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• W2004669976 abstract "Dynamic spatial control of MOF position is obtained by incorporating carbon-coated cobalt nanoparticles within metal organic framework (MOF)-5 crystals. The cobalt framework composite obtained responds efficiently to magnetic stimuli. A luminescent functionality is added, showing that multifunctional MOF devices can be prepared. This new generation of adaptive material is tested as a position-controlled molecular sensor. Metal organic frameworks (MOF) are very promising ultraporous materials for a variety of applications, including sensing,1 detecting,2 gas storage and separation,3, 4 catalysis,5 and drug delivery.6 The high surface area in the thousands of square meters per gram, and the controlled pore size and pore size distribution of MOFs are relevant features for the fabrication of devices that rely on materials with highly controlled transport properties. In addition, recent investigations describe MOFs as adaptive materials1, 7 because they respond to a variety of stimuli (e.g., molecular and environmental).8 Despite the interesting intrinsic properties of these ultraporous materials, different strategies are currently under investigation to achieve spatial control of MOF position on a variety of substrates. The different proposed routes involve controlled crystal sizes for subsequent growth,9 surface functionalization,10 soft lithography,11 and seeding approaches through heterogeneous nucleation.1 This latter approach has been shown to allow exogenous functionality to be coupled with the properties intrinsic to MOFs. In the present study we utilize functionality gained through synthesis of MOF with magnetic nanoparticles to control the location of MOF crystal growth and to dynamically position 3D MOF forms for use in reconfigurable engineering devices. Once one or more exogenous species are embedded in the MOF crystals, a framework composite (FC) is obtained.1 Because of the exciting potential properties, the recent research trend has focused on the synthesis of the nanospecies into preformed MOF crystals. A variety of FCs, mainly based on metallic inclusions, has been reported. Fischer's group used chemical vapor deposition to grow a variety of metallic nanoparticles (e.g., Pd, Au, and Cu) inside the MOF lattice.12, 13 AgS-like compounds and TiO2 particles have been grown inside the porous framework as well.14, 15 Alternatively, MOFs have been used as templates for the preparation of silica nanoparticles.16 The route involving MOF preparation and the subsequent growth of nanoparticles in the frameworks is a two-step approach in which not all kinds of particles can be synthesized because of the need for chemical vapor deposition precursors. Furthermore, not all of the precursors can be used because their chemical compatibility with the MOF network is a prerequisite. In addition it is difficult to achieve spatial control of the nanospecies growth within the MOF crystals.17 Thus several limitations have been identified related to the post-impregnation route and the achievable properties of the final FC. Recently, Amelot and co-workers18 presented an innovative two-step route to induce Ag nanoparticle formation directly within a single MOF-5 crystal. Using a solution containing the proper precursors, a lithographic protocol was used to spatially control metallic particle formation inside the MOF. In their study, the MOF crystal was impregnated with a silver nitrate solution and then lithographed. This approach opens new routes for FC engineering and spatial control of active species within photocatalytic MOFs. An alternative and emerging strategy for FC fabrication is to use the nanomaterial already prepared, and then add the nanospecies to the MOF growing medium in order to fabricate FC in a one-pot approach. This route allows for the practical use of any presynthesized material compatible with the solvent involved in the MOF synthesis. For example, silica particles prepared using an inexpensive soft chemistry method can be embedded in MOF-5, offering a faster route for MOF preparation due to the seeding effect in solution or on surfaces.19 Although the silica particles employed present just a seeding effect, other ceramic particles can be used to simultaneously increase the MOF production rate or, if these particles are deposited on a surface, they can be used to induce MOF growth in controlled locations.1 Using recently discovered nanoflaked α-hopeite microparticles (called DRMs), spatially controlled positioning of MOF-5 within lithographed substrates was demonstrated. These ceramic seeds can be decorated with a variety of functional materials allowing for the preparation of a new generation of molecule-selective active devices.1 This route represents a new straightforward synthetic approach that could revolutionize the fabrication of MOF-based devices for a