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Silica-coated upconversion lanthanide nanoparticles: The effect of crystal design on morphology, structure and optical properties

  1. 1 ,
  2. 1 ,
  3. 1 ,
  4. 1 ,
  5. 2 ,
  6. 2 ,
  7. 2 and
  8. 1
1Institute of Macromolecular Chemistry, Academy of Sciences of the Czech Republic, Heyrovského nám. 2, 162 06 Prague 6, Czech Republic
2Institute of Physiology, Academy of Sciences of the Czech Republic, Vídeňská 1083, 142 20 Prague 4, Czech Republic
  1. Corresponding author email
Associate Editor: A. R. Khokhlov
Beilstein J. Nanotechnol. 2015, 6, 2290–2299. https://doi.org/10.3762/bjnano.6.235
Received 14 May 2015, Accepted 17 Nov 2015, Published 03 Dec 2015
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Abstract

NaYF4:Yb3+/Er3+ nanoparticles were synthesized by thermal decomposition of lanthanide trifluoroacetates using oleylamine (OM) as both solvent and surface binding ligand. The effect of reaction temperature and time on the properties of the particles was investigated. The nanoparticles were characterized by transmission electron microscopy (TEM), electron diffraction (ED), energy dispersive spectroscopy (EDX), dynamic light scattering (DLS), thermogravimetric analysis (TGA), elemental analysis and X-ray diffraction (XRD) to determine morphology, size, polydispersity, crystal structure and elemental composition of the nanocrystals. TEM microscopy revealed that the morphology of the nanoparticles could be fine-tuned by modifying of the synthetic conditions. A cubic-to-hexagonal phase transition of the NaYF4:Yb3+/Er3+ nanoparticles at temperatures above 300 °C was confirmed by both ED and XRD. Upconversion luminescence under excitation at 980 nm was observed in the luminescence spectra of OM–NaYF4:Yb3+/Er3+ nanoparticles. Finally, the OM–NaYF4:Yb3+/Er3+ nanoparticles were coated with a silica shell to enable further functionalization and increase biocompatibility and stability in aqueous media, preventing particle aggregation.

Keywords: lanthanide; nanoparticles; oleylamine; silica; upconversion

Introduction

Due to their unique physicochemical properties, nanometer-scale materials are finding widespread applications as drug delivery systems in the diagnosis and treatment of various diseases [1,2]. Recently, upconversion nanoparticles have shown promise as optical materials [3] and a number of reviews [4-6] have described their applications in drug and gene delivery [7], cell labeling and tracking [8], bioimaging [9] and photodynamic therapy [10]. Lanthanide-doped upconversion nanoparticles emit visible light upon excitation by near-IR light (NIR). Compared with organic dyes and semiconductor quantum dots, upconversion nanoparticles have attractive chemical and optical properties, as well as low toxicity [11], sharp emission bandwidths, large anti-Stokes shifts [12] and high resistance to photobleaching and photoblinking [13]. NIR light can non-invasively penetrate living organisms deeply because the excitation wavelength is within the optical transparency window of tissues (700–1000 nm) [14]. Upconversion proceeds by different mechanisms, such as energy transfer and excited-state absorption and photon avalanche. These three mechanisms are based on the sequential absorption of two or more photons. Upconversion emission proceeds by sequential absorption of two photons and leads to population of a highly excited state. If the activator sequentially obtains energy from the sensitizer, it reaches the excited state and emits light at a short wavelength [15]. In the NaYF4-based particles, the Yb3+ sensitizer is often used to absorb photons at 980 nm, providing an excited state from which energy is transferred to a neighboring activator (e.g., Er3+). Hexagonal β-NaYF4 crystals sensitized by Yb3+ and activated by Er3+/Tm3+ ions are a highly efficient host material for green and blue upconversion [16-18].

There are many techniques to synthesize small-sized high-quality upconversion particles. The most widely used of these, wet-chemical methods, involve thermal decomposition of rare earth organic acid precursors, typically metal trifluoroacetates, acetylacetonates, oleates or acetates, in non-aqueous media in the presence of surfactants and at high temperatures [19]. In addition to their effect on reaction temperature and time, the advantages of trifluoroacetates include the rapid formation of reactive fluoride compounds and the ability to control morphology, shape, crystal phase and size depending on the ratios of the starting reagents (i.e., organic precursors, surfactants and solvents) [20]. The surfactants, e.g., oleylamine (OM) and oleic acid, typically consist of polar capping groups and long hydrocarbon chains. Other synthetic methods include the hydro(solvo)thermal technique, which involves mixing lanthanide and fluoride salts (e.g., NH4F) in a high-boiling point solvent (e.g., ethylene glycol) at high temperature and pressure [21,22].

Upconversion particles are typically prepared in different morphologies, sizes and shapes with high surface areas to efficiently conjugate target ligands and drugs [23]. It is important to tailor the surface of the nanoparticles to the specific application. Thus, various ligands and functionalities have to be attached to the particle surface to provide efficient drug delivery, to ensure engulfment by the cells, or to control the release of biomolecules and their specific target. Finally, the surface modification must ensure that the particles can be dispersed in the aqueous biological media. Charged or polar moieties, such as amphiphilic (co)polymers [24], lipids [25] and silica [26], are therefore attached to the particle surface. The silica coating imparts many useful properties to the nanoparticles, including additional functionalization and biocompatibility [27].

