This work was sponsored by the Chemical Sciences, Geosciences and Biosciences Division, Office of Basic Energy Sciences, Office of Science, U.S. Department of Energy, grant no. DE-FG02-12ER16352. S.T.H. thanks the National Science Foundation for financial support through the National Science Foundation Graduate Research Fellowship under Grant No. 1122374.

1. Synthesis of Silica-encapsulated Monometallic or Bimetallic Metal Oxide Nanoparticles
<ol>
	<li>Prepare the reverse microemulsion
	<ol>
		<li>Add 240 ml of anhydrous n-heptane to a clean, oven-dried 1 L round bottom flask (RBF) containing an oven-dried magnetic stir bar using a clean, oven-dried graduated cylinder.</li>
		<li>Add 54 ml of polyoxyethylene (4) lauryl ether to the n-heptane under constant stirring. 
		Note: Because of the high viscosity and low surface tension of this surfactant, a clean, dry 60 ml syringe should be used to obtain accurate volumes instead of a graduated cylinder.</li>
		<li>Add 7.8 ml of ultrapure, deionized (DI) water under constant stirring using a pipette. Seal the RBF with a rubber stopper and Parafilm wax. Let the RME mix for at least 10 min.</li>
		<li>Add 0.1 to 0.5 ml of reagent-grade NH4OH to the emulsion if it is desired to reduce the hydrolysis time. 
		Note: Some metal alkoxide precursors hydrolyze slowly at neutral pH. Let the RME mix for at least another 10 min after adding NH4OH. As a representative example, adding 0.5 ml of NH4OH is recommended for syntheses involving titanium (IV) isopropoxide.</li>
	</ol>
	</li>
	<li>Prepare a metal alkoxide precursor, alcohol, and n-heptane solution
	<ol>
		<li>Connect a clean, oven-dried 250 ml RBF to a Schlenk line and flush with nitrogen. Alternatively, place the clean, oven-dried 250 ml RBF into a dry nitrogen glovebox.</li>
		<li>Add 12 ml of 5% w/v tungsten isopropoxide (WIPO) in isopropanol using a clean, dry syringe. At this stage, other metal alkoxides can also be added, such as tantalum (V) isopropoxide (TaIPO), molybdenum (V) isopropoxide (MoIPO), niobium (V) isopropoxide (NbIPO), titanium (IV) isopropoxide (TiIPO), nickel (II) methoxyethoxide (NiMEO), cobalt (II) isopropoxide (CoIPO), etc. 
		Note: Metal alkoxides can be purchased commercially or synthesized by the addition of an anhydrous alcohol to the corresponding metal chloride salt using a Schlenk line as described elsewhere (Caution: metal alkoxide synthesis from the metal chloride releases gaseous HCl and must be performed in a well-ventilated fume hood).27</li>
		<li>Using a clean, oven-dried cannula, transfer 120 ml of anhydrous n-heptane to the 250 ml RBF containing the metal alkoxide solution</li>
	</ol>
	</li>
	<li>Using a clean, oven-dried cannula, transfer the metal alkoxide-alcohol-n-heptane solution into the RME under constant stirring over the span of 10 min. 
	Note: For metal alkoxides that react vigorously with water, such as tellurium (IV) isopropoxide, a much slower drop-wise rate of addition is required. The final solution should be optically clear regardless of the metal alkoxide precursor used, but can be various colors depending on the metal alkoxides used and their oxidation states. We note that whether the emulsion is transparent or translucent is dependent on particle size while the color is dependent on metal oxidation state.</li>
	<li>After 4 hr, use a clean, dry syringe to inject 1.4 ml of reagent-grade NH4OH into the solution dropwise. Then, using another clean, dry syringe, inject 1.2 ml of reagent-grade tetraethyl orthosilicate (TEOS) dropwise. 
	Note: Sodium hydroxide (NaOH) should not be used as it can lead to densification of the silica shells during carburization/nitridation and result in sodium impurities in the lattice of the final nanoparticles. Residual NH4OH on the other hand conveniently decomposes during the heat treatments.</li>
	<li>After 16.5 hr, remove the rubber stopper and use a clean, dry graduated cylinder to add 300 ml of methanol to the solution under constant stirring.</li>
	<li>After 10 min of stirring, remove the stir bar and allow the solution to settle. 
	Note: There will be two liquid phases present: a heptane-rich upper phase and a methanol-rich lower phase. The silica-encapsulated metal oxide nanoparticles, designated as SiO2/MOx will sediment to the bottom of the flask from the lower phase.</li>
	<li>After 1 hr, decant the liquid phases into an organic waste container and collect the solid phase SiO2/MOx in clean 50 ml centrifuge tubes. 
	Note: if polypropylene or polystyrene centrifuge tubes are being used, the precipitant cannot be stored long-term in this state as the residual heptane will slowly dissolve the centrifuge tube, causing it to elongate. Furthermore, residual NH4OH and TEOS can cause the SiO2 to continue to grow beyond what was desired.</li>
	<li>Centrifuge the SiO2/MOx phase at 2,056 x g for 5 min, then decant the supernatant into an organic waste container.</li>
	<li>Add 10-30 ml of acetone to each 50 ml centrifuge tube and disperse the powder into the acetone by shaking or sonicating. This helps remove excess surfactant before calcination.</li>
	<li>Centrifuge the SiO2/MOx and acetone mixture at 4,626 x g for 10 min and then decant the supernatant into an organic waste container. Allow the SiO2/MOx gel to dry overnight.</li>
</ol>
2. Heat Treatment of the Synthesized Powder
Caution Statement: Hydrogen, methane, and ammonia gas are extremely flammable. Ammonia gas is toxic. A thorough leak-check should be performed before all heat treatments, and the treatments should be performed in quartz-tubular furnace kept in a well-ventilated fume hood with an oil bubbler at the gas outlet. All gas cylinders should be equipped with flame arrestors and stored away from the furnace. If required by law or institutional regulations, excess ammonia gas should be bubbled through a large volume of water and either discarded as base waste or neutralized to pH 7 ammonium chloride solution using HCl.
<ol>
	<li>Calcination of the SiO2/MOx powder in air
	<ol>
