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Monodisperse upconversion GdF3:Yb, Er rhombi by microwave-assisted synthesis

Nanoscale Research Letters20116:267

Received: 3 November 2010

Accepted: 29 March 2011

Published: 29 March 2011


We have synthesized a variety of monodisperse colloidal GdF3:Yb, Er upconversion nanocrystals with different shape, size, and dopants by microwave-assisted synthesis. Typical upconversion emission from Er3+ was observed. In addition to highly monodisperse spherical particles, we were able to prepare monodispersed rhombic-shaped slices that showed a tendency for self-assembly into stacks.


  • High Resolution Transmission Electron Microscopy
  • High Resolution Transmission Electron Microscopy
  • NaYF4
  • Upconversion Luminescence
  • GdF3


In recent publications we have shown that microwave-assisted synthesis allows for the preparation of highly monodisperse, spherical upconversion nanocrystals [1], as well as nanocrystals with unusual morphologies [2]. In this research letter, we report on the microwave-assisted synthesis of monodispersed spherical and rhombic GdF3-based nanoparticles, which show a high tendency for self-assembly in one- and two-dimensional superstructures.

Research on upconversion nanocrystals increased exponentially over the past several years (e.g., in 2000, one article on upconversion nanomaterials was published, in 2009, it have been 57) as the extremely attractive prospects for applications of these materials in bioanalytics [3], (cancer) therapy [4], and electro-optics [5]. And subsequently, it is concluded that the most efficient infrared-to-visible upconversion phosphors are Yb/Er or Yb/Tm co-doped fluorides, such as hexagonal phase NaYF4 [6, 7], LaF3 [8, 9], and orthorhombic phase YF3 [10], GdF3 [11]. Especially in the past few years, the NaYF4-based phosphors, as the highest efficient upconversion phosphors, with different morphologies and different dopants have been widely investigated, based on various synthesis procedures. However, GdF3 as one of the efficient upconversion phosphor host [8], not too much work has been reported focusing on Yb/Er codoped fluorecence upconversion. Although Tm, Dy, Ho, and Yb/Tm doped GdF3 has been reported [1114]. As far as we know, in 1971, the preparation of GdF3:Yb, Er phosphor was reported firstly by Major et al. In their procedure, the oxide precursors were dissolved in high purity nitric acid and precipitated with excess hydrofluoric acid, and finally experienced calcination. They found that the color of the anti-Stokes luminescence of the Yb/Er doped GdF3 phosphors was controllable by preparation processes, and was associated with the crystal structure of the host lattices. And they gave a dominant green emission when excited by 940 nm infrared light [10]. In 2006, Fan et al. employed a hydrothermal synthesis procedure to produced Yb/Er codoped GdF3 nanoparticles. For their prepared sample, typical upconversion emission was observed but with much weaker intensity than that of bulk crystal [15].

Microwave-assisted synthesis of nanomaterials offers several interesting synthetic opportunities which are based on the specific microwave effects: (i) microwave irradiation is absorbed by polar and ionic substances only (dielectric heating); (ii) enhanced reaction rates can be observed; (iii) heterogeneous heating (viz. "hot spots") and wall effects can be suppressed [16]. Details on the microwave-assisted synthesis of AYF4 (A = Na, Li) nanocrystals can be found elsewhere [1]. This research letter is concerned with the effects of microwave irradiation on the shape evolution of GdF3 nanocrystals.

In this paper, we firstly presented the preparation of colloidal upconversion GdF3:Yb, Er nanocrystals, based on a new microwave-assisted synthesis method. We have synthesized a variety of GdF3-based upconversion nanocrystals with different shape, size, and dopants by microwave-assisted synthesis. In addition to highly monodisperse spherical particles, we were able to prepare monodisperse rhombic-shaped slices that showed a tendency for self-assembly into stacks.


According to our previous work [1], introduction of Li+ can help to enhance the upconversion efficiency. So here in the procedure, Li+ was used as well. In a typical synthesis (standard conditions), 0.115 mmol (13.8 mg) lithium trifluoroacetate (TFA), 0.083 mmol (41.2 mg) gadolinium TFA, 17 μmol (8.5 mg) ytterbium TFA, and 1.7 μmol (0.86 mg) erbium TFA were dissolved in 6 ml of a 1:1 (v:v) mixture of oleic acid and octadecene in a nitrogen atmosphere. The solution was thoroughly degassed at 120°C and transferred into a microwave reaction vessel. Then, the mixture was heated for 10 min at 290°C by microwave irradiation. The resulting nanocrystals were precipitated by addition of 3 ml of ethanol to the cold reaction solution and subsequent centrifugation. The supernatant was discarded and the nanocrystals were repeatedly washed with ethanol. Eventually, the particles were re-dissolved in chloroform or toluene for further studies.

