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Journal of Nanotechnology
Volume 2013 (2013), Article ID 578684, 9 pages
http://dx.doi.org/10.1155/2013/578684
Research Article

Synthesis by Microwaves of Bimetallic Nano-Rhodium-Palladium

1Laboratorio Nacional de Nanotecnología, Centro de Investigación en Materiales Avanzados, S.C., Avenida Miguel de Cervantes 120, 31109 Chihuahua, CHIH, Mexico
2Instituto de Investigaciones en Materiales, Universidad Nacional Autónoma de México, Apartado Postal 70-360, 04510 México, DF, Mexico
3Facultad de Ciencias, Ciudad Universitaria, Universidad 3000, Circuito Exterior S/N, 04510 México, DF, Mexico

Received 29 May 2013; Revised 31 August 2013; Accepted 12 September 2013

Academic Editor: Jorge Seminario

Copyright © 2013 M. Ugalde et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract

An improved acrylamide sol-gel technique using a microwave oven in order to synthesize bimetallic Rh-Pd particles is reported and discussed. The synthesis of Pd and Rh nanoparticles was carried out separately. The polymerization to form the gel of both Rh and Pd was carried out at 80°C under constant agitations. The method chosen to prepare the Rh and Pd xerogels involved the decomposition of both gels. The process begins by steadily increasing the temperature of the gel inside a microwave oven (from 80°C to 170°C). In order to eliminate the by-products generated during the sol-gel reaction, a heat treatment at a temperature of 1000°C for 2 h in inert atmosphere was carried out. After the heat treatment, the particle size increased from 50 nm to 200 nm, producing the bimetallic Rh-Pd clusters. It can be concluded that the reported microwave-assisted, sol-gel method was able to obtain nano-bimetallic Rh-Pd particles with an average size of 75 nm.

1. Introduction

Bimetallic alloy (solid solutions or intermetallics compounds) nanostructures, synthesized from two single components, have been of interest because of their superior properties, in comparison with their respective single-component species, that is, Ag, Pd, Rh, and so forth [1]. The synthesis of noble metals and alloys, in nanometric scale, has been extensively investigated in nanotechnology because of their optical and electronic properties, as well as for their useful applications in many fields such as medicine [2], catalysis, and sensors [36]. Hardness, high melting and boiling points, and high thermal and electrical conductivity are some of the existing properties of these noble metals.

Rhodium and palladium (Rh and Pd) crystallize in a face centered cubic (fcc) unit cell. Both metals add s electrons to the collective d band of palladium [7] and increase the lattice parameter of the palladium host lattice [8, 9]. It was found that rhodium behaves as an absorber of hydrogen at high pressure of gaseous hydrogen when situated within the palladium lattice [10, 11].

Recently, Pd nanocrystals have been prepared in aqueous solutions giving rise to a great variety of shapes, including truncated octahedron, cube, octahedron, and thin plate [1214], making them ideal candidates as seeds for growing bimetallic nanostructures. The control of crystal size and its dispersion are among the main goals of nanocrystal preparation. This is due to the physicochemical properties of a bimetallic nanocrystal that can be tailored by controlling their particle size, shape, and elemental composition, as well as their internal and surface structures. Recently, the complexity of nanomaterials can be further enhanced by the formation of multimetallic nanostructures (e.g., core-shell and dumbbell). Synthesis parameters such as capping agent, metal ion, and reaction temperature also play an important role in the overgrowth process [15]. Among the available methods to obtain nanosized bimetallic particles of rhodium-palladium are the coimpregnation method [16, 17], nanocrystals stabilized in micelles, [18, 19] gas evaporation [20, 21] polyol process [22], and the sol-gel method [23].