We herein report the preparation of OM–NaYF4:Yb3+/Er3+ nanoparticles with controlled morphology, size, composition, phase and luminescence. Thorough particle characterization was performed to elucidate the relationship between synthetic conditions and particle structure. Surface modification of the particles using silica precursors enhanced colloidal stability and facilitated the transfer of the crystals in aqueous media.

Experimental

Materials

Sodium and yttrium(III) trifluoroacetate, ytterbium(III) chloride hexahydrate, erbium(III) chloride hexahydrate, oleylamine (OM), tetramethoxysilicate (TMOS; > 99%) and Igepal CO-520 (polyoxyethylene(5) nonylphenyl ether) were purchased from Sigma-Aldrich (St. Louis, MO, USA). Ytterbium(III) oxide was prepared by dissolving ytterbium(III) chloride hexahydrate (1 g) in water (10 mL) followed by the addition of 25% NH4OH (1.2 mL). Erbium(III) oxide was prepared analogously from the respective chloride (0.5 g) dissolved in water (5 mL), which was followed by the addition of 25% NH4OH (0.6 mL). The resulting ytterbium(III) oxide was washed with water to remove ammonium chloride, and trifluoroacetic acid (0.58 ml) was added to reach pH 1. Water was removed on a rotary evaporator, and the resulting ytterbium(III) trifluoroacetate was dried in a desiccator for 24 h. Erbium(III) trifluoroacetate was obtained similarly with the only difference being the addition of 0.29 mL of trifluoroacetic acid. All other chemicals employed in this study were obtained from Lachema (Brno, Czech Republic). Ultrapure Q-water ultrafiltered on a Milli-Q Gradient A10 system (Millipore, Molsheim, France) was employed in all experiments.

Synthesis of OM-stabilized upconversion nanoparticles

Synthesis of the upconversion nanoparticles was similar to a previously reported protocol [20] with slight modifications. To prepare the hexagonal NaYF4:20%Yb/2%Er particles, a mixture of CF3COONa (2 mmol), (CF3COO)3Y (0.78 mmol), (CF3COO)3Yb (0.2 mmol) and (CF3COO)3Er (0.02 mmol) was dissolved in OM (10 mL) in a 100 mL three-neck round-bottom flask and heated to 120 °C under vigorous magnetic stirring to remove water. Heating then continued at a predetermined temperature (e.g., 330 °C) for a given amount of time (0.5–4 h) under argon to prevent oxidation. The resulting transparent yellowish reaction mixture was cooled and ethanol (20 mL) was added. The OM–NaYF4:Yb3+/Er3+ nanoparticles were separated by centrifugation, washed three times with hexane and deionized water and transferred in hexane.

Synthesis of silica-coated upconversion nanoparticles

The surfaces of the OM–NaYF4:Yb3+/Er3+ nanoparticles were coated with silica using a reverse microemulsion method [28] with slight modifications. The OM–NaYF4:Yb3+/Er3+ nanoparticles (50 mg) were dispersed in cyclohexane (10 mL). Igepal CO-520 (0.5 mL) and 25% aqueous ammonia (0.08 mL) were added, and the suspension was mixed using a Sonopuls sonicator (Bandelin, Berlin, Germany) for 30 min, yielding a stable colloid. TMOS (0.04 mL) was then added, and the mixture was stirred (600 rpm) at room temperature for 2 days. The resulting NaYF4:Yb3+/Er3+&SiO2 nanoparticles were precipitated by the addition of acetone (10 mL), separated by centrifugation and washed five times with ethanol and ethanol/water (1:1 v/v) to remove the surfactant.

Characterization of the nanoparticles

The nanoparticles were visualized and analyzed on a Tecnai G2 Spirit Twin transmission electron microscope (TEM; FEI; Brno, Czech Republic) equipped with an energy dispersive spectrometer (EDX; Mahwah, NJ, USA). Bright field TEM imaging (BF), electron diffraction (ED) and energy dispersive spectroscopy (EDX) were used to determine the morphology, crystal structure and elemental composition of the nanocrystals, respectively. All TEM micrographs, diffractograms and spectra were taken at an accelerating voltage of 120 kV. Particle size distribution was analyzed with the Atlas software (Tescan Digital Microscopy; Brno, Czech Republic). The number-average diameter (Dn) and weight-average diameter (Dw) and uniformity (polydispersity index PDI = Dw/Dn) were calculated from at least 500 individual particles. Dn and Dw can be expressed as follows:

[2190-4286-6-235-i1]
(1)
[2190-4286-6-235-i2]
(2)

where ni and Di are the number and diameter of the particles, respectively. The ED patterns were processed with ProcessDiffraction software [29] and compared with the diffraction patterns of known NaYF4 crystal structures calculated with PowderCell software [30] or downloaded from crystallographic databases.

The hydrodynamic particle size (Dh) was measured using dynamic light scattering (DLS) on a ZEN 3600 Zetasizer Nano Instrument (Malvern Instruments; Malvern, UK) at pH 1. Thermogravimetric analysis (TGA) was performed in air using a Perkin Elmer TGA 7 analyzer (Norwalk, CT, USA) from 30 to 850 °C at a heating rate of 10 °C·min−1. Elemental analysis was determined on a Perkin-Elmer 2400 CHN apparatus.