		<li>Crush the dried SiO2/MOx gel into a fine powder using a glass stir bar or mortar and pestle. Put the powder in alumina crucible boats and load into a quartz-tube furnace.</li>
		<li>Using a 2 &#176;C/min heating rate, calcine the SiO2/MOx powder under 100 sccm of air at 450 &#176;C for 1 hr. This removes any residual surfactant and also increases the microporosity of the silica shells. After the furnace has cooled, remove the calcined SiO2/MOx powders and store in ambient conditions.</li>
	</ol>
	</li>
	<li>Carburization of the SiO2/MOx powder in a methane/hydrogen atmosphere
	<ol>
		<li>Load the calcined SiO2/MOx powder into an unglazed alumina crucible boat and place into a quartz-tube furnace. Flush the quartz-tube furnace with nitrogen for at least 30 min to remove oxygen. Perform a leak check by spraying all joints with soapy water.</li>
		<li>Using a 2 &#176;C/min heating rate, carburize the SiO2/MOx powder under 120 sccm of hydrogen and 33 sccm of methane at 850 &#176;C for 4 hr to form SiO2/MCx.</li>
		<li>After 4 hr, stop the flow of methane and hold the powder at 850 &#176;C for 1 hr in just 120 sccm of hydrogen to scavenge any excess surface carbon.</li>
		<li>Allow the furnace to slowly cool to room temperature under 120 sccm of hydrogen. Then, flush the furnace with nitrogen for at least 30 min to remove hydrogen.</li>
		<li>Flow 95 sccm of nitrogen and 5 sccm of air over the powder for 3 hr to slowly passivate the carbides before exposure to air.</li>
		<li>Remove the SiO2/MCx powder from the furnace and store in a vacuum dessicator or in a dry nitrogen glovebox to prevent long-term bulk oxidation of the metal carbide nanoparticles in air.</li>
	</ol>
	</li>
	<li>Nitridation of the SiO2/MOx powder in an ammonia atmosphere
	<ol>
		<li>Load the calcined SiO2/MOx powder into an alumina crucible boat and place into a quartz-tube furnace.</li>
		<li>Flush the quartz-tube furnace with nitrogen for at least 30 min to remove oxygen.</li>
		<li>Using a 2 &#176;C/min heating rate, nitridize the SiO2/MOx powder under 100 sccm of ammonia at 800 &#176;C for 4 hr to form SiO2/MNx.</li>
		<li>Allow the furnace to slowly cool to room temperature. Then, flush the furnace with nitrogen for at least 30 min to remove ammonia.</li>
		<li>Flow 95 sccm of nitrogen and 5 sccm of air over the powder for 3 hr to slowly passivate the nitrides before exposure to air.</li>
		<li>Remove the SiO2/MNx powder from the furnace and store in a vacuum dessicator or in a dry nitrogen glovebox to prevent long-term bulk oxidation of the metal nitride nanoparticles in air.</li>
	</ol>
	</li>
</ol>
3. Removing the Silica Shells and Supporting the Nanoparticles
Caution Statement: ammonium bifluoride (ABF) is highly toxic. It should only be handled in a well-ventilated fume hood using proper personal protective equipment, including butyl-rubber gloves, a face shield, and an HF-resistant labcoat with HF-resistant sleeves. Glass and metal lab equipment should never be used when handling ABF.
<ol>
	<li>Silica Dissolution in Ammonium Bifluoride for Acid-Stable Metal Carbides and Nitrides (such as WC and W2N)
	<ol>
		<li>Weigh out 200 mg of SiO2/MCx or SiO2/MNx and put in a 30 ml sealable polypropylene container with a Teflon-coated magnetic stir bar.</li>
		<li>If it is desired to support the nanoparticles on a high surface area catalyst support, such as carbon black or carbon nanotubes, weigh out the material and add it to the sealable polypropylene container. 
		Note: The mass weighed out will depend on the desired loading of nanoparticles on the support. For catalyst supports that are not stable in ABF, such as alumina, the support can be added after the silica has been removed and the ABF is neutralized. If no support is added, a nanodispersion will be obtained.</li>
		<li>Add 20 ml of ultrapure DI water and begin mixing to form a suspension. Alternatively, add 20 ml of pre-made 20 wt% ABF solution.</li>
		<li>Weigh out 5 g of ABF and then add to the stirring mixture. Once added, seal the polypropylene container. 
		Note: Dissolution of ABF in water is endothermic, so the temperature of the solution will drop.</li>
		<li>To ensure complete dissolution of the silica and good dispersion of the nanoparticles on the catalyst support, stop the reaction after 16 hr by adding reagent-grade NH4OH dropwise to neutralize the ABF solution to a pH of 6-7. Caution: this reaction is exothermic.</li>
		<li>Empty the neutralized mixture into a centrifuge tube and centrifuge at 2,056 x g for 10 min.</li>
		<li>Empty the supernatant into an alkaline waste container (to ensure total neutralization) and redisperse the catalyst powder in 20 ml of ultrapure DI water.</li>
		<li>Centrifuge at 4,626 x g for 10 min, discard the supernatant, and do one final 20 ml DI water rinse. Up to 12,850 x g may be required for unsupported nanoparticles.</li>
		<li>Dry the powder under vacuum and then store in a vacuum dessicator or a dry nitrogen glovebox to prevent long-term bulk oxidation of the metal carbide or nitride nanoparticles.</li>
	</ol>
	</li>
	<li>Silica Dissolution in Sodium Hydroxide for Alkaline-Stable Carbides and Nitrides (such as TaC and Ta3N5)
	<ol>
		<li>Weigh out 200 mg of SiO2/MCx or SiO2/MNx and put in a 50 ml glass RBF with a magnetic stir bar. Weigh out and add a catalyst support if desired.</li>
		<li>Add 30 ml of at least 0.1 M aqueous NaOH solution. Attach a condenser to the RBF or seal with a rubber stopper and Parafilm wax.</li>
		<li>Heat at 60 &#176;C under constant stirring for 16 hr. After cooling, centrifuge the solution at 2,056 x g for 10 min.</li>
		<li>Empty the supernatant into an alkaline waste container and redisperse the catalyst powder in 20 ml of ultrapure DI water.</li>
		<li>Centrifuge at 4,626 x g for 10 min, discard the supernatant, and do one final 20 ml DI water rinse. Up to 12,850 x g may be required for unsupported nanoparticles.</li>
		<li>Dry the powder under vacuum and then store in a vacuum dessicator or a dry nitrogen glovebox to prevent long-term bulk oxidation of the metal carbide or nitride nanoparticles.</li>
	</ol>
	</li>
</ol>