number of applications such as catalysis, optics, and sensing. The proper choice of the functional extrinsic material is critical for the preparation of new efficient MOF-based devices with tailored properties. For example, the control of the crystal position using an external stimulus might be of high technological interest for applications such as dynamic filters where the MOF is needed in an “on” or “off” position to selectively gate a channel. An effective route is a one-pot approach where precursors with magnetic properties are utilized in the MOF synthesis. Traditionally, the strategy employed for the preparation of MOF with magnetic properties involves precursors of elements with magnetic properties (e.g., Mn, V, and Co) assembled with organic linkers in a framework that presents a magnetic response;20-23 however, no evidence for the control of the crystal position using an external field has been reported. In the recent work of Lohe et al.7 the possibility to functionalize aluminum- and copper-based MOFs using extrinsic superparamagnetic nanoparticles (γ-Fe2O3) is explored. The procedure involves a two-step synthesis: the MOF precursors are first grafted on the magnetic particle surface; the particles are then used to grow the MOFs. Application of an alternating magnetic field is used to vary the temperature of this magnetic FC highlighting the application of these FCs for controlled drug release. However additional unexplored advantages can be offered by such an interesting class of FC. Position-guided sensors or gates and new routes for patterning MOF-based devices can take advantage of controlling MOF positions using an external field. Therefore, depending on the application, different magnetic properties can be preferred. Here we present a straightforward one-pot protocol to embed carbon-coated cobalt nanoparticles within zinc-based metal organic frameworks. The choice of the magnetic particle is due to the large-scale production of these nanomagnets with high air and thermal stabilities.24 As Grass et al. have reported, the carbon coating improves the magnetic properties.23 In addition, the compatibility of MOF-5 with carbon-based materials has been already demonstrated.25-27 Therefore we considered such particles as ideal candidates for the preparation of ferromagnetic FCs. With this approach we demonstrate some advantages provided by the use of an external field to control the position of MOF-5 crystals embedding a small amount of magnetic nanoparticles in the framework. The presented recipe involves the addition of carbon-coated cobalt nanoparticles and a surfactant (Pluronic F127) in the MOF-5 growing medium, followed by classical solvothermal synthesis. The clouds of surfactant embed the magnetic nanoparticles, avoiding premature sedimentation of the functional nanospheres. After 24 h of thermal treatment, dark crystals are obtained. Cubic shape of the synthesized crystals is detected, similar to the shape of the MOF-5 control sample. An optical microscopy image of the magnetic FC shows cobalt clusters evenly distributed inside and outside the crystals (see Figure S1, Supporting Information). Solvent exchange was performed, removing the original precursor solution with fresh dichloromethane (this process was repeated 5 times). With this procedure unembedded Co particles were efficiently removed and the original solvent was substituted. Dried Co FC crystals appear dark blue in color while regular MOF-5 crystals are white (see Figure S2, Supporting Information). This color is a clear indication that cobalt species are embedded in the porous framework. By inductively coupled plasma optical emission spectroscopy (ICP-OES) analysis performed on Co FC crystals, 197 mg g−1 of Zn and 4.4 mg g−1 of Co have been measured. This corresponds to a volume concentration of 0.052% of Co nanoparticles within each MOF-5 crystal, calculated using the size and the density of the Co particles, as well as of MOF-5. From the optical microscopy investigation, clusters of metal nanoparticles are detected. An elemental mapping using particle induced X-ray emission (PIXE) confirms an inhomogeneous distribution of the magnetic material inside MOF crystals detecting micrometer-sized domains of cobalt clusters (Figure S3, Supporting Information). Using scanning electron microscopy (SEM) we investigated the morphology of the Co FC crystals. The cubic crystal faces (Figure 1a) are decorated with clusters of micrometer and sub-micrometer size (Figure 1b). Performing an energy dispersive X-ray (EDX) analysis, these clusters present an intense signal of cobalt (Figure 1c). Cobalt Lα, Kα, and Kβ emissions are detected at 0.776, 6.929, and 7.648 keV, respectively. The signals of the elements constituting MOF-5 are detected: carbon (Kα, 0. 