X-ray diffraction (XRD) was measured on a Rigaku MolMet (Molecular Metrology System) instrument (Tokyo, Japan) using a pinhole camera attached to a microfocused Osmic MicroMax 002 X-ray beam generator operating at 45 kV and 0.66 mA (30 W). The camera was equipped with a removable imaging plate 23 × 25 cm (Fujifilm). The experimental setup covered a momentum transfer (q) range of 0.25–3.5 Å−1, where q = (4π/λ)sinθ, wavelength λ = 1.54 Å and 2θ was the scattering angle. The center and sample-to-detector distance were calibrated using Si powder. The samples were measured in a transmission mode. Crystallinities (Cr) were estimated using integral intensities (sum of areas) diffracted by crystalline (Ic) and amorphous (Ia) phases according to Equation 3:

[2190-4286-6-235-i3]
(3)

The crystal size was calculated [31] according to the Scherrer Equation 4:

[2190-4286-6-235-i4]
(4)

where K is the shape factor (typically 0.9), β is the full width of half maximum (FWHM) of reflection (in radians) and λ is the wavelength of the X-rays (1.54 Å).

Infrared spectra were obtained on a Nexus Nicolet 870 FTIR spectrometer (Thermo Fisher Scientific; Waltham, MA, USA) equipped with a liquid nitrogen-cooled mercury cadmium telluride (MCT) detector using a Golden Gate single reflection ATR cell (Specac; Slough, UK). Spectra (256 scans) were acquired at room temperature at a resolution of 4 cm−1. Water vapor (atmospheric spectrum) and background were subtracted from the spectra, and an ATR correction was applied.

Upconversion luminescence spectra were recorded on a Leica TCS SP2 AOBS confocal inverted fluorescent microscope (Leica Microsystems; Mannheim, Germany) using a PL APO 100×/1.40–0.70 oil immersion objective (a pinhole 1 Airy unit) and a Chameleon laser Ultra Ti:sapphire laser (Coherent; Santa Clara, CA, USA) at 980 nm excitation. The nanoparticle (0.01 g) dispersion in hexane was placed on a cover glass using a spin coating technique.

Results and Discussion

To prepare NaYF4:Yb3+/Er3+ nanoparticles with a hexagonal unit cell, lanthanide trifluoroacetates were decomposed in OM, serving as both solvent and surface binding ligand [20]. Because the particle size plays a key role in biomedical applications, e.g., for internalization of nanoparticles by cells of the reticuloendothelial system [32], the effects of both reaction temperature and time were investigated to control morphology, particle size and crystallinity.

Effect of reaction temperature

In the first series of experiments, reaction temperature was varied from 250 to 350 °C, while the other reaction parameters, such as the composition NaYF4:20%Yb3+/2%Er3+, the concentration of sodium and lanthanide trifluoroacetates in OM (8.8 wt %) and the reaction time (1 h), were held constant. The selected composition of rare-earth ions produced highly efficient IR-to-visible upconversion [20]. As illustrated in the TEM/BF micrographs (Figure 1), the particles were well separated, suggesting that the long OM chains on the particle surface effectively prevented aggregation. The particles had regular spherical shapes with sizes (Dn) in the range of 6–10 nm (Table 1). The particle size increased as the temperature increased up to 350 °C, which is close to the OM boiling point. Particle size distribution was relatively narrow, as documented by the polydispersity index (PDI) ranging from 1.07 to 1.30. Nearly monodispersed particles (PDI = 1.07), which are supposed to possess uniform physical, chemical and biological properties, were obtained at 350 °C. Small size (about 10 nm) and narrow size distribution are important for particles to be considered as probes of target proteins, oligonucleotides and other biomolecules in cells and tissues. DLS experiments showed that the average hydrodynamic particle size in water was large (Dh = 163–265 nm), suggesting the formation of particle aggregates. DLS provides the z-average of the particle size, which is substantially larger than the number-average diameter determined by TEM. For example, the hydrodynamic diameter of the no. 4 OM-NaYF4:Yb3+/Er3+ nanoparticles (Table 1) was 135–240 nm, with the most frequent fraction between 150–200 nm (Figure 2). The large difference between the number-average diameter (TEM) and the hydrodynamic diameter (DLS) is due to the fact that hydrophobic particles tend to aggregate and cannot be resolved as individual particles by DLS.

[2190-4286-6-235-1]

Figure 1: TEM micrographs of OM-NaYF4:Yb3+/Er3+ nanoparticles prepared at (a) 250, (b) 300 and (c) 350 °C for 1 h.

Table 1: Effect of reaction temperature on OM–NaYF4:Yb3+/Er3+ nanoparticles prepared for 1 h.

no. T (°C) Dn (nm) PDI Dh (nm) PI L(cubic) (nm) L(hex) (nm) crystallinity (wt %) C (wt %) N (wt %) coating (wt %) I545/I660
C N TGA
1 250 6 1.28 237 0.43 8.8 12.1 76 3.87 0.24 4.8 4.6 8.7 1.93
2 280 8 1.21 265 0.43 9.7 14.0 77 2.60 0.13 3.2 2.5 5.2 2.50
3 300 9 1.16 199 0.35 6.4 17.2 67 4.20 0.30 5.2 5.9 11.1 1.83
4 330 10 1.30 188 0.27 6.4 18.6 74 3.00 0.15 3.7 2.9 7.1 1.79
5 350 9 1.07 163 0.24 – 21.3 71 18.89 2.42 23.4 21 35.2 1.68

Dn: number-average diameter (TEM); PDI: polydispersity index (TEM); Dh: hydrodynamic diameter (DLS); PI: polydispersity (DLS); L: average crystallite size (XRD); C: carbon content; N: nitrogen content; TGA: thermogravimetric analysis; I545/I660: characteristic upconversion ratio.