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The authors have nothing to disclose.

A procedure for synthesizing non-sintered, metal terminated transition metal carbide and nitride nanoparticles with tunable sizes and structure is presented here.26 Critical steps in the method include: using a moisture-free RBF to contain the diluted metal alkoxide precursor, avoiding alkali metal impurities during all steps, precipitating the RME with excess methanol as opposed to acetone or isopropanol, performing a proper leak check before carburizing or nitridizing the components, and using proper PPE when working with ammonium bifluoride.
The method can be modified in several areas. The TMO PSD can be adjusted using different RME systems, different water:surfactant ratios, different metal alkoxide:water ratios, different pH values, and different hydrolysis times. The TMCN PSD can be manipulated by manipulating the starting TMO PSD as well as by adding different amounts of NH4OH and TEOS, using different TEOS hydrolysis times, and using different carburization/nitridation temperatures. The crystalline phase-purity of the TMCN NPs can be manipulated using different temperatures and different centerline velocities of the carburizing/nitridizing gases. The composition of the TMCN NPs can be adjusted by using any hydrolysable early transition metal alkoxide, leading to a large array of potential multimetallic TMC and TMN NPs that could be synthesized with this method.
This technique is most suitable for applications of TMC and TMN NPs that require non-sintered particles of finely controlled sizes that also exhibit metal-terminated surfaces. This technique is also suitable for the ease with which a variety of multimetallic TMC and TMN NPs can be formulated. The technique is limited by the thermal stability of the silica coatings. TMC and TMN NPs that require carburization or nitridation temperatures in excess of 1,000 &#176;C likely cannot be synthesized by this method due to the thermal collapse of the silica microporosity at these extreme temperatures. The technique is also limited to TMC and TMN NPs that are stable in either ammonium bifluoride or alkaline solutions as either an acidic or an alkaline treatment is required to remove the silica coatings after carburization/nitridation.
With respect to existing methods to synthesize TMCN NPs, this method is unique in its ability to simultaneously mitigate both particle sintering and excess surface impurity deposition. It is also unique in its versatility for synthesizing a wide array of monometallic and multimetallic TMCN NPs, requiring only that a hydrolysable early transition metal alkoxide precursor can be purchased or synthesized. Although this method is more complex than standard wet-impregnation syntheses, it allows non-sintered and metal-terminated TMCN NPs to be loaded onto a high surface area support at room temperature and at any desired wt% loading. In wet impregnation syntheses, the catalyst supports must be exposed to carburizing conditions, leading to their thermal degradation, and low wt% loadings must be used to mitigate excessive particle sintering.
Future directions after learning this technique include exploration of other multimetallic compositions, other RME or Sol-Gel systems, using ceramic coatings other than silica such as alumina, co-feeding carburization and nitridation gases, and using other reactive gas precursors to make for example borides or phosphides.

Early transition metal carbides (TMCs) are low-cost, earth-abundant materials that exhibit high thermal and electrochemical stability as well as unique catalytic activities.1-3 In particular, tungsten carbide (WC) and molybdenum carbide (Mo2C) have been studied extensively for their catalytic similarities to the platinum group metals (PGMs).4,5 Due to these favorable properties, TMCs have been identified as candidates for replacing expensive PGM catalysts in emerging renewable energy technologies, such as biomass conversion, fuel cells, and electrolyzers.6,7
To maximize catalytic activity, commercial catalysts are almost always formulated as ultrasmall nanoparticles (diameters &#60;10 nm) dispersed on a high surface area support, such as carbon black.8 However, the synthesis of TMCs requires temperatures higher than ~700 &#176;C. This leads to extensive sintering of the nanoparticles (NPs), excess surface carbon deposition (coke), and thermal support degradation. Both particle sintering and support degradation lead to decreased material surface areas. Excess surface impurity deposition blocks active metal sites, which has been shown to greatly reduce or in some instances completely eliminate the catalytic activity of TMCs.9,10 As such, the fundamental study of TMC reactivity is predominantly performed on bulk microparticles or thin films with finely controlled surfaces rather than on high surface area TMC nanomaterials.
Many methods have been developed to synthesize TMC NPs, but these methods are not suitable for synthesizing catalytically active TMC NPs. Traditional wet impregnation techniques use metal salt solutions impregnated on a high surface area support. On heating, wet impregnation methods can expose the catalyst support to destructive carburizing conditions leading to support degradation. Furthermore, sintering can only be mitigated at low wt% loadings of the metal on the support, and it is also not possible to synthesize unsupported TMC nanopowders using wet impregnation. Several newer methods involve mixing a metal precursor with a carbon precursor and applying conventional and unconventional heating techniques.11-18 Excess carbon is used to prevent sintering, but this excess carbon results in extensive surface carbon, making these materials not suitable for catalytic applications.
Due to these synthetic challenges, TMCs have traditionally been studied as co-catalysts11 for PGMs, catalyst supports for PGMs,19-22 or supports for active PGM monolayers.23-25 The method presented here offers the ability to synthesize both non-sintered and metal-terminated TMC NPs as well as transition metal nitride (TMN) NPs with tunable sizes, crystalline phases, and metallic composition.26 The method presented also offers the ability to obtain TMC or TMN nanodispersions or deposit the TMC and TMN NPs on a high surface area catalyst support at room-temperature, thereby mitigating thermal support degradation. This method is therefore suitable for standalone catalytic applications of TMC and TMN NPs, the development of advanced multimetallic TMC and TMN NPs, or other applications requiring finely controlled particle sizes and surfaces.26
The method presented here uses a three step protocol to synthesize TMC and TMN NPs. In the first step, a reverse microemulsion (RME) is used to coat early transition metal oxide (TMO) NPs in silica nanospheres. The emulsion is prepared by dispersing water droplets in a nonpolar medium using a commercial nonionic surfactant. The silica-encapsulated TMO NPs are then subjected to either carburizing or nitridizing heat treatments. Here, the silica prevents particle sintering at high temperatures while allowing the reactive gases to diffuse to the TMO NPs and convert them to TMC or TMN NPs. In the final step, the silica shells are removed using either acidic or alkaline treatment to obtain TMC or TMN nanodispersions that can be dispersed on a high surface area support, such as carbon black.

<table><tbody><tr><td>n-heptane</td><td>Sigma-Aldrich</td><td>246654</td><td></td></tr><tr><td>polyoxyethylene (4) lauryl ether</td><td>Sigma-Aldrich</td><td>235989</td><td>Brij&amp;reg; L4</td></tr><tr><td>tungsten (VI) isopropoxide</td><td>Alfa Aesar</td><td>40247</td><td>W(VI)IPO</td></tr><tr><td>tungsten (VI) chloride</td><td>Sigma-Aldrich</td><td>&lt;a href=&quot;http://www.sigmaaldrich.com/catalog/product/aldrich/241911?lang=en&amp;amp;region=US&quot;&gt;241911&lt;/a&gt;</td><td>To prepare W(VI)IPO, homemade</td></tr><tr><td>tungsten (IV) chloride</td><td>Strem Chemicals</td><td>74-2348</td><td>To prepare W(IV)IPO, homemade</td></tr><tr><td>tantalum (V) isopropoxide</td><td>Alfa Aesar</td><td>&lt;a href=&quot;http://www.alfa.com/en/catalog/40038&quot;&gt;40038&lt;/a&gt;</td><td>Ta(V)IPO</td></tr><tr><td>niobium (V) isopropoxide</td><td>Alfa Aesar</td><td>&lt;a href=&quot;http://www.alfa.com/en/catalog/36572&quot;&gt;36572&lt;/a&gt;</td><td>Nb(V)IPO</td></tr><tr><td>nickel (II) methoxyethoxide</td><td>Alfa Aesar</td><td>42377</td><td>Ni(II)MEO</td></tr><tr><td>titanium (IV) isopropoxide</td><td>Sigma-Aldrich</td><td>&lt;a href=&quot;http://www.sigmaaldrich.com/catalog/product/aldrich/87560?lang=en&amp;amp;region=US&quot;&gt;87560&lt;/a&gt;</td><td>Ti(IV)IPO</td></tr><tr><td>molybdenum (V) isopropoxide</td><td>Alfa Aesar</td><td>&lt;a href=&quot;http://www.alfa.com/en/catalog/39159&quot;&gt;39159&lt;/a&gt;</td><td>Mo(V)IPO</td></tr><tr><td>molybdenum (V) chloride</td><td>Sigma-Aldrich</td><td>&lt;a href=&quot;http://www.sigmaaldrich.com/catalog/product/aldrich/208353?lang=en&amp;amp;region=US&quot;&gt;208353&lt;/a&gt;</td><td>To prepare Mo(V)IPO, homemade</td></tr><tr><td>tetraethyl orthosilicate</td><td>Sigma-Aldrich</td><td>333859</td><td>TEOS</td></tr><tr><td>ammonium hydroxide</td><td>Sigma-Aldrich</td><td>320145</td><td></td></tr><tr><td>methanol</td><td>Sigma-Aldrich</td><td>34860</td><td></td></tr><tr><td>anhydrous isopropanol</td><td>Sigma-Aldrich</td><td>&lt;a href=&quot;http://www.sigmaaldrich.com/catalog/product/sial/278475?lang=en&amp;amp;region=US&quot;&gt;278475&lt;/a&gt;</td><td>To prepare homemade alkoxides</td></tr><tr><td>ammonium bifluoride</td><td>Sigma-Aldrich</td><td>224820</td><td></td></tr><tr><td>carbon black</td><td>Cabot Corp.</td><td>Vulcan&amp;reg; XC72R</td><td></td></tr><tr><td>Methane</td><td>AirGas</td><td>ME R300</td><td></td></tr><tr><td>Hydrogen</td><td>AirGas</td><td>HY UHP300</td><td></td></tr><tr><td>Ammonia</td><td>AirGas</td><td>AM AH80N705</td><td></td></tr><tr><td>Quartz Tube Furnace</td><td>MTI Corp.</td><td>OTF-1200X-S-UL</td><td></td></tr></tbody></table>