Different methods have been developed to produce metal nanoparticles, but these differ significantly, depending on the application required. Osseo-Asare and Arriagada [18] stabilized Rh particles using the ionic (poly (N-vinyl-2-pyrrolidone)-co-(1-vinyl-3-alkylimidazolium halide)) copolymer in ionic solvents. They found a distribution of particles of ~3 ± 0.6 nm. These nanoparticles were used as catalysts for arene hydrogenation. Similarly, Pileni [19] produced Rh nanoparticles through chemical reduction. This synthesis method is widely used to produce nanoparticles, which will be used as catalysts, on an industrial scale. They reported that the Rh nanoparticles are formed by reducing Rh ions in ethanol-water solvent with the polymers of polyvinylpyrrolidone (PVP) [20, 21]. The PVP encapsulates the nanoparticles in the solution and prevents their accumulation. The growth of the nanoparticles may be limited during the reduction by the space restrictions imposed by the three-dimensional PVP network. The particles generated from this method showed an average size of 3.2 ± 0.7 nm. However, it was noted that within the network of the Rh-PVP, there were Cl atoms. These species came from the reagent used (RhCl3 (3H2O)). During the synthesis, the Cl atoms were entrapped as an impurity in the interlattice planes of the material. The particles produced can only be used for catalysis, since the aforementioned reagent stabilizes them. Thus, the impurities anchored in the structure may detrimentally affect their catalytic properties. Therefore, it is imperative to produce impurity-free Rh, Pd, or Rh-Pd nanoparticles, in order to widen their possible applications [2442].

Based on the above, the objective of this work is to synthesize an impurities-free bimetallic alloy of palladium-rhodium through a modified polyacrylamide sol-gel method, using microwave radiation. The motivation of this study is based on the observation that a possible synergism may exist between both metallic atoms, as they are located in close proximity. The possible union effect can be reflected in the chemical performances of both metals, which differ from the chemical behavior of each of the metallic components alone. Finally, it is worth mentioning that sol-gel method was chosen because nanoparticle size control can be achieved by means of heat treatments or pH variations.

2. Experimental Procedure

2.1. Materials and Synthesis Procedure

The reagents used in this work were Rhodium metal (99.9%, Sigma-Aldrich), Palladium acetate (Pd(OAc)2 99%, Aldrich), sulfuric acid (H2SO4, J. T. Baker), nitric acid (HNO3; 70%, J. T. Baker), ammonium hydroxide (NH4OH; 28–30%, J. T. Baker), ethylenediaminetetraacetic acid (EDTA; 99%, Fluka), N,N′-methylenebisacrylamide (99.5%, Fluka), 2,2′-azobis(2-methylpropionamidine) dihydrochloride (98%, Fluka), acrylamide monomer (99%, Sigma-Aldrich), and distilled water.

The synthesis of Pd and Rh nanoparticles was carried out separately, using an acrylamide sol-gel technique [43]. The synthesis of Rh nanoparticles started dissolving 439 mmoL of Rh metal in H2SO4 and distilled water (80 mL) at 70°C, forming a yellowish solution. Later, the solution was cooled down to ambient temperature prior to adjusting the pH ca. to 7 by adding NH4OH, following the method outlined in [44]. As soon as a pH ca. 7 was reached, the solution was heated up to 80°C, and 51.6 mmoL of EDTA was added to complex the rhodium ions, avoiding the formation of agglomerates. After this, 211 mmoL of acrylamide monomer and 9.72 mmoL of cross-linking agent, N,N′ methylenebisacrylamide, were added to the initial solution. Finally, to produce the gel, 5.5 mmoL of initiator, 2,2′-azobis(2-methylpropionamidine)dihydrochloride, was added to reach the polymerization [43]. The pH of the solution was constantly monitored by means of a pH meter (Thermo Scientific Orion star A221). The polymerization of Rh was carried out at 80°C under constant agitation. It is worth noting that all the processes were done under air atmosphere. In neutral or basic conditions, the time required to form the gel decreases considerably [26].

The synthesis of Pd nanoparticles was carried out by dissolving Pd acetate in 300 mL of distilled water, at 80°C. After this, 12 mL of HNO3 and H2O2 were added. Later, the solution was cooled down to ambient temperature prior to adjusting the pH ca. to 7 by adding NH4OH, similar to the method used for Rh. As soon as a pH ca. 7 was reached, the solution was heated up to 80°C, and 10.2 mmoL of EDTA was added. This EDTA reagent is used in this process with the aim of trapping the Pd metal ions and preventing the formation of agglomerates, until the reaction starts. By doing this, the Pd ions remain stable during the decomposition of EDTA [43].