[2190-4286-6-235-2]

Figure 2: Particle size distribution of no. 4 OM-NaYF4:Yb3+/Er3+ nanoparticles (Table 1) determined by DLS.

Morphology and crystalline structure of the dry OM–NaYF4:Yb3+/Er3+ nanocrystals were determined by TEM/BF, TEM/ED and XRD. The crystal structure of NaYF4 typically exhibits two polymorphic forms: the metastable cubic α-phase and the thermodynamically stable hexagonal β-phase. The latter is a much better host lattice for the luminescence of various optically active lanthanide ions. Altering reaction temperature is a successful approach to control crystal structures. Higher reaction temperature and longer reaction time are required to provide sufficient free energy to overcome the activation barrier of an α/ß phase transition [19,33]. In the XRD experiments, all crystal diffractions and amorphous halos of the OM–NaYF4:Yb3+/Er3+ nanoparticles were fitted by Voigt [34] and Gaussian peak functions, respectively, yielding the position, full width of half maximum (FWHM), and area for each peak. The effect of reaction temperature on OM–NaYF4:Yb3+/Er3+ crystallinity is shown in Figure 3a. The degree of crystallinity of the particles reached 67–77 wt % (Table 1). The amorphous halo originated from OM surrounding the NaYF4:Yb3+/Er3+ crystallites. Sizes of the cubic and hexagonal phases were estimated using the Scherrer equation from the [111] (2θ = 28.2) and [101] (2θ = 30.9) reflections, respectively [35]. XRD diffractograms of the OM–NaYF4:Yb3+/Er3+ nanoparticles prepared at lower temperatures exhibited both α- and β-phases, but the average α-phase crystallite size decreased from about 9 to 6 nm with increasing temperature (Table 1). In contrast, the average size of the β-phase crystals increased from 12 to 21 nm, which was in rough agreement with the Dn determined by TEM. As seen in the diffractograms, nanoparticles with both cubic and hexagonal phases were obtained at 250 and 280 °C, respectively. When the particles were synthesized at temperatures above 300 °C, the intensity of the peaks corresponding to the hexagonal OM–NaYF4:Yb3+/Er3+ phase increased significantly. The particles obtained at 330 and 350 °C exhibited the hexagonal phase, but traces of the cubic phase were still present in the lower temperature particles. The position of the XRD peaks (Figure 3a) corresponded to the hexagonal phase, as published in literature [20].

[2190-4286-6-235-3]

Figure 3: X-ray diffraction patterns of OM-NaYF4:Yb3+/Er3+: effect of (a) reaction temperature (time 1 h) and (b) time (temperature 330 °C). Lines corresponding to hexagonal and cubic phases were found in [36]. The arrows at the top of the image denote the most intensive diffractions of the cubic phase.

The results presented above are in good agreement with those from TEM/ED (Figure 4a,b and Figure 5a,b). Both methods illustrated the significant impact of the reaction temperature on the properties of the particles. The particles prepared at low temperatures (250 °C) exhibited cubic crystal structures [19,33] (Figure 4a,b), whereas the particle structure obtained at higher temperatures (≥ 330 °C) was hexagonal and corresponded to Na(Y0.57Yb0.39Er0.04)F4 (Figure 5a,b). The EDX spectra contained strong peaks for the main components (Na, Y, F) and detectable Yb, but the amount of Er was below the detection limit (Figure 4c and Figure 5c). The spectra also contained signals from the sample holder (Cu), supporting carbon film (C), small amounts of oleylamine (C, O, N) and inorganic impurities (Si).

[2190-4286-6-235-4]

Figure 4: TEM analysis: (a) ED pattern, (b) comparison of experimental ED pattern and calculated XRD pattern, and (c) EDX spectrum of no. 1 OM–NaYF4:Yb3+/Er3+ nanoparticles. Peaks were indexed according to [20].

[2190-4286-6-235-5]

Figure 5: TEM analysis: (a) ED pattern, (b) comparison of experimental ED pattern and calculated XRD pattern, and (c) EDX spectrum of OM-NaYF4:Yb3+/Er3+ nanoparticles no. 4. Peaks were indexed according to [20].

Another method used to investigate the OM–NaYF4:Yb3+/Er3+ nanoparticles was elemental analysis. The amount of the OM shell on the NaYF4:Yb3+/Er3+ nanoparticles was determined from carbon and nitrogen concentrations according to the following equations: % coating according to C = (% C in sample × 100)/80.74, where 80.74 is % C in OM, and % coating according to N = (% N in sample × 100)/5.23, where 5.23 is % N in OM. The percentage of the OM shell on the nanoparticles prepared at 250–330 °C ranged between approximately 3 and 6 wt % according to both carbon and nitrogen analysis. In contrast, the no. 5 OM–NaYF4:Yb3+/Er3+ nanoparticles obtained at 350 °C (Table 1) contained relatively high amounts of coating (23 and 21 wt % according to C and N analysis, respectively). The OM content on the OM–NaYF4:Yb3+/Er3+ nanoparticles prepared at different reaction temperatures was also determined by TGA (Figure 6a). Small weight losses (ca. 1 wt %) observed upon heating from room temperature to ca. 150 °C were ascribed to evaporation of water and ethanol. Major weight loss was observed at temperatures between 200 and 500 °C due to OM decomposition. If the particles were prepared at 250–330 °C, the amount of OM on the particle surface was rather low (ca. 5–11 wt %). However, the no. 5 particles prepared at 350 °C contained much higher amounts of OM (35 wt %) due to its enhanced adsorption on the surface. Determination of the amount of coating by elemental analysis and TGA was mostly in agreement, but the TGA results were systematically higher, likely due to chemical transformation of inorganic compounds at high temperatures.