reverse microemulsion-mediated synthesis of monometallic and bimetallic early transition metal carbide and nitride nanoparticles

A reverse microemulsion is used to encapsulate monometallic or bimetallic early transition metal oxide nanoparticles in microporous silica shells. The silica-encapsulated metal oxide nanoparticles are then carburized in a methane/hydrogen atmosphere at temperatures over 800 &#176;C to form silica-encapsulated early transition metal carbide nanoparticles. During the carburization process, the silica shells prevent the sintering of adjacent carbide nanoparticles while also preventing the deposition of excess surface carbon. Alternatively, the silica-encapsulated metal oxide nanoparticles can be nitridized in an ammonia atmosphere at temperatures over 800 &#176;C to form silica-encapsulated early transition metal nitride nanoparticles. By adjusting the reverse microemulsion parameters, the thickness of the silica shells, and the carburization/nitridation conditions, the transition metal carbide or nitride nanoparticles can be tuned to various sizes, compositions, and crystal phases. After carburization or nitridation, the silica shells are then removed using either a room-temperature aqueous ammonium bifluoride solution or a 0.1 to 0.5 M NaOH solution at 40-60 &#176;C. While the silica shells are dissolving, a high surface area support, such as carbon black, can be added to these solutions to obtain supported early transition metal carbide or nitride nanoparticles. If no high surface area support is added, then the nanoparticles can be stored as a nanodispersion or centrifuged to obtain a nanopowder.