277 keV), oxygen (Kα, 0.523 keV) and zinc (Lα, 1.012 keV; Kα, 8.637 keV; Kβ, 9.53 keV). An iridium signal (Mα, 1.978 keV) is also detected because an iridium target was used to deposit a conductive thin metal coating on top of the sample in order to collect the SEM images. We used a 30 keV electron beam for 6 min in order to generate a crack on the top surface of the Co FC crystal (Figure 1d) with a crack width of 1.65 μm (Figure 1e). This crack dimension was large enough for an EDX measurement inside the crystal framework. The collected spectrum is presented in Figure 1f. Although the cobalt signal is less intense than the one recorded on the surface, it proves that the cobalt nanoparticles were also embedded within the MOFs. SEM characterization of the carbon-coated cobalt nanoparticle doped MOF-5 framework composite (Co FC). a) SEM image of a Co FC crystal. Similar to MOF-5 the Co FC crystals have a cubic shape. X-ray diffraction confirms the typical pattern of MOF-5 for both control and Co FC samples (see Supporting Information, Figure S4). b) SEM image of the Co FC surface which highlights the presence of clusters. c) EDX analysis of the cluster inside the dashed square presented in (b). A strong signal of Co (Lα, Kα, Kβ) is detected in the EDX spectra. d) SEM image of the same Co FC crystal presented in (a) after focusing a 30 keV electron beam on a 2 μm × 2 μm area for 6 min. The crack induced by the electrons is highlighted in the dotted square. e) Close-up of the crack presenting the area in which an EDX measurement has been performed (continuous line contoured square). f) EDX spectra related to the previous figure. Cobalt signal is detected inside the crack. The magnetic characterization presented in Figure 2a has been performed on undoped MOF-5 and shows a diamagnetic response in the scanned field range. On the other hand, a strong ferromagnetic response (150 emu g−1 at saturation) has been measured on a pure Co nanoparticle sample (Figure 2b). Finally, the Co FCs present a magnetic response, which is the overlap of the paramagnetic behavior of the porous framework and the magnetization properties of the metallic nanoparticles. A saturation value of 0.8 emu g−1 is measured for the Co FCs (Figure 2c). Magnetization curves of a) MOF-5, b) cobalt nanoparticles, and c) carbon-coated cobalt-nanoparticle-doped MOF-5 framework composite (Co FC). The magnetic response is strong enough to allow control of the Co FCs position using a magnetic field. A 4 mL vial containing washed dark blue Co FC crystals in dichloromethane has been vigorously stirred and a magnet has been put in contact with the vial. The cobalt-doped MOFs accumulate at the glass surface where the magnetic field is most dense (close to the magnet tip) as shown in Figure 3a. Figures 3b,c show the quick removal of the magnet. Because of the removal of the magnetic field, the crystals slide along the glass surface (Figure 3d) falling down onto the bottom of the glass (Figure 3e) and then lying in the lower part of the sealed vessel (Figure 3f). The sequence of frames represents the experimental evidence of the Co FC response to the magnetic field. Using the magnetic field as an external stimulus, the position of the FC can be statically or dynamically controlled opening new prospects in the field of MOF based devices. Despite the fact that the carbon coated magnetic particles are bigger than the MOF-5 pore diameter, the Brunauer–Emmett–Teller (BET) surface area is 2282 m2 g−1 (see Figure S5, Supporting Information). The control sample, prepared in similar conditions without adding cobalt nanoparticles and surfactant, presents a surface area of 2376 m2 g−1. These results indicate that the introduction of the Co nanoparticles provokes a surface area loss of 4%. The magnetic MOFs presented in this work have the highest surface area reported thus far. Effect of a magnet on the carbon-coated cobalt-nanoparticle-doped MOF-5 framework composite (Co FC). After stirring the solution containing Co FCs a significant proportion of crystals are collected by the magnet. Removing the magnet, the crystals slide down to the bottom of the vial. A possibility offered by controlling the position of such ultraporous crystals is presented in Figure 4. Here, two magnetic bars have been inserted in a 1 mm glass capillary (Figure 4a). This custom-made magnetic finger was used to collect washed Co FCs. The crystals preferentially accumulate close to the extremities of the two magnets. The finger with the magnetic MOFs was subsequently introduced into a new MOF growing medium to promote further crystal growth. After 48 h, the subsequent growth due to the seeding effect of the original Co FC crystals was interrupted. Crystals were then immersed in a solution with tetrahydrofuran (THF) containing a dye (fluorescein isothiocyanate, FITC). After 3 h the color of the crystals turned to orange (Figure 4b). The original contour of the dark crystals can be appreciated and the subsequent growth can be observed as well. The magnetic-dye-doped crystals