[2190-4286-6-235-6]

Figure 6: TGA of OM–NaYF4:Yb3+/Er3+ nanoparticles prepared at (a) different reaction temperatures for 1 h and (b) different reaction times at 330 °C.

To investigate the optical properties of the OM–NaYF4:Yb3+/Er3+ nanoparticles prepared at different reaction temperatures, the upconversion emission spectra were recorded at 980 nm excitation (Figure 7a). The energy transfer upconversion started after sequential absorption of NIR photons (e.g., 980 nm) by Yb3+ ions, leading to the population of Yb3+ ions from the 4F7/2 ground to the 4F5/2 excited state (Figure 8). This scheme was proposed by Wang, who suggested that the energy was then transferred from the two excited Yb3+ ions to the 4F7/2 state of the neighboring Er3+ ion [37]. The 2H11/2 and 4S3/2 states of the Er3+ ion were populated by nonradiative multiphonon relaxation of the 4F7/2 state. From these levels, the ion could return directly to the 4I15/2 ground state or populate the 4F9/2 state by an additional nonradiative multiphonon relaxation. Consequently, three different Er3+ transitions were induced by NIR photons leading to the visible light emission [37]. Hence, the NaYF4:Yb3+/Er3+ nanocrystals exhibited three bands of green (520 and 545 nm) and red (660 nm) upconversion emissions corresponding to 2H11/2 and 4S3/2 → 4I15/2 and 4F9/2 → 4I15/2 transitions, respectively. These bands were induced by 4f–4f transitions of the Er3+ ions.

[2190-4286-6-235-7]

Figure 7: NIR-to-vis upconversion emission spectra of OM–NaYF4:Yb3+/Er3+ nanoparticles excited at 980 nm with a power density of 3 mW/cm2. Effect of (a) reaction temperature and (b) time.

[2190-4286-6-235-8]

Figure 8: Energy-level diagram of Yb3+/Er3+ and the upconversion mechanism at 980 nm excitation. The doted and dashed curves represent photon excitation/energy transfer and relaxation, respectively. Only visible emissions are shown [38].

Because the red light photons are important for prospective biomedical applications, the I545/I660 ratio should be rather low and the total luminescence intensity high. The ratio of green to red emission intensities changed from 2.50 to 1.68. The light emitted by the no. 1 particles prepared at 250 °C had a low intensity due to their cubic crystal structure. However, the no. 2 particles prepared at 280 °C had a higher I545/I660 ratio. This can be explained by the different interatomic distances between the Yb3+ and Er3+ ions in the crystal structure, which changed from cubic to hexagonal. The crystals were not completely hexagonal and contained some cubic impurities, and the distances between Yb3+ and Er3+ therefore differed, increasing the green light intensity. The red light intensity remained constant due to insufficient energy transfer to Er3+ and energy losses between the ions. When the particles were prepared at temperatures above 300 °C, luminescence intensities were slightly higher, indicating that maximum luminescence efficiency was achieved by optimizing the interatomic distance between the absorbers and the emitters.

Effect of reaction time

In these experiments, OM-NaYF4:Yb3+/Er3+ nanoparticles were prepared at 330 °C and reaction times ranged from 0.5 to 4 h. Other reaction conditions were held constant as described above. The size of the NaYF4:Yb3+/Er3+ nanoparticles of nos. 4 and 6–9 was again approximately 10 nm and the particle size distribution was rather narrow (Table 1 and Table 2). The degree of crystallinity according to XRD (Figure 3b) was approximately 75 wt % (Table 2). A small amorphous halo originated primarily from OM on the nanoparticle surface. In α- and β-phase particles, the presence of an amorphous halo is indicative of a disorder-to-order type cubic-to-hexagonal phase transition [39]. The size of α crystallites ranged from 6 to 6.5 nm, and the size of β-phase crystals ranged between 18–21 nm. Interestingly, diffraction peaks corresponding to the cubic phase were hardly visible in the OM–NaYF4:Yb3+/Er3+ nanoparticles prepared for 3 h, and the size of the crystallites could not be determined. No structural changes were observed by XRD in the particles prepared at different reaction times, indicating that a 4 h reaction time was not sufficient for full conversion of the particles into the hexagonal phase at reaction temperatures below 350 °C. The percentage of coating was again analyzed by both elemental analysis and TGA. The thermal degradation of the OM–NaYF4:Yb3+/Er3+ nanoparticles was similar to that shown in Figure 6a, with the main loss typically occurring between 200 and 600 °C (Figure 6b). According to elemental analysis, the amount of coating ranged from 3 to 7.5 wt %, in accordance with previously described results on the effect of reaction temperature. The content of OM according to TGA was again higher (5.6–14.3 wt %) than when determined by elemental analysis (Table 2). The amount of coating grew as reaction time increased from 0.5 to 3 h.