In the first step of the protocol, the goal is to encapsulate the monometallic or bimetallic transition metal oxide (TMO) NPs within microporous silica spheres. Figure 1 shows images taken of representative syntheses before and after precipitation with methanol. Two reproducible morphological outcomes have been observed during this step that appear to be dependent on the metals used in the synthesis: the TMO NPs can be singly coated with a silica sphere (Figure 2b) or multiple TMO NPs can be coated within a single silica sphere (Figure 2a). Singly-coated TMO NPs have been observed for syntheses using Ti, Ta, and Nb, while multiply-coated TMO NPs have been observed for Mo and W. It is possible to synthesize these metals also in singly-coated formulations by performing the metal alkoxide hydrolysis at elevated pH. Table 1 details results for controlling particle size and composition using the RME. We hypothesize that at elevated pH, the rate of NP growth is higher, and larger NPs can more easily nucleate SiO2 sphere growth (Figure 6c, d). At low pH, certain metal alkoxides hydrolyze very slowly, resulting in ultrasmall TMO nuclei that ultimately become embedded in SiO2 spheres (Figure 6a, b).
The metal composition of the TMO NPs is controlled by the metal alkoxides added to the RME and whether they are mixed together (as presented in the given protocol) or added sequentially. For instance, TaIPO could be mixed with WIPO and heptane before injecting into the RME, or a TaIPO/heptane mixture could be injected into the RME 4 hr after a WIPO/heptane mixture has been injected and allowed to hydrolyze.
Many variables must be considered to control the size of the TMO NPs. The first set of variables is the selection of the surfactant and the oil phase. Here, the water/n-heptane/Brij-L4&#174; system has been chosen due to its wide stability window and the ability to synthesize very small nanoparticles. Alternatively, water/n-heptane/Igepal CO-520&#174; can be used if larger TMO NPs are desired as shown in Figure 3. Alternatively, one can modify the rates of nucleation vs. growth by adding NH4OH to the RME before metal alkoxide addition, resulting in larger NPs as shown in Figure 6c, and d, and&#160; outlined in Table 1. Once the RME system is chosen, the first set of variables controlling TMO size can be grouped together as RME control parameters. These include the water:surfactant ratio, the oil:water ratio, the oil:surfactant ratio, the temperature of the RME, and the extent of convective mixing. These parameters dictate the size of the suspended water droplets, their proximity to one another within the emulsion, their average polydispersity, and the rates of droplet coalescence and separation.
The final set of variables affecting TMO NP size can be classified as metal alkoxide hydrolysis control parameters. These include the metal alkoxide:water molar ratio, the length of time the metal alkoxide is allowed to hydrolyze before initiating the silica coating, the pH of the water droplets, the temperature, and the rate of metal alkoxide addition to the RME system.
Ultimately, the goal of this method is to produce non-sintered and metal-terminated TMC and TMN nanoparticles (referred to as TMCN NPs for convenience). Obtaining this result hinges on synthesizing microporous silica coatings with high thermal stability that also inhibit the sintering of TMC and TMN nanoparticles. To achieve this result, there are two sets of variables that must be considered: control variables affecting the thermal stability of the silica, and control variables affecting the TMCN particle size distribution (PSD).
On heating, microporous silica can transition to dense phases and ultimately to quartz, making it difficult to obtain phase-pure TMCN NPs and can make silica removal more challenging. To maximize the thermal stability of the silica coatings, it has been observed that a high pH is required during TEOS hydrolysis and that the SiO2/TMO NPs should be precipitated from the RME using methanol as opposed to other common precipitating agents such as acetone or isopropanol. Figure 4 shows powder x-ray diffractograms (PXRD) of carburized SiO2/WOx materials with the silica coatings performed at different pH values while Figure 5 shows PXRD diffractograms of carburized SiO2/WOx materials with the silica coatings performed at the same pH but precipitated with three different solvents. TEOS hydrolysis at high pH has been shown to lead to a high number of undercoordinated Q2 and Q3 sites, resulting in a higher micropore volume.28 The influence of the precipitating agent on silica thermal stability is poorly understood but TEM images suggest that flocculation with methanol leads to less aggregated SiO2/TMO flocs as compared with acetone and isopropanol (results not shown). We find support for this hypothesis from TEM images of SiO2/TMO flocs precipitated with less than the recommended amount of methanol in the procedure. For syntheses flocculated with less methanol, the flocs appear more aggregated and the silica is less stable, transitioning to quartz-like domains at lower temperatures than when excess methanol is used during the flocculation step (results not shown).
The TMCN PSD is controlled by the size of the initial TMO NPs as well as the silica nanostructure. In theory, if TMCN sintering can be fully mitigated by the silica shells at carburizing/nitridizing conditions, then the TMCN PSD will be fully controlled by the initial TMO PSD, adjusted by the density difference between the initial hydrated, amorphous TMO lattice and the final crystalline TMC or TMN lattice. Such a result has been closely achieved by using thick silica shells with representative examples shown in Figure 6c, and d.
If sintering is not fully mitigated, then the final TMCN PSD will be controlled by both the initial TMO PSD and the silica coating. This is particularly true for thin silica coatings or for ultrasmall 1-2 nm TMO NPs that can more easily diffuse within the silica coatings. A representative example is shown in Figure 6a and 6b. Here, the same initial 1-2 nm TMO PSD is used, but the silica coating is altered from 50 nm to 35 nm. In the thick silica coating, sintering is mitigated and a 1-2 nm TMC PSD is obtained while in the thin silica coating, sintering is only partially mitigated and a 2-3 nm TMC PSD results. Note that some sintering is present at the surface of silica spheres post-carburization, which we attribute to small surface-bound TMC NPs that can laterally diffuse across the surface of the silica spheres and sinter.
After carburization, it has been observed that for multiply-coated TMCN NPs, the silica coatings remain spherical with minimal sintering of the silica (Figure 6a and 6b). In contrast, for singly-coated TMCN NPs, the silica coatings sinter together (Figure 6c and 6d). We hypothesize that multiply-coated TMCN NPs provide structural integrity to the silica spheres at high temperatures, preventing the sintering of the silica spheres. While this is not the case for singly-coated TMCN NPs, the sintering of the silica spheres has not been observed to inhibit the ability of the silica coatings to both prevent sintering of the TMCN NPs while also allowing carburizing or nitridizing gas molecules to diffuse through them (Figure 6c and 6d). PXRD diffractograms have been included in Figure 8 for various monometallic and heterometallic early transition metal carbide and nitride nanoparticles of various sizes.
Dissolution of the TMCN NPs onto carbon black (CB) leads such as Vulcan XC-72r to well-dispersed, supported NPs. A representative result is shown in Figure 7c. Alternatively, if no support is added, a black nanodispersion suspension is obtained as shown in Figure 7a. Because no surface stabilizing agents are added during or after the dissolution, the TMCN NPs form small aggregates in solution, a representative example of which is shown in Figure 7b.
<table border="0" cellpadding="0" cellspacing="0">
	<tbody>
		<tr>
			<td>Experimental Result</td>
			<td>Precursors</td>
			<td>Volume (ml)</td>
			<td>Initial NH4OH (ml)</td>
			<td>Final NH4OH (ml)</td>
			<td>TEOS (ml)</td>
		</tr>
		<tr>
			<td>1-2 nm WC</td>
			<td>W(VI)IPO (5% w/v)</td>
			<td>12</td>
			<td>0</td>
			<td>2.7</td>
			<td>1.2</td>
		</tr>
		<tr>
			<td>2-3 nm WC</td>
			<td>W(VI)IPO (5% w/v)</td>
			<td>12</td>
			<td>0</td>
			<td>1.4</td>
			<td>0.6</td>
		</tr>
		<tr>
			<td>6-8 nm WC</td>
			<td>W(VI)IPO homemade (5% w/v)</td>
			<td>12</td>
			<td>0.4</td>
			<td>1.4</td>
			<td>1.6</td>
		</tr>
		<tr>
			<td>7-10 nm WC</td>
			<td>W(IV)IPO homemade (6.5% w/v)</td>
			<td>8.8</td>
			<td>1.4</td>
			<td>1.4</td>
			<td>1.6</td>
		</tr>
		<tr>
			<td>9-13 nm WC</td>
			<td>W(IV)IPO homemade (6.5% w/v)</td>
			<td>10.2</td>
			<td>1.4</td>
			<td>1.4</td>
			<td>1.6</td>
		</tr>
		<tr>
			<td rowspan="2">4-6 nm Ti0.1W0.9C</td>
			<td>W(VI)IPO (5% w/v)</td>
			<td>10.8</td>
			<td rowspan="2">0.7</td>
			<td rowspan="2">1.4</td>
			<td rowspan="2">0.6</td>
		</tr>
		<tr>
			<td>Ti(IV)IPO (5% w/v)</td>
			<td>0.7</td>
		</tr>
		<tr>
			<td rowspan="2">7-10 nm (Ni0.3W0.7)2C</td>
			<td>W(VI)IPO (5% w/v)</td>
			<td>8.4</td>
			<td rowspan="2">0.4</td>
			<td rowspan="2">1.4</td>
			<td rowspan="2">0.6</td>
		</tr>
		<tr>
			<td>Ni(II)MEO (5% w/v)</td>
			<td>1.4</td>
		</tr>
	</tbody>
</table>

