One-step growth of lanthanoid metal–organic framework (MOF) films under solvothermal conditions for temperature sensing †

A one-step direct solvothermal synthesis of an Ln metal–organic framework (MOF) film is reported. The LnHL (Ln = Tb and Gd) films that were deposited on a Gd 2 O 3 subtrate are continuous and smooth. The Gd 0.9 Tb 0.1 HL film can be used as a ratiometric thermometer, showing good linear behaviour in the temperature range of 110–250 K with a sensitivity up to 0.8% K (cid:2) 1 .

Metal-organic frameworks (MOFs) are promising materials for many applications such as gas storage and separation, ion and small molecule sensing, catalysis and proton conduction. [1][2][3][4] Lanthanoid MOFs are especially interesting materials due to their unique luminescence properties like high quantum yields, characteristic sharp line emissions and long lifetime. 5,6 Recently, the preparation and study of films of MOFs on supports gained increasing attention. [7][8][9][10][11] Due to the brittleness and insolubility of MOF crystals, thin films of such materials are difficult to process with common surface deposition methods, limiting the application of MOF films. 12 Five major methods to fabricate MOF films have been reported: (1) deposition of MOF films directly onto bare substrates or functionalized substrates with organic molecules; (2) deposition of MOF films on seeded substrates; (3) deposition of preformed MOF nanocrystals; (4) layer-by-layer deposition of MOF films; (5) electrodeposition. 13,14 Gold, silicon wafers, graphene, glass, indium tin oxide (ITO), and porous aluminium oxide are mostly used as substrates for MOF films. [13][14][15][16][17][18][19][20] Until now, most research concerning MOF films focuses on transition metals like Zn, Cu, Mn and Fe. Only few lanthanoid MOF films have been reported and most of these have been synthesized by post-functionalization strategies based on the 'parent' zinc, copper or indium MOF films, or by spin coating or dip coating of Ln MOF nanocrystals. 7,21-30 Meyer et. al. reported the in situ growth of Sr/Eu MOFs on anodic aluminum oxide (AAO) membranes using a melt approach with Eu and Sr metals and imidazole. Alternatively, the growth process was carried out by an electride-induced reaction from liquid ammonia. 31 Temperature is one of the most important parameters both in scientific research and industry. 32 In recent years, lanthanoidbased ratiometric luminescence thermometers have drawn great attention; the investigations in this field are mainly based on lanthanoid coordination compounds, or Er III /Yb III nanoparticles. 33 As the number of combinations of organic ligands with lanthanoid ions is unlimited, the composition and properties of a luminescence thermometer based on Ln MOFs can be varied easily. By careful engineering of a film of such a luminescence thermometer onto a suitable substrate a novel device can be developed with which surface temperature distribution can be easily mapped via a non-invasive method.
It has been reported that Zn and Cu MOF films can grow on zinc or copper metal surfaces, and indium-containing MOF films can grow on glass containing an indium tin oxide (ITO) coating. 15,[34][35][36] As most Ln MOFs are synthesized by hydrothermal or solvothermal methods, a method to deposit Ln MOF films using such hydro/solvothermal conditions would be highly valuable. To the best of our knowledge, such direct hydrothermal or solvothermal synthesis of Ln MOF films has not yet been reported, which may attributed mainly to the lack of a suitable substrate. Herein we report for the first time the use of an Ln oxide as substrate for the deposition of Ln MOF films by in situ solvothermal methods. Potentially, this method can be used for the production of a wide range of Ln MOF films.