Table 2: Effect of reaction time on OM–NaYF4:Yb3+/Er3+ nanoparticles prepared at 330 °C.

no. time (h) Dn (nm) PDI Dh (nm) PI L(cubic)
(nm) 		L(hex)
(nm) 		crystallinity
(wt %) 		C (wt %) N (wt %) coating (wt %) I545/I660
C N TGA
6 0.5 8 1.20 265 0.54 6.3 19.8 75 2.37 0.11 2.9 2.0 5.6 1.86
4 1 10 1.30 188 0.27 6.4 18.6 74 3.00 0.15 3.7 2.9 7.1 1.79
7 2 11 1.08 200 0.54 6.5 20.8 77 6.12 0.21 7.6 4.0 13.8 1.39
8 3 10 1.15 289 0.69 – 19.9 73 5.88 0.32 7.3 6.1 14.3 1.38
9 4 9 1.09 308 0.63 6.0 17.6 75 5.42 0.31 6.7 5.8 10.9 1.31

Dn: number-average diameter (TEM); PDI: polydispersity index (TEM); Dh: hydrodynamic diameter (DLS); PI: polydispersity (DLS); L: average crystallite size (XRD); C: carbon content; N: nitrogen content; TGA: thermogravimetric analysis; I545/I660: characteristic upconversion ratio

Visible upconversion spectra of the OM–NaYF4:Yb3+/Er3+ nanoparticles prepared at constant temperature (330 °C) and varying reaction time are shown in Figure 7b. The presence of green and red light was confirmed in three emission spectra of the investigated nanoparticles after two-photon excitation at 980 nm. The intensities of green and red light slightly and significantly increased with increasing reaction time, which can be associated with a highly ordered ion structure of the nanocrystals. The intensity ratio I545/I660 decreased with increasing reaction time.

Modification of the OM–NaYF4:Yb3+/Er3+ nanoparticle surface with SiO2

The OM–NaYF4:Yb3+/Er3+ nanoparticles were easily dispersed in nonpolar organic solvents, such as hexane or toluene, due to the presence of aliphatic OM side chains on the surface. However, the nanoparticles must disperse in aqueous media for biological applications. To disperse the no. 4 NaYF4:Yb3+/Er3+ nanoparticles in water, they were coated with a thin silica shell using a microemulsion technique. TMOS and Igepal CO-520 were used as a precursor and an emulsifier, respectively. Compared with the initial 10 nm OM–NaYF4:Yb3+/Er3+ nanoparticles, the TEM micrograph (Figure 9) showed that the size of the NaYF4:Yb3+/Er3+&SiO2 particles had increased to 17 nm due to the presence of the silica shell on the surface. The NaYF4:Yb3+/Er3+&SiO2 nanoparticles had a clear core–shell structure with a shell thickness of about 3.5 nm. The presence of the silica shell on the NaYF4:Yb3+/Er3+ nanoparticles was further confirmed by comparing the ATR FTIR spectra of unmodified and modified nanoparticles (Figure 10). The initial OM–NaYF4:Yb3+/Er3+ particles had characteristic absorption bands at 2925 and 2857 cm−1 attributed to the asymmetric and symmetric stretching vibrations of the methylene units in the long OM chain [40,41]. After deposition of the silica onto the surface, these peaks were not detected in the ATR FTIR spectrum. New intense absorption bands at 1090 and 795 cm−1 in the spectrum of the NaYF4:Yb3+/Er3+&SiO2 particles were attributed to the symmetric and asymmetric Si–O–Si stretching vibrations, respectively [42]. An intense 960 cm−1 band was also observed in the spectrum of the modified nanoparticles, corresponding to the symmetric stretching vibrations of the Si–OH bonds in the silica [26]. The main evidence for the presence of an OH group was the appearance of intensive broad absorption bands at 3445 and 1630 cm−1. These bands are characteristic of OH vibrations. The abovementioned characteristic silica bands verified the presence of SiO2 on surface of the NaYF4:Yb3+/Er3+ and successful surface modification.

[2190-4286-6-235-9]

Figure 9: TEM micrograph of NaYF4:Yb3+/Er3+&SiO2 nanoparticles. Inset: C – particle core and S – SiO2 shell.

[2190-4286-6-235-10]

Figure 10: ATR FTIR spectra of OM–NaYF4:Yb3+/Er3+ and NaYF4:Yb3+/Er3+&SiO2 nanoparticles.

Conclusion

OM–NaYF4:Yb3+/Er3+ nanoparticles were synthesized by conventional thermal decomposition of lanthanide trifluoroacetates in OM. Particle morphology was controlled by the careful selection of reaction temperature and time, as evidenced by TEM. XRD and TEM/ED measurements confirmed the presence of cubic α- and hexagonal β-phases in the crystallites. The latter form is preferred in biomedical applications due to its high upconversion efficiency. From a synthetic point of view, temperature had the greatest influence on the resulting crystalline structure. The pure hexagonal phase was obtained at reaction temperatures ≥ 350 °C and annealing times above 1 h. To generate free radicals such as singlet oxygen (destructive to cancer cells) in biological experiments, the nanoparticles should emit photons at 660 nm to excite phthalocyanine, a typical photosensitizer [43]. Upconversion OM–NaYF4:Yb3+/Er3+ nanoparticles were excited by near-infrared light at 980 nm, i.e., at the Yb3+ absorption maximum. Photons were emitted at 520, 545 and 660 nm in the fluorescence spectra of the OM–NaYF4:Yb3+/Er3+ nanoparticles. The NaYF4:Yb3+/Er3+ nanoparticles were successfully coated with a silica shell using the reverse microemulsion method, making them dispersible in water and promising candidates for applications in biology and medicine.