Table 1: Controlling TMC particle size by controlling RME parameters. *Initial NH4OH is if NH4OH has been added to the emulsion before metal alkoxide hydrolysis while final NH4OH is the total amount of NH4OH present in the emulsion before TEOS is injected.
<img alt="Figure 1" src="/files/ftp_upload/53147/53147fig1.jpg" /> 
Figure 1: Representative pictures of RME syntheses containing SiO2/TMO NPs immediately before (A &#8211; C) and after (D, F) the addition of 300 ml of methanol. (A) shows a synthesis of SiO2/WOx, (B) shows an SiO2/Mo0.06W0.94Ox synthesis, and (C) shows an SiO2/Mo0.54W0.46Ox synthesis while (D) and (E) show different viewing angles of the SiO2/WOx synthesis after the addition of methanol. In (D) and (E), the top phase is the heptane-rich liquid phase, the lower liquid phase is methanol-rich, and at the bottom of the flask are the SiO2/WOx flocs. Re-print with permission from reference 26.
<img alt="Figure 2" src="/files/ftp_upload/53147/53147fig2.jpg" /> 
Figure 2: Representative TEM images of (A) multiply-coated WOx NPs within SiO2 spheres and (B) singly-coated Ta0.3W0.7Ox NPs within SiO2 spheres. The scale bars are in nanometers. Modified from reference 26.
<img alt="Figure 3" src="/files/ftp_upload/53147/53147fig3.jpg" /> 
Figure 3: Representative TEM images of SiO2/WOx synthesized under identical conditions described in the procedure except with 60 ml of Igepal&#174; CO-520 instead of 54 ml of the Brij&#174;-L4 surfactant. The scale bar is in nanometers. Modified from reference 26.
<img alt="Figure 4" src="/files/ftp_upload/53147/53147fig4.jpg" /> 
Figure 4: Representative PXRD diffractograms of SiO2/WOx coated at different pH values. Carburizations were conducted at 835 &#176;C for 4 hr under 21% CH4/H2 and are shown for materials coated using a pH of (A) 10, (B) 10.5, (C) 10.9, and (D) 11.1. The low pH syntheses (A and B) have quartz-like silica (indicated by the sharp peak at 22&#176;) and multiple carbide phases while the high pH syntheses (C and D) have a broad peak centered at 22&#176;, indicative of amorphous silica, and single-phase face-centered-cubic WC NPs. Re-print with permission from reference 26.
<img alt="Figure 5" src="/files/ftp_upload/53147/53147fig5.jpg" /> 
Figure 5: Solvent precipitation effect studies by precipitating SiO2/WOx or SiO2/MoxW1-xOy with (A) Methanol, (B) Acetone, and (C) Isopropanol. All materials were rinsed with acetone after precipitation. The PXRD diffractograms are for the resulting materials post-carburization at 835 &#176;C for 4 hr under 21% CH4/H2. Re-print with permission from reference 26.
<img alt="Figure 6" src="/files/ftp_upload/53147/53147fig6.jpg" /> 
Figure 6: Representative TEM and HAADF-STEM images of (A) 1-2 nm SiO2/WC NPs post-carburization, (B) 2-3 nm SiO2/WC NPs post-carburization, (C) 7-10 nm SiO2/WC NPs post-carburization, (D) 9-13 nm SiO2/WC NPs post-carburization. The scale bars are in nanometers. Modified from reference 26.
<img alt="Figure 7" src="/files/ftp_upload/53147/53147fig7.jpg" /> 
Figure 7: (A) photographs of a hexagonal WC nanodispersion dispersed in water at 7.5 mg/ml before and after three weeks of sitting in stagnant ambient conditions, (B) representative HAADF-STEM image of an unsupported &#946;-WC nanopowder, (C) representative HAADF-STEM image of &#946;-WC NPs supported on carbon black at 25 wt%. The scale bars are in nanometers. Modified from reference 26.
<img alt="Figure 8" src="/files/ftp_upload/53147/53147fig8.jpg" /> 
Figure 8: PXRD diffractograms of silica-encapsulated monometallic and heterometallic early transition metal carbides and nitrides of various sizes. All TMNs were nitridized under 100 sccm NH3 at 800 &#176;C for 4 hr. 2-3 nm SiO2/W2C was synthesized at 775 &#176;C under 18% CH4/H2 for 4 hr while all of the &#60;3 nm TMC NPs were synthesized at 835 &#176;C under 21% CH4/H2. The larger TMC NPs were synthesized at 900 &#176;C under 21% CH4/H2. Modified from reference 26.

Watch this Scientific Journal Video about Reverse Microemulsion-mediated Synthesis of Monometallic and Bimetallic Early Transition Metal Carbide and Nitride Nanoparticles at JoVE.com

Reverse Microemulsion-mediated Synthesis of Monometallic and Bimetallic Early Transition Metal Carbide and Nitride Nanoparticles

A &#8220;removable ceramic coating method&#8221; is presented in visual format for the synthesis of non-sintered and metal-terminated monometallic and bimetallic early transition metal carbide and nitride nanoparticles with tunable sizes and crystal structures.

A reverse microemulsion is used to encapsulate monometallic or bimetallic early transition metal oxide nanoparticles in microporous silica shells. The ...

reverse-microemulsion-mediated-synthesis-monometallic-bimetallic

Nanyang Technological University

Research

JoVE Journal

Chemistry

10.8K Views.  Massachusetts Institute of Technology. A “removable ceramic coating method” is presented in visual format for the synthesis of non-sintered and metal-terminated monometallic and bimetallic early transition metal carbide and nitride nanoparticles with tunable sizes and crystal structures.

Video: Reverse Microemulsion-mediated Synthesis of Monometallic and Bimetallic Early Transition Metal Carbide and Nitride Nanoparticles

Preparation and Reactivity of Gasless Nanostructured Energetic Materials

High-Energy Ball Milling (HEBM) is a ball milling process where a powder mixture placed in the ball mill is subjected to high-energy collisions from the balls. Among other applications, it is a versatile technique that allows for effective preparation of gasless reactive nanostructured materials with high energy density per volume (Ni+Al, Ta+C, Ti+C). The structural transformations of reactive media, which take place during HEBM, define the reaction mechanism in the produced energetic&#160;composites. Varying the processing conditions permits fine tuning of the milling-induced microstructures of the fabricated composite particles. In turn, the reactivity, i.e., self-ignition temperature, ignition delay time, as well as reaction kinetics, of high energy density materials depends on its microstructure. Analysis of the milling-induced microstructures suggests that the formation of fresh oxygen-free intimate high surface area contacts between the reagents is responsible for the enhancement of their reactivity. This manifests itself in a reduction of ignition temperature and delay time, an increased rate of chemical reaction, and an overall decrease of the effective activation energy of the reaction. The protocol provides a detailed description for the preparation of reactive nanocomposites with tailored microstructure using short-term HEBM method. It also describes a high-speed thermal imaging technique to determine the ignition/combustion characteristics of the energetic materials. The protocol can be adapted to preparation and characterization of a variety of nanostructured energetic composites.

This protocol describes the preparation of gasless nanostructured energetic materials (Ni+Al, Ta+C, Ti+C) using the short-term high-energy ball milling (HEBM) technique. It also describes a high-speed thermal imaging method to study the reactivity of mechanically fabricated nanocomposites. These protocols can be extended to other reactive nanostructured energetic materials.

High-Energy Ball Milling (HEBM) is a ball milling process where a powder mixture placed in the ball mill is subjected to high-energy collisions from the ...

Engineering

Generation of Zerovalent Metal Core Nanoparticles Using n-(2-aminoethyl)-3-aminosilanetriol

In this work, a facile one-pot reaction for the formation of metal nanoparticles in a water solution through the use of n-(2-aminoethyl)-3-aminosilanetriol is presented. This compound can be used to effectively reduce and complex metal salts into metal core nanoparticles coated with the compound. By controlling the concentrations of salt and silane one is able to control reaction rates, particle size, and nanoparticle coating. The effects of these changes were characterized through transmission electron microscopy (TEM), UV-Vis spectrometry (UV-Vis), Nuclear Magnetic Resonance spectroscopy (NMR) and Fourier Transform Infrared spectroscopy (FTIR). A unique aspect to this reaction is that usually silanes hydrolyze and cross-link in water; however, in this system the silane is water-soluble and stable. It is known that silicon and amino moieties can form complexes with metal salts. The silicon is known to extend its coordination sphere to form penta- or hexa-coordinated species. Furthermore, the silanol group can undergo hydrolysis to form a Si-O-Si silica network, thereby transforming the metal nanoparticles into a functionalized nanocomposites.