under UV irradiation are luminescent, and the typical cubic MOF-5 shape can be detected (Figure 4c). In Figure 4d a SEM image taken of the same sample is presented. The image shows interpenetrated crystals with dimensions up to 20 times the original magnetic seed crystal sizes. The crystals attached to the magnetic finger were dried under vacuum and detached from the substrate. The ring of Co FC crystals could then be moved along the glass capillary by moving the magnetic field (Figure 4e,f). Scheme showing the magnetic finger used to position Co FCs and the results obtained with further growth of MOF-5 crystals. a) Two magnetic bars have been inserted in a 1 mm capillary. The magnetic finger was then used to collect Co FCs. The magnetic composite crystals are preferentially positioned to where the magnetic field lines are most dense. b) Picture under visible light of the positioned Co FCs that act as seeds for the further growth of the Co FC performed in a MOF-5 growing medium for 48 h. The crystal clusters are then doped with fluorescein isothiocyanate. The impregnation process turns the crystals to orange. c) Picture under UV light (365 nm) of the dye-doped crystal clusters. This picture highlights the contour of the cubic crystals. d) SEM image of the crystal clusters (scale bar 200 μm). This image shows interpenetrated crystals due to the growing process when leaving the Co FC crystals in the MOF-5 precursor solution at 95 °C for 48 h. e) After drying the crystals from the solvent the position of ring of MOF located between the magnetic bars was reconfigurable using the magnetic bars, as presented in the sequence (e–h). These experiments demonstrate that by the preparation of this active FC it is possible to control the position of isolated crystals or to induce the formation of interpenetrated MOF forms in specific locations using an external stimulus. Both of these systems might be useful for a variety of applications and the one we propose here is an amine sensor. Using a magnetic finger, the Co FCs were positioned to fabricate a sensor device comprised of a localized cluster of functionalized MOF crystals. The magnetically positioned FITC impregnated Co FCs were used for rapid detection of primary amines (e.g., phenyl-diamine). The dimension of this molecule ensures that it can diffuse inside the framework and react with the isothiocyanate group of the dye. In Figure 5a a real-time photoluminescence measurement is presented. The initial luminescence of the dye-doped Co FCs dramatically drops after the injection of the diamine. A small shift to lower wavenumbers is detected as well. In Figure 5b the trend of the intensity at 550 nm is reported. Within 4 min a 50% intensity decrease is detected, and in 12 min the intensity loss is 75%. An overall loss of about 88% is detected after 60 min and no further significant decrease was detected. For the first time magnetic and optical properties have been combined in a MOF for the fabrication of a sensor for primary amine detection. The application of position-controlled bi-functional FC can hold great potential for lab-on-chip devices, which enable fast detection with only small reaction volumes. In such smart platforms, MOF nanoreactors can be precisely driven across the microfluidic chip using an external magnetic field. Real-time luminescence response of a bifunctional framework composite to a primary amine. a) Luminescence spectra of dye-doped Co FCs collected every 2 min in the 450–750 nm region after the addition of a dilute 1,4-diaminobenzene solution. b) Intensity of luminescence of dye-doped Co FCs at 550 nm with time. The combination of multiple stimuli (magnetic, optical) allows for positioning control and molecular detection, thereby opening new frontiers for adaptive MOF-based devices. Using the presented Co FC, spatially controlled growth of MOF-5 crystals using a magnetic field is now possible. Furthermore the surface area is not significantly affected by the metal nanoparticles embedded in the framework. The combination of the magnetic features with luminescent properties allows for the fabrication of a new generation of multistimuli multiresponse MOF-based materials. A new straightforward synthesis in now available for the fabrication of a new generation of adaptive dynamically reconfigurable MOF-based devices. Carbon-coated cobalt nanoparticles, Zn(NO3)2, 1,4-benzenecarboxylic acid (BCA), N-diethyl formamide (DEF), Pluronic F-127, fluorescein isothiocyanate (FITC), and 1,4-diaminobenzene were purchased from Aldrich and used as-received. MOF-5 growing medium was synthesized by dissolving 0.15 g of Zn(NO3)2 and 0.0127 g of BCA in 4 mL of DEF. The 4 mL sealed vial was sonicated for 15 min. 0.2 g of Pluronic F127 and 0.016 g of Co nanoparticles were added and sonicated for another 10 min. 20 vials (4 mL each) were prepared to obtain Co FC and 20 vials were filled with MOF-5 