Transmission electron micrographs (TEMs) were recorded on a JEOL 2000EX and a JEOL 2010 microscope at 200 kV. Selected area electron diffraction (SAED) patterns were measured on the same instrument. The X-ray diffraction (XRD) patterns were measured with a thermo ARL XTRA equipped with a Cu X-ray tube (λ = 1.5418 Å). Upconversion spectra were recorded on an Oceanoptics USB spectrometer and a home-made cuvette holder and excitation source (980 nm, 100 mW laser diode).

Results and discussion

Figure 1 shows TEMs of the resulting nanocrystals. It was observed that the particles were regularly shaped rhombic plates with approximately 3.2 nm thickness, approximately 45 nm in length and with a roughly calculated aspect ratio of 1:3. Both micrographs show clearly that the nanoplates have a strong tendency to form two-dimensional aggregates. This effect can be attributed to the minimization in energy, which is achieved by hydrophobic interaction of the surface ligands of the nanoparticles at their largest faces.
Figure 1
Figure 1

TEMs of GdF 3 nanocrystals. (A) Overview graph of single nanocrystals and "stacks". (B) Blow-up of self-assembled nanocrystals.

The XRD pattern of these particles (Figure 2) which shows orthorhombic phase GdF3 was obtained. Almost all the diffraction peaks of the XRD pattern can be assigned, respectively, to the planes of orthorhombic GdF3 crystalline (JCPDS-file 012-0788), as indicated (101), (020), (111), (210), (002), (221), (112), (301), (230), (212) in Figure 2 (red, round dot). However, two more weak diffraction peaks can also be observed at 2θ = 38.7° and 45°, which cannot be assigned to GdF3. We considered that these two weak peaks arose from the diffraction of LiF (JCPDS-file 045-1460) [17]. And it suggests that the Li+ was not only introduced into the expected phosphor GdF3 crystal to replace some Gd3+ sites as impurity but also a few LiF was formed. A further confirmation of a predominant GdF3 lattice can be found by measuring distances of the lattice fringes in the high resolution transmission electron microscopy (HRTEM). Lattice fringes were found with distances of 3.29 and 2.94 Å (cf. Figure 3B), corresponding well to the theoretically calculated distance of the {111} and {210} planes of the orthorhombic-YF3 space group GdF3 (orthorhombic phase JCPDS-file 012-0788), respectively. It is noteworthy that the same XRD patterns were observed for decreased and increased reactant concentrations.
Figure 2
Figure 2

XRD pattern of GdF3 nanocrystals as depicted in Figure 1. Full circle (red): diffraction pattern according to JCPDS-file 012-0788; full square (green): diffraction pattern according to JCPDS-file 045-1460.

Figure 3
Figure 3

TEMs of GdF3 nanocrystals prepared with 25% of the original concentration of reactants. (A) Overview picture. (B) High-resolution TEM of single nanocrystals.

In our previous work, we found that changing the reaction parameters (especially the concentration of reactants) in the synthesis of NaYF4-based upconversion nanocrystals, has crucial influence on the morphology of the resulting particles [2]. In this work, we observed that, based on our precursors, GdF3 nanocrystals were obtained and always adopt a rhombic shape under microwave irradiation, even when other synthesis parameters were changed.

Figure 3 shows TEMs of GdF3 nanocrystals that were synthesized under the above conditions, but with 25% of the original concentration of reactants. The particles are smaller than the ones displayed in Figure 1 (approximately 15-18 nm in length), but have roughly the same thickness and aspect ratio. Therefore, the rate of growth along the "edges" of the particles has to be much faster as compared to the primary faces ({111} and {210}). Figure 3B shows a HRTEM of the same particles. It can be observed that the lattice fringes are always aligned with one edge of the rhombi. This observation and the overall shape of the nanocrystals are in agreement with the anticipated orthorhombic-YF3 space group [18].

When the concentration of reactants was increased by a factor of five, compared with the standard conditions, the nanocrystals were still predominantly rhombic in shape (in addition, some spherical particles were observed), but approximately 150 nm in length and 5 nm in thickness (cf. Figure 4A). This finding confirms further that the nanocrystals grow preferentially in two dimensions. Again, the XRD pattern is associated well with the orthorhombic phase GdF3, and without diffraction peaks of LiF any more (Figure 4C). Figure 4C inset shows the SAED pattern of this prepared sample. Figure 4B shows the TEM of the obtained nanocrystals that were prepared under identical conditions as the ones in Figure 4A, but using traditional conductive heating. Shape and size of these particles are roughly in the order of magnitude of the standard conditions described above. However, the XRD pattern (inset Figure 4B) of these nanocrystals shows that mainly cubic LiF nanocrystals have been synthesized.
Figure 4
Figure 4

TEM, XRD and SAED characterization of obtained samples. (A) TEM micrograph of GdF3 nanocrystals synthesized at five times the standard concentration. (B) LiF nanocrystals synthesized by traditional conductive heating at the same conditions like A. Inset: XRD pattern of the obtained nanocrystals. (C) XRD pattern of GdF3 nanocrystals synthesized at five times the standard concentration. Inset: SAED pattern of the prepared sample.