In order to start the polymerization, 562.7 mmoL of acrylamide monomer and 129.7 mmoL of the cross-linker N–N′ methylenebisacrylamide were added. Immediately, 3.68 mmoL of a chemical initiator αα′ azodiisobutyramidine dihydrochloride was incorporated to the solution in order to increase interconnection velocity [43, 44]. The polymerization occurred at 80°C in air, under continuous magnetic stirring.

The method chosen to prepare the Rh and Pd xerogels involves the decomposition of both gels. The process begins by heating up both gels inside a microwave oven, that is, from 80°C to 170°C. The microwave is equipped with an infrared temperature sensor, installed in such fashion that it can measure the temperature of the material, in analysis, within the reaction area. In this process, the oven increases the temperature steadily. Once a temperature of 170°C has been reached (under an argon flux), the process to generate the xerogel of Rh and Pd lasts 30 min and 3 min, respectively. The produced Rh and Pd xerogels were pulverized, using an agate electric mortar (Retsch GmbH-Mortar Grinder RM 100), and heated at 1000 ± 4°C for 2 h, under an argon flux.

2.2. Characterization

The crystalline structure of the materials produced was determined by XRD, using a Bruker AXS D8-advance diffractometer, with Cu Kα radiation (λ = 1.5406 Å), 40 KV and 30 mA, equipped with a graphite diffracted beam monochromator. The diffractogram patterns were collected at room temperature over the 2θ range of 2.5° to 70°, with a step size of 0.02°, and time per step of 0.6 s. A thermal analyzer (STD Q600, TA-Instruments) using a standard alumina pan, with a heating rate of 10°C min−1 in air atmosphere, over a range of temperatures of 30°C to 1000°C was used to study decomposition temperatures.

The microstructure and morphology were observed using a scanning electron microscope (SEM JSM5800L, JEOL) and a high-resolution transmission electron microscope (HRTEM JEM-2200FS, JEOL). The samples were prepared by dispersing ca. 2 mg of Rh-Pd nanocrystals in 4 mL of 1-propanol and were then sonicated for 15 min. Finally, a drop of dispersion was deposited on a lacey carbon supported copper grid (200 mesh). A series of SEM micrographs, at 10 kV, and HR-TEM, at 200 kV, were taken. The composition of the material was determined with an Energy Dispersive X-Ray (EDX) spectroscope, with an Oxford Incax-sight 7688 detector. The size distribution was determined from the micrographs taken with the HRTEM. The size distribution histograms were calculated using “Image J” software (Image Processing and Analysis in Java). In this work, the diameters of at least 100 particles were measured and mean values were determined. The statistical error was also included.

3. Results and Discussion

3.1. X-Ray Diffraction Patterns

The combination of the XRD and TGA analysis proved to be useful when observing the number of phases that changed during the applied heat treatments to the gel and xerogel. Figure 1(a) shows the gel and xerogel diffractograms of Rh. Both diffractograms showed the presence of two distinctive crystalline phases, that is, ammonium sulfate (NH4)2SO4 (PDF 01-78-0579) and edetic acid C10H16N208 (PDF 00-033-1672). The former could be attributed to the addition of NH4OH, which was used to neutralize pH of the solution in the reaction. The latter could be associated with the reaction between the polymer and the EDTA. The xerogel diffractogram clearly shows six low intensity peaks that correspond to edetic acid; this evidences that the edetic acid is being removed during this process.

fig1
Figure 1: XRD patterns of (a) Rh, (b) Pd, and (c) bimetallic Rh-Pd.