Acknowledgements

Financial support from the Grant Agency of the Czech Republic (project 15-01897S) is gratefully acknowledged. The authors also acknowledge the Charles University in Prague, Department of Physical and Macromolecular Chemistry, for the opportunity of Uliana Kostiv’s doctoral studies.

References

  1. Knopp, D.; Tang, D.; Niessner, R. Anal. Chim. Acta 2009, 647, 14–30. doi:10.1016/j.aca.2009.05.037
    Return to citation in text: [1]
  2. Wang, L. S.; Chuang, M. C.; Ho, J. A. Int. J. Nanomed. 2012, 7, 4679–4695. doi:10.2147/IJN.S33065
    Return to citation in text: [1]
  3. Haase, M.; Schäfer, H. Angew. Chem., Int. Ed. 2011, 50, 5808–5829. doi:10.1002/anie.201005159
    Return to citation in text: [1]
  4. Zhou, J.; Liu, Q.; Feng, W.; Sun, Y.; Li, F. Chem. Rev. 2015, 115, 395–465. doi:10.1021/cr400478f
    Return to citation in text: [1]
  5. Chen, G.; Qiu, H.; Prasad, P. N.; Chen, X. Chem. Rev. 2014, 114, 5161–5214. doi:10.1021/cr400425h
    Return to citation in text: [1]
  6. Gnach, A.; Lipinski, T.; Bednarkiewicz, A.; Rybka, J.; Capobianco, J. A. Chem. Soc. Rev. 2015, 44, 1561–1584. doi:10.1039/C4CS00177J
    Return to citation in text: [1]
  7. Wang, C.; Cheng, L.; Liu, Z. Biomaterials 2011, 32, 1110–1120. doi:10.1016/j.biomaterials.2010.09.069
    Return to citation in text: [1]
  8. Wang, F.; Liu, X. Chem. Soc. Rev. 2009, 38, 976–989. doi:10.1039/b809132n
    Return to citation in text: [1]
  9. Mader, H. S.; Kele, P.; Saleh, S. M.; Wolfbeis, O. S. Curr. Opin. Chem. Biol. 2010, 14, 582–596. doi:10.1016/j.cbpa.2010.08.014
    Return to citation in text: [1]
  10. Chatterjee, D. K.; Fong, L. S.; Zhang, Y. Adv. Drug Delivery Rev. 2008, 60, 1627–1637. doi:10.1016/j.addr.2008.08.003
    Return to citation in text: [1]
  11. Chatterjee, D. K.; Rufaihah, A. J.; Zhang, Y. Biomaterials 2008, 29, 937–943. doi:10.1016/j.biomaterials.2007.10.051
    Return to citation in text: [1]
  12. Schäfer, H.; Ptacek, P.; Kömpe, K.; Haase, M. Chem. Mater. 2007, 19, 1396–1400. doi:10.1021/cm062385b
    Return to citation in text: [1]
  13. Wang, F.; Han, Y.; Lim, C. S.; Lu, Y.; Wang, J.; Xu, J.; Chen, H.; Zhang, C.; Hong, M.; Liu, X. Nature 2010, 463, 1061–1065. doi:10.1038/nature08777
    Return to citation in text: [1]
  14. Vogel, A.; Venugopalan, V. Chem. Rev. 2003, 103, 577–644. doi:10.1021/cr010379n
    Return to citation in text: [1]
  15. Auzel, F. Chem. Rev. 2004, 104, 139–173. doi:10.1021/cr020357g
    Return to citation in text: [1]
  16. Naccache, R.; Vetrone, F.; Mahalingam, V.; Cuccia, L. A.; Capobianco, J. A. Chem. Mater. 2009, 21, 717–723. doi:10.1021/cm803151y
    Return to citation in text: [1]
  17. Suyver, J. F.; Grimm, J.; van Veen, M. K.; Biner, D.; Krämer, K. W.; Güdel, H. U. J. Lumin. 2006, 117, 1–12. doi:10.1016/j.jlumin.2005.03.011
    Return to citation in text: [1]
  18. Kang, X.; Cheng, Z.; Li, C.; Yang, D.; Shang, M.; Ma, P.; Li, G.; Liu, N.; Lin, J. J. Phys. Chem. C 2011, 115, 15801–15811. doi:10.1021/jp203039t
    Return to citation in text: [1]
  19. Mai, H.-X.; Zhang, Y.-W.; Si, R.; Yan, Z.-G.; Sun, L.-D.; You, L.-P.; Yan, C.-H. J. Am. Chem. Soc. 2006, 128, 6426–6436. doi:10.1021/ja060212h
    Return to citation in text: [1] [2] [3]
  20. Yi, G. S.; Chow, G. M. Adv. Funct. Mater. 2006, 16, 2324–2329. doi:10.1002/adfm.200600053
    Return to citation in text: [1] [2] [3] [4] [5] [6] [7]
  21. Lin, M.; Zhao, Y.; Wang, S. Q.; Liu, M.; Duan, Z. F.; Chen, Y. M.; Li, F.; Xu, F.; Lu, T. J. Biotechnol. Adv. 2012, 30, 1551–1561. doi:10.1016/j.biotechadv.2012.04.009
    Return to citation in text: [1]