Generation of Zerovalent Metal Core Nanoparticles Using n-2-aminoethyl-3-aminosilanetriol

A novel method for metal core nanoparticle synthesis using a water stable silanol is described.

In this work, a facile one-pot reaction for the formation of metal nanoparticles in a water solution through the use of ...

The Synthesis of [Sn10(Si(SiMe3)3)4]2- Using a Metastable Sn(I) Halide Solution Synthesized via a Co-condensation Technique

The number of well-characterized metalloid tin clusters, synthesized by applying the disproportionation of a metastable Sn(I) halide in the presence of a sterically demanding ligand, has increased in recent years. The metastable Sn(I) halide is synthesized at&#160;&#34;outer space conditions&#34; via the preparative co-condensation technique. Thereby, the subhalide is synthesized in an oven at high temperatures, around 1,300 &#176;C, and at reduced pressure by the reaction of elemental tin with hydrogen halide gas (e.g., HCl). The subhalide (e.g., SnCl) is trapped within a matrix of an inert solvent, like toluene at -196 &#176;C. Heating the solid matrix to -78 &#176;C gives a metastable solution of the subhalide. The metastable subhalide solution is highly reactive but can be stored at -78 &#176;C for several weeks. On heating the solution to room temperature, a disproportionation reaction occurs, leading to elemental tin and the corresponding dihalide. By applying bulky ligands like Si(SiMe3)3, the intermediate metalloid cluster compounds can be trapped before complete disproportionation to elemental tin. Hence, the reaction of a metastable Sn(I)Cl solution with Li-Si(SiMe3)3 gives [Sn10(Si(SiMe3)3)4]2- 1 as black crystals in high yield. 1 is formed via a complex reaction sequence including salt metathesis, disproportionation, and degradation of larger clusters. Further, 1 can be analyzed by various methods like NMR or single crystal X-ray structure analysis.

The Synthesis of [Sn10SiSiMe334]2- Using a Metastable SnI Halide Solution Synthesized via a Co-condensation Technique

The disproportionation reaction of a metastable Sn(I) chloride solution, obtained via the preparative co-condensation technique, is used for the synthesis of a metalloid tin cluster compound.

The number of well-characterized metalloid tin clusters, synthesized by applying the disproportionation of a metastable Sn(I) halide in the presence of a ...

Synthesis and Testing of Supported Pt-Cu Solid Solution Nanoparticle Catalysts for Propane Dehydrogenation

A convenient method for the synthesis of bimetallic Pt-Cu catalysts and performance tests for propane dehydrogenation and characterization are demonstrated here. The catalyst forms a substitutional solid solution structure, with a small and uniform particle size around 2 nm. This is realized by careful control over the impregnation, calcination, and reduction steps during catalyst preparation and is identified by advanced in situ synchrotron techniques. The catalyst propane dehydrogenation performance continuously improves with increasing Cu:Pt atomic ratio.

A convenient method for the synthesis of 2 nm supported bimetallic nanoparticle Pt-Cu catalysts for propane dehydrogenation is reported here. In situ synchrotron X-ray techniques allow for the determination of the catalyst structure, which is typically unobtainable using laboratory instruments.

A convenient method for the synthesis of bimetallic Pt-Cu catalysts and performance tests for propane dehydrogenation and characterization are ...

Chemical Precipitation Method for the Synthesis of Nb2O5 Modified Bulk Nickel Catalysts with High Specific Surface Area

We demonstrate a method for the synthesis of NixNb1-xO catalysts with sponge-like and fold-like nanostructures. By varying the Nb:Ni ratio, a series of NixNb1-xO nanoparticles with different atomic compositions (x = 0.03, 0.08, 0.15, and 0.20) have been prepared by chemical precipitation. These NixNb1-xO catalysts are characterized by X-ray diffraction, X-ray photoelectron spectroscopy, and scanning electron microscopy. The study revealed the sponge-like and fold-like appearance of Ni0.97Nb0.03O and Ni0.92Nb0.08O on the NiO surface, and the larger surface area of these NixNb1-xO catalysts, compared with the bulk NiO. Maximum surface area of 173 m2/g can be obtained for Ni0.92Nb0.08O catalysts. In addition, the catalytic hydroconversion of lignin-derived compounds using the synthesized Ni0.92Nb0.08O catalysts have been investigated.

Chemical Precipitation Method for the Synthesis of Nb2O5 Modified Bulk Nickel Catalysts with High Specific Surface Area

A protocol for the synthesis of sponge-like and fold-like Ni1-xNbxO nanoparticles by chemical precipitation is presented.

We demonstrate a method for the synthesis of NixNb1-xO catalysts with sponge-like and fold-like nanostructures. By varying the Nb:Ni ratio, a series of ...

Ligand-Mediated Nucleation and Growth of Palladium Metal Nanoparticles

The size, size distribution and stability of colloidal nanoparticles are greatly affected by the presence of capping ligands. Despite the key contribution of capping ligands during the synthesis reaction, their role in regulating the nucleation and growth rates of colloidal nanoparticles is not well understood. In this work, we demonstrate a mechanistic investigation of the role of trioctylphosphine (TOP) in Pd nanoparticles in different solvents (toluene and pyridine) using in situ SAXS and ligand-based kinetic modeling. Our results under different synthetic conditions reveal the overlap of nucleation and growth of Pd nanoparticles during the reaction, which contradicts the LaMer-type nucleation and growth model. The model accounts for the kinetics of Pd-TOP binding for both, the precursor and the particle surface, which is essential to capture the size evolution as well as the concentration of particles in situ. In addition, we illustrate the predictive power of our ligand-based model through designing the synthetic conditions to obtain nanoparticles with desired sizes. The proposed methodology can be applied to other synthesis systems and therefore serves as an effective strategy for predictive synthesis of colloidal nanoparticles.

The main goal of this work is to elucidate the role of capping agents in regulating the size of palladium nanoparticles by combining in situ small angle x-ray scattering (SAXS) and ligand-based kinetic modeling.

The size, size distribution and stability of colloidal nanoparticles are greatly affected by the presence of capping ligands. Despite the key contribution ...