Figure 5 shows the upconversion emission spectrum of the nanocrystals from Figure 4A, under 980 nm near infra-red (NIR) excitation. Mainly two emission bands were observed, with emission peaks at 521, 545, and 660 nm. These emission peaks can be attributed to the 4f-4f transitions of the Er3+ ions. The green emission accounts for the 2H(11/2), 4S(3/2)4I(15/2) transition, the red emission is caused by the 4F(9/2)4I(15/2) transition. The difference compared with typical reported Yb/Er emission spectrum is that a weak red emission at approximately 628 nm was observed, which could be attributed to the transition 4I(9/2)4I(15/2). Based on Yb/Er codopants, the observed upconversion efficiency of the GdF3-based nanocrystals is relatively lower than that of the NaYF4-based nanocrystals in our lab [1]. Comparing these values with data from the literature shows that the microwave-assisted synthesis does not influence the optical properties of the nanocrystals per se.
Figure 5
Figure 5

Upconversion spectrum of GdF 3 :Yb, Er nanocrystals under excitation of 980 nm.

In order to establish the reason for the strict rhombic shape of the nanocrystals, we replaced lithium with sodium in the above synthesis method. Yb/Ho codoped NaGdF4 nanocrystals were synthesized under the same conditions as above. Figure 6A shows the TEMs of the resulting particles with high and low reactant concentration, respectively. It can be seen that monodisperse, spherical particles were synthesized at low reactant concentration, and a bimodal distribution of monodisperse, spherical, and irregular larger nanocrystals at higher concentrations. Hence, these particles adopted a completely different morphology compared with GdF3. Figure 6C shows a XRD pattern of these particles, which confirms that the nanocrystals have crystallized in the cubic α-NaGdF4 phase (JCPDS 27-697). Therefore, we can conclude that the rhombic morphology of the GdF3 nanocrystals was primarily driven by the crystal lattice. Under the 980 nm excitation, mainly three emission bands were observed (Figure 6D). Predominantly green upconversion luminescence was observed at 542 nm, corresponding to the transition from the 5F4 and 5S2 to the 5I8 ground state. A weaker red and NIR upconversion luminescence was observed at 650 and 751 nm, which could be attributed to the transition from the 5F55I8 and 5F4, 5S25I7 states, respectively, which is in agreement with data from the literature.
Figure 6
Figure 6

TEMs of NaGdF4:Yb, Ho nanocrystals. (A) Five times standard concentration; (B) 25% standard concentration; (C) XRD pattern of NaGdF4:Yb, Ho nanocrystals; (D) Upconversion spectrum of NaGdF4:Yb, Ho nanocrystals under excitation of 980 nm.


Our experimental results allow for three major conclusions:
  1. 1.

    The presence of lithium does not impair the predominant orthorhombic-YF3 space group of GdF3 at all concentrations tested.

  2. 2.

    The crystallization in the orthorhombic-YF3 space group and the rhombic shape of the nanoparticles are specific microwave effects. Conductive heating leads to completely different nanocrystals, although rhombic in shape.

  3. 3.

    The optical properties (viz. upconversion) of the nanocrystals seem to be unaffected by the microwave-assisted synthesis method.


Thus, beyond being rapid and easy to use, microwave-assisted synthesis of upconversion nanocrystals allows for the crystallization of new nanocrystals and morphologies. Rhombic plates, like the ones synthesized in our study, might be key to self-assembly or supramolecular strategies towards an improvement of the upconversion quantum yield.



selected area electron diffraction




transmission electron microscopy


X-ray diffraction


high resolution transmission electron microscopy


near infra-red.



We acknowledge gratefully the financial support of the Deutsche Forschungsgemeinschaft (DFG project NA 373/7-1) for this work. Furthermore, we would like to thank Dr Richard D Tilley of the Victoria University of Wellington, NZ, for the HRTEM measurements. And we also thank Dr Miroslaw Batentschuk of the University Erlangen for proof reading of the manuscript.

Authors’ Affiliations

Institute Materials for Electronics and Energy Technology (I-MEET), Friedrich Alexander Universität Erlangen-Nürnberg, Erlangen, Germany
Ian Wark Research Institute, University of South Australia, Mawson Lakes, Australia


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© Wang and Nann; licensee Springer. 2011

This article is published under license to BioMed Central Ltd. This is an Open Access article distributed under the terms of the Creative Commons Attribution License (, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.