Pellets of a Gd 2 O 3 substrate (diameter 13 mm, thickness around 1.5 mm) were prepared by compressing Gd 2 O 3 powder under static 10 tons pressure for 10 min. These pellets were transferred to a tube furnace and sintered at 1500 1C for 15 h to increase their mechanical strength (see ESI † for detailed description of the preparation). We envisaged that surface Gd ions from the Gd 2 O 3 substrate could act as nucleation sites for the growth of the MOF and thereby assist in the formation and improve the quality of the Ln MOF. The Gd III ion does not show any luminescence properties due to its f 7 electron configuration, and thus does not interfere with the luminescence properties of the film. Films of the compounds TbHL, GdHL and Gd 0.9 Tb 0.1 HL (H 4 L = 5-hydroxy-1,2,4-benzenetricarboxylic acid) on Gd 2 O 3 substrates were obtained using the solvothermal method with the same conditions as for the preparation of the bulk crystals. 37 The films were characterized with powder X-ray diffraction (PXRD) and scanning electron microscopy (SEM). The PXRD patterns of the films are highly similar to the simulated pattern from the single crystal X-ray structure of TbHL reported previously (Fig. 1), indicating that indeed the MOF grown on the Gd 2 O 3 surface has the same structure as the bulk material. 37 SEM was used to study the morphology of the Gd 2 O 3 substrate and the TbHL film. The Gd 2 O 3 substrate is a porous material (Fig. 2a). The TbHL film is packed tightly and smoothly onto the surface of the Gd 2 O 3 substrate (Fig. 2b); the thickness of the TbHL film is approximately 10 mm ( Fig. 2c and d).
Similar to the growth mechanism of the In MOF film on ITO glass, the Cu MOF film on a copper grid and the zinc MOF film on activated metallic zinc, we assume that the Gd 2 O 3 substrate provides Gd III ions as nucleation sites to improve the growth of the MOF at its surface. 15,[34][35][36] In addition the porous structure may provide better adhesion between the MOF film and the substrate. However, the presence of a porous structure by itself is not enough for the formation of a MOF film, as using a porous Al 2 O 3 pellet as the substrate did not yield the desired films.
Under 366 nm UV light (high pressure Hg lamp), the Gd 2 O 3 substrate is not luminescent while the TbHL film on this substrate exhibits intense green luminescence (Fig. S1, ESI †). When irradiated with 325 nm UV light, the TbHL film displays the characteristic Tb III sharp-line emissions at 490 ( 5 D 4 -7 F 6 ), 541 ( 5 D 4 -7 F 5 ), 587 ( 5 D 4 -7 F 4 ) and 622 nm ( 5 D 4 -7 F 3 ) (Fig. 3a). The dominant emission belongs to the hypersensitive 5 D 4 -7 F 5 transition (541 nm). Emission from the ligand is not observed, indicating efficient energy-transfer from the ligand to the Tb III center. A GdHL film on the Gd 2 O 3 substrate shows a weak broad-band emission from 350-650 nm as a result of ligand-centred phosphorescence (Fig. 3b). A Gd 0.9 Tb 0.1 HL film, doped with 10% Tb, clearly shows Tb III emission whereas the ligand-based phosphorescence is very weak (Fig. 3c). The excitation spectrum of the Gd 0.9 Tb 0.1 HL film, monitored at 541 nm, reveals a broad excitation band with a maximum at 325 nm that is ascribed to ligand-centred excitation. The two small peaks in the excitation spectrum at 369 ( 5 L 10 ' 7 F 6 ) and 379 nm ( 5 D 3 ' 7 F 6 ) are a result of the direct excitation of the Tb III ion (Fig. S2, ESI †). The emission lifetimes of Tb emission in the TbHL film and Gd 0.9 Tb 0.1 HL film were determined by monitoring the 541 nm emission. The lifetime of terbium emission in the TbHL film is 0.60 ms, which is shorter than that in the Gd 0.9 Tb 0.1 HL film (0.69 ms) (Fig. S3, ESI †). Due to short Tb-Tb distances (4.212 Å and 4.532 Å) in the TbHL film, the energy at the emitting level of the Tb ion can migrate efficiently, increasing the probability of quenching at a defect site. In contrast, in the 'diluted' Gd 0.9 Tb 0.1 HL film the Gd III ions effectively act as insulators, preventing energy migration between Tb ions and thus enhancing the lifetime of Tb emission.
