered at 545 nm) accompanying the HS to LS transition. Since this intensity modulation was not accompanied by any observable change of the luminescence lifetime we proposed a radiative energy transfer mechanism via (partial) reabsorption of the emitted photons by the LS complexes. In each of these examples, the overall temperature dependence of the luminescence exhibits a very similar hysteresis when compared to that observed here for the CdTe composites highlighting thus the excellent versatility of this approach. The relatively weak variation of the luminescence intensity accompanying the SCO in the CdTe composites suggests that probably a radiative energy transfer process occurs between the luminophore and the iron complex.
We were particularly interested in the origin of the instability of the luminescence signal in the CdTe–SCO composites and we have thus investigated the concomitant effect of light exposure and temperature changes on the luminophore itself. Figure 3a presents the fluorescence intensity variation as a function of temperature through five thermal cycles between 323 K and 403 K for a fresh sample. The fluorescence intensity has dropped by ca. 65% after the first cycle, which we attribute tentatively to the desolvation effect. For every further cycle, the fluorescence was bleached to a small extent when compared to the preceding cycle. Figure 3b shows a complete thermal cycle of the luminescence signal of our quantum dots between 323 K and 403 K. Prior to this measurement, the sample was annealed at 403 K. At the end of the cycle, ca. 9% intensity loss is observed. The reasons of this luminescence bleaching are not clearly understood, although it might be caused by changes on the surface of the crystals. We have also investigated the thermal variation of the CdTe fluorescence lifetime, which is often a more robust property than the luminescence intensity. Variable temperature luminescence lifetime measurements were performed between 298 K and 373 K for a complete thermal cycle. Figure 3c shows the three-exponential fit of the raw decay data acquired at 298 K and 368 K. As expected, an important lifetime decrease is observed at higher temperature due to the thermal activation of non-radiative decay channels. The evolution of the luminescence lifetime as a function of the temperature is also plotted in Figure 3d. As the temperature increases from 298 K and 373 K, the luminescence lifetime decreases from ca. 7.1 ns to 3.1 ns. When the temperature decreases to the initial value, the lifetime recovers only to ca. 5.7 ns. This thermal instability of the lifetime may be linked to the photothermal degradation of the nanocrystal surface, which can affect the exciton lifetime. The fact that the luminescence decay must be fitted with a multi-exponential function indicates that different types of excitons contribute to the overall emission process and it is possible that the photobleaching does not affect them in the same way, leading to a change of the average lifetime as well. Similar to our results, several publications have mentioned the strong decrease of fluorescence intensity and lifetime upon the increase of the temperature (see for example References [33,34,35]). However, most of these publications have failed to notice the partial irreversibility of these changes over thermal cycles which is clearly seen in our experiments.

3. Experimental Details

[Fe(H-trz)2(trz)]BF4@SiO2 core-shell particles were synthesized as reported in Reference [31]. A similar strategy was used to synthesize [Fe(H-trz)2(trz)]BF4 particles without SiO2 shell, modifying also the reactant concentrations (in this case a two-fold molar excess ligand to iron salt was used). In a second step, these particles were covered by a branched polyethylenimine (BPEI) polymer. CdTe nanocrystals, 2 nm in diameter, coated with COOH groups, were purchased from Plasmachem (Berlin, Germany) and present luminescence emission centered at 520 ± 5 nm in aqueous solution. The SCO@SiO2 or SCO@BPEI particles (100 mg) were mixed with the fluorescent CdTe nanocrystals (0.5 mg) overnight in 10 mL ethanol/water (1:1) mixture and the resulting suspension was centrifuged affording samples [Fe(H-trz)2(trz)]BF4@SiO2@CdTe (1) and [Fe(H-trz)2(trz)]BF4@BPEI@CdTe (2). Transmission electron microscopy (TEM) images were obtained by using a JEOL JEM 1011 electron microscope (JEOL, Dearborn, MA, USA) operated at 100 kV. High resolution Transmission Electronic Microscopy (HRTEM) coupled energy-dispersive X-ray spectroscopy (EDX) analysis were carried out using high-resolution microscope JEOL JSM 2100F (JEOL, Dearborn, MA, USA) operated at 200 kV. Fluorescence microscopy images have been recorded with an Olympus BX51 upright microscope (Olympus, Tokyo, Japan) equipped with a 100 W halogen lamp, a CCD image sensor (Clara, Andor Technology, Belfast, UK) and a × 5 (NA = 0.1) or a × 50 (NA = 0.5) magnification objective. The excitation and collected light beams were separated by a dichroic mirror with a cutting edge at 510 nm and band-pass filters centered at 450 nm (FWHM = 45 nm) and at 550 nm (FWHM = 50 nm) for excitation and emission, respectively. For spectroscopic analysis we used a Shamrock SR-303i imaging spectrometer (Andor Technology, Belfast, UK), which was connected to the microscope by an optical fiber. Luminescence lifetime measurements were performed using the time-correlated single photon counting (TCSPC) technique by means of a DeltaFlex (Horiba, Kyoto, Japan) instrument equipped with a 449 nm electroluminescent diode (pulse duration 1.2 ns). Detection was performed by setting the emission monochromator to 540 nm completed with an additional bandpass filter around this wavelength. Fittings and lifetime calculations were performed using the DAS6 fluorescence decay analysis software (Horiba, Kyoto, Japan). Variable temperature experiments were carried out in ambient air at a rate of 5 Kmin−1 using a Linkam THMS600 cryostat (Linkam Scientific Instruments, Tadworth, UK).