The Pd diffraction patterns of the xerogel and gel products are displayed in Figure 1(b). The Pd gel showed a typical halo for amorphous materials. It is thought that this material has been produced by the remained amount of acrylamide polymer, although a small Bragg peak was observed at ~2θ = 40°. This low intensity peak could be attributed to Pd (PDF 03-065-6174). On the other hand, the Pd xerogel diffractogram not only showed the amorphous contribution and the peak that corresponds to Pd but also displayed a number of peaks that were identified as palladium oxide (PdO) (PDF 01-075-0584), Pd (NO3)2(H2O)2 (PDF 01-085-2483), and NH4NO3 (PDF 00-08-0452). It is thought that these compounds are the product of the transformation of the gel to xerogel.

After the heat treatment at 1000°C for 2 h, all by-products shown in Figures 1(a) and 1(b) disappeared. This can be clearly observed in Figure 1(c), where only the peaks of Pd (PDF 03-065-6174) and Rh (PDF 01-087-0714) metallic elements are displayed. Therefore, the formation of the bimetallic compound Rh-Pd is supported by these results.

3.2. Thermogravimetric Analysis (TGA)

The TGA curves are important to determine the temperatures to which the formation of organic matter and subproducts take place during the sol-gel synthesis. The results obtained from this technique did help to control the process parameters to produce the Rh-Pd bimetallic material.

The TGA results obtained from the rhodium and palladium gel and xerogel were analyzed separately and are shown in Figure 2. The TGA gel and xerogel traces for rhodium (Figure 2(a)) showed a weight loss at ~230°C and 241°C, respectively, indicating that there was a process of polymer degradation. The removal of (NH4)2SO4 occurred at 328°C in the gel and at 378°C in xerogel. It was also observed that the formation of Rh2O3 occurred at 597°C and 620°C for the gel and xerogel, respectively. When increasing the temperature up to 1000°C, particles of Rh were obtained, confirming the elimination of all by-products generated before and during heat treatment.

fig2
Figure 2: TGA curves from gel and xerogel for (a) rhodium and (b) palladium.

Figure 2(b) exhibits the thermograms for the Pd gel and xerogel. For the Pd gel, an initial weight loss at 148°C was evident. This was attributed to the evaporation of H2O, while at 260°C the weight loss corresponded to the removal of NH4NO3. Similarly, at 400°C, the elimination of Pd (NO3)2(H2O)2 compound is detected, and finally at 505°C the decomposition of PdO was observed. The TGA for the Pd xerogel curve displays a weight loss at 293°C, as a consequence of the degradation of both the acrylamide and NH4NO3 compounds. Some (Pd (NO3)2(H2O)2) traces were detected around 400°C, and then, the observed drop of the TGA curve at 557°C indicates that after this temperature, the formation of Pd particles can be favored.

From these results and considering the decomposition points of Rh2O3 and PdO, both compounds were heat treated at 1000°C for 2 h under an Ar flux. After this, it was expected that the growth of those Pd-Rh particles might occur. Table 1 shows the average of weight loss obtained by means of thermal analysis.

tab1
Table 1: Study of thermal transitions for the Rh and Pd gel and xerogel, respectively.

3.3. Scanning Electron Microscopy (SEM)

Figure 3(a) shows the bimetallic material before being subjected to the heat treatment at 1000°C. This image clearly shows a morphology mainly composed by elongated granules ranging from 500 nm to 1 µm. Figure 3(b) shows the morphology of the bimetallic Rh-Pd grains produced after applying the heat treatment; it was observed that the material started to grow, forming sphero-hexagonal shapes between 1 and 7 μm. The EDS elemental analysis of the Rh-Pd particles is shown in Figure 4. The average composition percentage for the Rh and Pd was 34.53% and 65.47%, respectively. Figure 5 shows the elemental SEM mapping performed to the produced Rh-Pd particles. This analysis confirmed the homogeneous distributions of the Rh and Pd elements in the material.

fig3
Figure 3: SEM analysis for the (a) material before the heat treatment and (b) Rh-Pd alloy powders after applying the heat treatment at 1000°C for 2 h.
fig4
Figure 4: EDS analysis for the Rh-Pd alloy particles after applying the heat treatment at 1000°C for 2 h.
578684.fig.005
Figure 5: SEM elemental mapping for the bimetallic Rh-Pd.
3.4. High Resolution Transmission Electron Microscopy (HRTEM)