  22. Li, C.; Lin, J. J. Mater. Chem. 2010, 20, 6831–6847. doi:10.1039/c0jm00031k
    Return to citation in text: [1]
  23. Verma, A.; Rotello, V. M. Chem. Commun. 2005, 303–312. doi:10.1039/b410889b
    Return to citation in text: [1]
  24. Luccardini, C.; Tribet, C.; Vial, F.; Marchi-Artzner, V.; Dahan, M. Langmuir 2006, 22, 2304–2310. doi:10.1021/la052704y
    Return to citation in text: [1]
  25. Skajaa, T.; Zhao, Y.; van den Heuvel, D. J.; Gerritsen, H. C.; Cormode, D. P.; Koole, R.; van Schooneveld, M. M.; Post, J. A.; Fisher, E. A.; Fayad, Z. A.; de Mello Donega, C.; Meijerink, A.; Mulder, W. J. M. Nano Lett. 2010, 10, 5131–5138. doi:10.1021/nl1037903
    Return to citation in text: [1]
  26. Qian, L. P.; Yuan, D.; Yia, G. S.; Chow, G. M. J. Mater. Res. 2009, 24, 3559–3568. doi:10.1557/jmr.2009.0432
    Return to citation in text: [1] [2]
  27. Guerrero-Martínez, A.; Pérez-Juste, J.; Liz-Marzán, L. M. Adv. Mater. 2010, 22, 1182–1195. doi:10.1002/adma.200901263
    Return to citation in text: [1]
  28. Jalil, R. A.; Zhang, Y. Biomaterials 2008, 29, 4122–4128. doi:10.1016/j.biomaterials.2008.07.012
    Return to citation in text: [1]
  29. Lábár, J. L. Ultramicroscopy 2005, 103, 237–249. doi:10.1016/j.ultramic.2004.12.004
    Return to citation in text: [1]
  30. Kraus, W.; Nolze, G. J. Appl. Crystallogr. 1996, 29, 301–303. doi:10.1107/S0021889895014920
    Return to citation in text: [1]
  31. Klug, H. P.; Alexander, L. E. X-Ray Powder Diffraction Procedures; Wiley: New York, NY, U.S.A., 1959; p 491.
    Return to citation in text: [1]
  32. Metz, S.; Bonaterra, C.; Rudelius, M.; Settles, M.; Rummeny, E. J.; Daldrup-Link, H. E. Eur. Radiol. 2004, 14, 1851–1858. doi:10.1007/s00330-004-2405-2
    Return to citation in text: [1]
  33. Wei, Y.; Lu, F.; Zhang, X.; Chen, D. Chem. Mater. 2006, 18, 5733–5737. doi:10.1021/cm0606171
    Return to citation in text: [1] [2]
  34. Voigt, W. Sitzungsber. - Bayer. Akad. Wiss., Math.-Naturwiss. Kl. 1912, 42, 603.
    Return to citation in text: [1]
  35. Hyppänen, I.; Hölsä, J.; Kankare, J.; Lastusaari, M.; Pihlgren, L.; Soukka, T. J. Fluoresc. 2011, 21, 963–969. doi:10.1007/s10895-010-0655-8
    Return to citation in text: [1]
  36. Wang, L.; Yan, R.; Huo, Z.; Wang, L.; Zeng, J.; Bao, J.; Wang, X.; Peng, Q.; Li, Y. Angew. Chem., Int. Ed. 2005, 44, 6054–6057. doi:10.1002/anie.200501907
    Return to citation in text: [1]
  37. Wang, L.; Li, Y. Chem. Mater. 2007, 19, 727–734. doi:10.1021/cm061887m
    Return to citation in text: [1] [2]
  38. Suyver, J. F.; Aebischer, A.; Biner, D.; Gerner, P.; Grimm, J.; Heer, S.; Krämer, K. W.; Reinhard, C.; Güdel, H. U. Opt. Mater. 2005, 27, 1111–1130. doi:10.1016/j.optmat.2004.10.021
    Return to citation in text: [1]
  39. Liang, X.; Wang, X.; Zhuang, J.; Peng, Q.; Li, Y. Adv. Funct. Mater. 2007, 17, 2757–2765. doi:10.1002/adfm.200600807
    Return to citation in text: [1]
  40. Mourdikoudis, S.; Liz-Marzán, L. M. Chem. Mater. 2013, 25, 1465–1476. doi:10.1021/cm4000476
    Return to citation in text: [1]
  41. Klokkenburg, M.; Hilhorst, J.; Erné, B. H. Vib. Spectrosc. 2007, 43, 243–248. doi:10.1016/j.vibspec.2006.09.008
    Return to citation in text: [1]
  42. Chekina, N.; Horák, D.; Jendelová, P.; Trchová, M.; Beneš, M. J.; Hrubý, M.; Herynek, V.; Turnovcová, K.; Syková, E. J. Mater. Chem. 2011, 21, 7630–7639. doi:10.1039/c1jm10621j
    Return to citation in text: [1]
  43. Guo, H.; Qian, H.; Idris, N. M.; Zhang, Y. Nanomedicine 2010, 6, 486–495. doi:10.1016/j.nano.2009.11.004
    Return to citation in text: [1]

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