growing medium solution to prepare an equivalent number of control samples. The Co FC crystals and control sample (regular MOF-5) were collected after 24 h of growth at 95 °C. The samples were stored, prepared and measured using dry inert gases. Magnetic Co FCs crystals were washed 5 times with dichloromethane (DCM) to remove the original DEF used in the zinc-based framework crystal preparation. THF was then used to wash the crystals twice. The vessels containing the crystals in THF were introduced into a vacuum chamber for 5 min to ensure the extraction of DCM from the framework. The procedure was conducted in a dry air atmosphere, and the samples were kept under nitrogen. The magnetic measurements have been performed using a Physical Properties Measurement System (PPMS) Model 6000, Quantum Design (qdusa.com). The instrument is equipped with a 9 T superconducting magnet. For the measurements of the hysteresis an ACMS probe (magnetometer) was employed. The “DC Extraction method” was used to perform the measurements. The magnets of two Teflon-coated magnetic stirrers (Spinbar, 7 mm × 4 mm) were removed from their plastic capsules and introduced into a 1 mm glass capillary (Capillary Tube Suppliers Ltd). The magnetic finger was used to collect and position the Co FC crystals and then introduced into a fresh MOF-5 growing medium. For the preparation of dye-doped Co FC, fluorescein isothiocyanate (FITC) powder (15 mg) was dissolved in 4 mL of THF. The Co FC crystals were added to the dye–THF solution. After 3 h the crystals turned orange and were subsequently washed 3 times using fresh THF. Under UV irradiation the dye-doped Co FCs presented strong yellow-green emissions. Time-resolved luminescence emission tests were performed recording the evolution of the emission intensity at 550 nm. The values were recorded continuously before and after the injection of the amino molecules over a 2 min time lapse. 1 min after the continuous acquisition was started, 20 μL of a diluted diaminobenzene solution (20 μL of diaminobenzene 98% in 1.5 mL THF) was added to the FITC-doped Co FC immersed in 3 mL of THF; the measurement was then continued for about 2 h. The reaction between the amino group and the FITC is illustrated in previous works.28 Supporting Information is available from the Wiley Online Library or from the author. Dr. Kristina Konstas is acknowledged for the help with BET sample preparation and Dr. Matthew Hill for helpful discussions on the BET analysis. Dr. Laura Villanova is acknowledged for data elaboration and graphics using R software. Dr. John Ward and Dr. Mark Greaves are thanked for their expert assistance with the SEM. Dr. Benedetta Marmiroli and Dr. Fernando Cacho-Nerin are acknowledged for helpful discussions. D.B., P.F., C.M.D., and A.J.H. acknowledge the CSIRO OCE Science Leader Scheme for support. D.B. acknowledges the Australian Research Council for support through the APD grant DP0988106. The authors thank the director of the CSIRO Computational and Simulation Sciences Transformational Capability Platform for financial support. The powder diffraction characterization was performed at the SAXS beamline of Elettra Synchrotron, Trieste, Italy. Detailed facts of importance to specialist readers are published as ”Supporting Information”. Such documents are peer-reviewed, but not copy-edited or typeset. They are made available as submitted by the authors. Please note: The publisher is not responsible for the content or functionality of any supporting information supplied by the authors. Any queries (other than missing content) should be directed to the corresponding author for the article." @default.
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• W2004669976 title "Dynamic Control of MOF-5 Crystal Positioning Using a Magnetic Field" @default.
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• W2004669976 cites W1975386163 @default.
• W2004669976 cites W1979400492 @default.
• W2004669976 cites W2002449355 @default.
• W2004669976 cites W2004550299 @default.
• W2004669976 cites W2009806571 @default.
• W2004669976 cites W2011012000 @default.
• W2004669976 cites W2022085591 @default.
• W2004669976 cites W2023058711 @default.
• W2004669976 cites W2025044983 @default.
• W2004669976 cites W2036246518 @default.
• W2004669976 cites W2044491102 @default.
• W2004669976 cites W2067181536 @default.
• W2004669976 cites W2073681157 @default.
• W2004669976 cites W2085749597 @default.
• W2004669976 cites W2095853776 @default.
• W2004669976 cites W2099486431 @default.
• W2004669976 cites W2100466426 @default.
• W2004669976 cites W2136094441 @default.
• W2004669976 cites W2139248937 @default.
• W2004669976 cites W2151042553 @default.
• W2004669976 cites W2152846900 @default.
• W2004669976 cites W2153562084 @default.
• W2004669976 cites W2164031809 @default.
• W2004669976 cites W2335010051 @default.
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