In order to observe the Rh-Pd particles by HRTEM, these were dispersed by ultrasonication. The HRTEM micrographs showed the formation of clusters with a polyhedron shape and distribution of the grains’ size ranging from 50 to 200 nm (Figure 6(a)). Figure 6(c) shows the micrograph of one Rh-Pd particle with a size of ~100 nm. It is thought that the change in size and geometry of those particles could be attributed to the sonication process, which fractured and broke the sphero-hexagonal shape particles, producing nano-hexagonal shapes particles, with an average size of 75 nm, as shown in Figure 6(b).

fig6
Figure 6: Micrographs of HRTEM of the nano-bimetallic Rh-Pd. (a) Sphero-hexagonal shapes, (b) average-size distribution of particles (~75 nm), and (c) grain of the bimetallic Rh-Pd of ~50 nm.

The results presented in this work for the synthesis of bimetallic Rh-Pd by sol-gel with acrylamide using microwaves were in good agreement with those reported in [45, 46]. They reported the synthesis of Pd-Rh bimetallic nanodendrites. These particles consisted of Rh branches anchored to a Pd nanocrystal core. The palladium nanocrystals synthesized by different methods exhibit distinct forms, that is, truncated octahedron, cube, and thin plate. According to Kobayashi, Pd has been successfully employed as seed to grow Rh branches. The bimetallic particles are around 20 nm. However, as mentioned above, the synthesized method used by Kobayashi is based on reducing Na3RhCl6 from L-ascorbic acid in an aqueous solution. This method has several shortcomings; one of the most important is that varying the concentration of Na3RhCl6 during the synthesis could only control the degree of Rh branching. A high concentration of Rh in the solution causes that only part of Rh can be anchored around the Pd, and the excess of the produced nano-Rh, that fails to be anchored, is dispersed in the formed solution; that is, it fails to complete its reactions with Pd to form the bimetal. On the other hand, the varieties of morphologies, found by Kobayashi for Pd grains used as inoculants to grow the Rh branches, were comparable to those reported in this work for the synthesis of bimetallic Rh-Pd by the modified sol-gel technique. This could be attributed to the heat treatment applied, in which the sintering process of the bimetallic material begins, causing the grain growth, forming sphero-hexagonal shaped-like morphology particles. Besides, this method did help the formation of a bimetallic compound with a reasonably well homogeneous distribution, as it was clearly observed in the SEM mapping.

4. Conclusion

The reported microwave-assisted, sol-gel method was able to obtain nano-bimetallic Rh-Pd particles with an average size of 75 nm. Thermogravimetric analysis helped determine not only the decomposition temperatures but also the heat treatment conditions needed to obtain nano-Rh-Pd-particles. After the heat treatment at 1000°C/2 h, the subproducts that were produced during the sol-gel reaction were removed. The synthesis of the nano-bimetallic Rh-Pd was confirmed by XRD and EDX. The HRTEM micrographs showed the formation of clusters with a polyhedron shape and distribution of the grains’ size ranging from 50 to 200 nm. The clusters were successfully dispersed with an ultrasonic cleaner. The sphero-hexagonal shaped-like morphology particles reported in this work could be attributed to the heat treatment process. Finally, it is worth noting that our Rh-Pd particles are not restricted to a single application, as the resulting Rh-Pd nanoparticles were found to be free of impurities, since the stabilizer used (EDTA) was completely removed with the heat treatment.

Acknowledgments

M. Ugalde acknowledges the financial support from CONACyT through the scholarship 207277.  I. A. Figueroa acknowledges the financial support from PAPIIT UNAM through project IB100712/RR180712. The authors also express their acknowledgment for the technical support of Laboratorio Nacional de Nanotecnología, Centro Nacional de Nanotecnología, and CIMAV and especially to Karla Campos Venegas, Carlos Ornelas, Omar Novelo, and Caín Gónzalez for their interesting useful discussions.

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