Synthesis of Bimetallic Pt/Sn-based Nanoparticles in Ionic Liquids

We demonstrate a method for the synthesis of bimetallic nanoparticles consisting of Pt and Sn. A synthesis strategy is used in which the particular physico-chemical properties of ionic liquids (ILs) are exploited to control both nucleation and growth processes. The nanoparticles form colloidal sols of very high colloidal stability in the IL, which is particularly interesting in view of their use as quasi-homogeneous catalysts. Procedures for both nanoparticle extraction in conventional solvents and for nanoparticle precipitation are presented. The size, structure and composition of the synthesized nanocrystals are confirmed using inductively coupled plasma atomic emission spectroscopy (ICP-AES), X-ray diffraction analysis (XRD) and transmission electron microscopy (TEM) with energy-dispersive X-ray spectroscopy (EDX). By this, we show that the nanocrystals are random-type alloy and of small (2-3 nm) size. The catalytic activity and selectivity in the hydrogenation of &#945;,&#946;-unsaturated aldehydes is tested in a semi-continuous batch-type reactor. In this context, the bimetallic Pt/Sn-based nanoparticles reveal a high selectivity towards the unsaturated alcohol.

A protocol for the synthesis of bimetallic nanoparticles in ionic liquids and the procedure of their catalytic testing in the selective hydrogenation of unsaturated aldehydes are described.

We demonstrate a method for the synthesis of bimetallic nanoparticles consisting of Pt and Sn. A synthesis strategy is used in which the particular ...

Molten-Salt Synthesis of Complex Metal Oxide Nanoparticles

The development of feasible synthesis methods is critical for the successful exploration of novel properties and potential applications of nanomaterials. Here, we introduce the molten-salt synthesis (MSS) method for making metal oxide nanomaterials. Advantages over other methods include its simplicity, greenness, reliability, scalability, and generalizability. Using pyrochlore lanthanum hafnium oxide (La2Hf2O7) as a representative, we describe the MSS protocol for the successful synthesis of complex metal oxide nanoparticles (NPs). Furthermore, this method has the unique ability to produce NPs with different material features by changing various synthesis parameters such as pH, temperature, duration, and post-annealing. By fine-tuning these parameters, we are able to synthesize highly uniform, non-agglomerated, and highly crystalline NPs. As a specific example, we vary the particle size of the La2Hf2O7&#160;NPs by changing the concentration of the ammonium hydroxide solution used in the MSS process, which allows us to further explore the effect of particle size on various properties. It is expected that the MSS method will become a more popular synthesis method for nanomaterials and more widely employed in the nanoscience and nanotechnology community in the upcoming years.

Here, we demonstrate a unique, relatively low-temperature, molten-salt synthesis method for preparing uniform complex metal oxide lanthanum hafnate nanoparticles.

The development of feasible synthesis methods is critical for the successful exploration of novel properties and potential applications of nanomaterials. ...

Imine Metathesis by Silica-Supported Catalysts Using the Methodology of Surface Organometallic Chemistry

With this protocol, a well-defined singlesite silica-supported heterogeneous catalyst [(&#8801;Si-O-)Hf(=NMe)(&#951;1-NMe2)] is designed and prepared according to the methodology developed by surface organometallic chemistry (SOMC). In this framework, catalytic cycles can be determined by isolating crucial intermediates. All air-sensitive materials are handled under inert atmosphere (using gloveboxes or a Schlenk line) or high vacuum lines (HVLs, &#60;10-5 mbar). The preparation of SiO2-700 (silica dehydroxylated at 700 &#176;C) and subsequent applications (the grafting of complexes and catalytic runs) requires the use of HVLs and double-Schlenk techniques. Several well-known characterization methods are used, such as Fourier-transform infrared spectroscopy (FTIR), elemental microanalysis, solid-state nuclear magnetic resonance spectroscopy (SSNMR), and state-of-the-art dynamic nuclear polarization surface enhanced NMR spectroscopy (DNP-SENS). FTIR and elemental microanalysis permit scientists to establish the grafting and its stoichiometry. 1H and 13C SSNMR allows the structural determination of the hydrocarbon ligands coordination sphere. DNP SENS is an emerging powerful technique in solid characterization for the detection of poorly sensitive nuclei (15N, in our case). SiO2-700 is treated with about one equivalent of the metal precursor compared to the amount of surface silanol (0.30 mmol&#183;g-1) in pentane at room temperature. Then, volatiles are removed, and the powder samples are dried under dynamic high vacuum to afford the desired materials [(&#8801;Si-O-)Hf(&#951;2&#960;-MeNCH2)(&#951;1-NMe2)(&#951;1-HNMe2)]. After a thermal treatment under high vacuum, the grafted complex is converted into metal imido silica complex [(&#8801;Si-O-)Hf(=NMe)(&#951;1-NMe2)]. [(&#8801;Si-O-)Hf(=NMe)(&#951;1-NMe2)] effectively promotes the metathesis of imines, using the combination of two imine substrates, N-(4-phenylbenzylidene)benzylamine, or N-(4-fluorobenzylidene)-4-fluoroaniline, with N-benzylidenetert-butylamine as substrates. A significantly lower conversion is observed with the blank runs; thus, the presence of the imido group in [(&#8801;Si-O-)Hf(=NMe)(&#951;1-NMe2)] is correlated to the catalytic performance.

A new group IV metal catalyst for imine metathesis is prepared by grafting amine metal complex onto dehydroxylated silica. Surface metal fragments are characterized using FT-IR, elemental microanalysis, and solid-state NMR spectroscopy. Further dynamic nuclear polarization surface enhanced NMR spectroscopy experiments complement the determination of the coordination sphere.

With this protocol, a well-defined singlesite silica-supported heterogeneous catalyst [(&#8801;Si-O-)Hf(=NMe)(&#951;1-NMe2)] is designed and prepared ...

A Salt-Templated Synthesis Method for Porous Platinum-based Macrobeams and Macrotubes

The synthesis of high surface area porous noble metal nanomaterials generally relies on time consuming coalescence of pre-formed nanoparticles, followed by rinsing and supercritical drying steps, often resulting in mechanically fragile materials. Here, a method to synthesize nanostructured porous platinum-based macrotubes and macrobeams with a square cross section from insoluble salt needle templates is presented. The combination of oppositely charged platinum, palladium, and copper square planar ions results in the rapid formation of insoluble salt needles. Depending on the stoichiometric ratio of metal ions present in the salt-template and the choice of chemical reducing agent, either macrotubes or macrobeams form with a porous nanostructure comprised of either fused nanoparticles or nanofibrils. Elemental composition of the macrotubes and macrobeams, determined with x-ray diffractometry and x-ray photoelectron spectroscopy, is controlled by the stoichiometric ratio of metal ions present in the salt-template. Macrotubes and macrobeams may be pressed into free standing films, and the electrochemically active surface area is determined with electrochemical impedance spectroscopy and cyclic voltammetry. This synthesis method demonstrates a simple, relatively fast approach to achieve high-surface area platinum-based macrotubes and macrobeams with tunable nanostructure and elemental composition that may be pressed into free-standing films with no required binding materials.

A synthesis method to obtain porous platinum-based macrotubes and macrobeams with a square cross section through chemical reduction of insoluble salt-needle templates is presented.

The synthesis of high surface area porous noble metal nanomaterials generally relies on time consuming coalescence of pre-formed nanoparticles, followed ...

Reverse Microemulsion-mediated Synthesis of Monometallic and Bimetallic Early Transition Metal Carbide and Nitride Nanoparticles

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