4. Conclusions

We synthesized nanocomposite materials based on luminescent CdTe nanocrystals and [Fe(H-trz)2(trz)]BF4 nanoparticles enrobed either with SiO2 or BPEI shells. Both samples exhibited a reversible modulation of the luminescence intensity upon the spin transition. Owing to the rather week luminescence modulation we tentatively attributed this phenomenon to a radiative energy transfer mechanism between the luminophore and the spin crossover complex resulting from the spectral overlap between the luminescence emission and the absorption of the complex in the LS state. The photo-thermal degradation of the luminophore was also observed and further work should focus on solving this issue by appropriate surface modification (encapsulation) of the CdTe nanocrystals [36]. The most interesting perspective of the present work will be the detailed investigation of the relationship between the spectral overlap and the luminescence modulation. To this aim CdTe nanocrystals provide an excellent scope as their emission spectra can be tuned over a wide spectral range (ca. 500–800 nm) around the metal-centered absorption bands of our SCO complex. As a more general conclusion, it appears that by an appropriate choice of the spectral characteristics of the luminophore its emission will be inexorably modulated by the SCO phenomenon in this type of hybrid nanocomposites. The nature of the luminophore used and the way it is mixed with the SCO entities will determine ‘merely’ the magnitude of the luminescence modulation. This allows one to change the luminescent properties of the composite material (for example, the Tb3+ emission is characterized by sharp lines and long decays, while pyrene and CdTe exhibit broad emission bands and fast decays), while keeping virtually the same spin crossover properties.

Supplementary Files

Supplementary File 1

Acknowledgments

This work was performed in the frame of the International Associated Laboratory (LIA) Kiev-Toulouse. We thank the Agence National de la Recherche (project ANR-13-BS07-0020-01) and the French Embassy in Ukraine for financial support.

Author Contributions

L.S., G.M and A.B. conceived and designed the experiments; O.K. and I.S. performed the experiments; O.K. and I.S. analyzed the data; L.S. and G.M. contributed reagents/materials/analysis tools; L.S., G.M. and A.B. wrote the paper.

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. (a) Photoluminescence emission spectra of CdTe nanocrystals at a few selected temperatures (excitation at 450 nm). (b) Absorption spectra of the SCO complex in the HS and LS states (reproduced by permission of The Royal Society of Chemistry).
Figure 1. (a) Photoluminescence emission spectra of CdTe nanocrystals at a few selected temperatures (excitation at 450 nm). (b) Absorption spectra of the SCO complex in the HS and LS states (reproduced by permission of The Royal Society of Chemistry).
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Figure 2. TEM images of samples 1 (a) and 2 (b). The HRTEM image of sample 1 in inset of (a) shows the localization of the CdTe particles, identified by EDX analysis, at the surface of the SCO@SiO2 nanoparticles. Normalized luminescence intensity of samples 1 (c) and 2 (d) recorded at 550 nm (excitation at 450 nm) as a function of the temperature for two successive thermal cycles (arrows indicate cooling and heating for the first cycle).
Figure 2. TEM images of samples 1 (a) and 2 (b). The HRTEM image of sample 1 in inset of (a) shows the localization of the CdTe particles, identified by EDX analysis, at the surface of the SCO@SiO2 nanoparticles. Normalized luminescence intensity of samples 1 (c) and 2 (d) recorded at 550 nm (excitation at 450 nm) as a function of the temperature for two successive thermal cycles (arrows indicate cooling and heating for the first cycle).
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Figure 3. (a) Fluorescence intensity variation of CdTe quantum dots for 5 consecutive temperature cycles (λex = 450 nm, λem = 550 nm);(b) Temperature dependence of the luminescence intensity of CdTe through a complete heating-cooling cycle; (c) Luminescence decay curves of CdTe nanocrystals at 298 K and 368 K (λex = 449 nm, λem = 540 nm); (d) Lifetime of CdTe luminescence as a function of temperature on heating and cooling.
Figure 3. (a) Fluorescence intensity variation of CdTe quantum dots for 5 consecutive temperature cycles (λex = 450 nm, λem = 550 nm);(b) Temperature dependence of the luminescence intensity of CdTe through a complete heating-cooling cycle; (c) Luminescence decay curves of CdTe nanocrystals at 298 K and 368 K (λex = 449 nm, λem = 540 nm); (d) Lifetime of CdTe luminescence as a function of temperature on heating and cooling.
Magnetochemistry 02 00011 g003

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MDPI and ACS Style

Kraieva, O.; Suleimanov, I.; Molnár, G.; Salmon, L.; Bousseksou, A. CdTe Quantum Dot Fluorescence Modulation by Spin Crossover. Magnetochemistry 2016, 2, 11. https://doi.org/10.3390/magnetochemistry2010011

AMA Style

Kraieva O, Suleimanov I, Molnár G, Salmon L, Bousseksou A. CdTe Quantum Dot Fluorescence Modulation by Spin Crossover. Magnetochemistry. 2016; 2(1):11. https://doi.org/10.3390/magnetochemistry2010011

Chicago/Turabian Style

Kraieva, Olena, Iurii Suleimanov, Gábor Molnár, Lionel Salmon, and Azzedine Bousseksou. 2016. "CdTe Quantum Dot Fluorescence Modulation by Spin Crossover" Magnetochemistry 2, no. 1: 11. https://doi.org/10.3390/magnetochemistry2010011

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