To evaluate the potential use of the Gd 0.9 Tb 0.1 HL film as a ratiometric thermometer, temperature-dependent emission spectra were recorded. As the temperature increases from 110 to 270 K, the intensity of the Tb III -based emission changes only slightly. However, the intensity of the ligand-based phosphorescence decreases dramatically with increasing temperature due to the thermal activation of non-radiative decay pathways (Fig. 4a and Fig. S4, ESI †). The different responses of the two kinds of emission to changes in temperature make this material a good candidate for ratiometric temperature sensing.
We define the thermometer parameter y as the ratio between the intensities I 541nm (Tb, 5 D 4 -7 F 5 , 541 nm) and I (phos+Tb) (the total emission intensity from 350-650 nm). A good linear  relationship was found in the temperature range of 110-250 K according to eqn (1), with a correlation coefficient R 2 = 0.994 (Fig. 4b).
The thermometer performance is evaluated by the relative sensitivity (S r ), defined by eqn (2).
The relative sensitivity of our thermometer film is up to 0.8% K À1 at 110 K (Fig. 4b). A comparison of the sensitivity of the ratiometric thermometer in this work with other reported materials is given in Fig. S5 (ESI †).
The accuracy and precision are other two important parameters to evaluate the performance of a thermometer. The accuracy is related to the correlation coefficient of the fitting curve. The standard deviation of the calibration curve is 0.0057 and the temperature precision is AE3.2 K based on eqn (1). The luminescence emission colour change of the Gd 0.9 Tb 0.1 HL film from 110 to 250 K has been visualized in a CIE (Commission International d'Eclairage) chromaticity diagram (Fig. S6, ESI †). The CIE coordinates at different temperatures as calculated from the emission spectra are provided in Table S1 (ESI †). The emission colour changes from blue-green at 110 K to green at 250 K.
The stability of the film was tested by exposing the sample to temperature cycles from 110 to 250 K for four times which proved it to be rather robust (Fig. S7, ESI †). After the low-temperature luminescence measurements, PXRD was measured again to confirm the stability of the crystal phase (Fig. 1).
As stated in the introduction, the composition and properties of a luminescence thermometer based on Ln MOFs can be varied easily. As a proof of principle another MOF film was prepared; it appeared that lowering the Tb content to approximately 1% (Gd 0.99 Tb 0.01 HL) resulted in further improvement of the performance ( Fig. S8 and S9, ESI †). The temperature relationship can be fitted with an exponential curve, with a relative sensitivity of 1.7% K À1 at 240 K up to 4.4% K À1 at 110 K. It thus appears that with a higher content of Gd the material becomes more sensitive, however, an even lower concentration of Tb will make the Tb emission too weak which will result in increased errors in the measurements.
In summary, for the first time lanthanoid MOF films were synthesized by a direct solvothermal method onto a Gd 2 O 3 substrate. Surface Gd ions from the Gd 2 O 3 substrate act as nucleation sites for the growth of the MOF and thereby assist in the formation and improve the quality of the Ln MOF. This new method unlocks a promising route to the synthesis of a wide range of Ln MOF films. The Gd 0.9 Tb 0.1 HL film was shown to be a potential thermometer for use in the temperature range of 110 to 250 K, with a relative sensitivity up to 0.8% K À1 , whereas the compound Gd 0.99 Tb 0.01 HL with a lower Tb content resulted in a relative sensitivity up to 4.4% K À1 at 110 K.  X. Liu gratefully acknowledges a grant from the Chinese Scholarship Council (no. 201206250014). We are grateful to Dr Hadi Arjmandi-Tash for his assistance with the SEM measurements. We thank Dr Hong Zhang and Dr Pengtao Jing (University of Amsterdam) for lifetime measurements.