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. 2015 Jan 5;5:7619. doi: 10.1038/srep07619

A Strategy for Fabricating Porous PdNi@Pt Core-shell Nanostructures and Their Enhanced Activity and Durability for the Methanol Electrooxidation

Xinyu Liu 1, Guangrui Xu 2, Yu Chen 2,a, Tianhong Lu 1, Yawen Tang 1,b, Wei Xing 3
PMCID: PMC5154597  PMID: 25557190

Abstract

Three-dimensionally (3D) porous morphology of nanostructures can effectively improve their electrocatalytic activity and durability for various electrochemical reactions owing to big surface area and interconnected structure. Cyanogel, a jelly-like inorganic polymer, can be used to synthesize various three-dimensionally (3D) porous alloy nanomaterials owing to its double-metal property and particular 3D backbone. Here, 3D porous PdNi@Pt core-shell nanostructures (CSNSs) are facilely synthesized by first preparing the Pd-Ni alloy networks (Pd-Ni ANWs) core via cyanogel-reduction method followed by a galvanic displacement reaction to generate the Pt-rich shell. The as-synthesized PdNi@Pt CSNSs exhibit a much improved catalytic activity and durability for the methanol oxidation reaction (MOR) in the acidic media compared to the commercial used Pt black because of their specific structural characteristics. The facile and mild method described herein is highly attractive for the synthisis of 3D porous core-shell nanostructures.

Direct methanol fuel cells (DMFCs), a green low-temperature power source, have wide applications in portable electronic devices, residence and automobiles because of their low pollution level, high energy efficiency, convenient storage and transportation, and clean utilization1,2,3,4,5,6,7,8. However, the realization and commercialization of DMFCs have been challanging because of low activity and weak long-term stability of anodic Pt electrocatalysts, as well as the high cost of precious metal Pt. Therefore, improving catalytic activity, stability and efficiency of anodic Pt electrocatalysts has currently been a pressing research topic in electrocatalysts development2,4,5,6,9,10.

Untill now, various highly active Pt-based muliti-metal nanostructures with the different structures, such as alloy3,11,12, core-shell13,14 and heterostructure15 nanocrystals, have been synthesized successfully. Recently, there has been a growing interest in the synthsis of Pt-based muliti-metal core-shell nanostructures consisting of nonprecious metal core (such as Ni@Pt16,17) or less expensive noble metal core (such as Pd@Pt18,19,20 and Au@Pd@Pt13,14). These Pt-based core-shell nanostructures with designed compositions and morphologies efficiently reduce the cost of Pt and synchronously improve Pt utilization. Meanwhile, these Pt-based core-shell nanostructures show the remarkably enhanced electrocatalytic activity and durability compared to single-component Pt electrocatalyst because of the geometric effect, electronic effect and synergistic effect between different components. For example, the Pd@Pt core-shell nanocrystals exhibited improved electrocatalytic activity and durability for the methanol oxidation reaction (MOR) compared to Pt nanodendrites and Pt nanocubes18. The Ni@Pt core-shell nanotube arrays exhibited higher electrocatalytic performance for the MOR compared to Pt/C catalyst16. To obtain core-shell nanostructures, many strategies have been developed successfully in the recent years. For instance, Li and co-workers utilized an epitaxial growth route to synthesize Pt@Pd nanocrystals with Na3C6H5O7 as a reductant at high temperature21. Koenigsmann and co-workers achieved Pd nanowire core@Pt monolayer shell nanostructures by Cu underpotential deposition followed by galvanic displacement of the Cu adatoms22. Yang and co-workers applied direct galvanic displacement to synthesize core-shell Pd@Pt/C electrocatalyst at high temperature23.

Besides structure, morphology of nanostructures plays an important role in determining their durability. For example, three-dimensionally (3D) porous morphology can contribute to remarkably enhanced electrocatalytic stability of nanostructures24,25,26. Essentially, no individual nanoparticle exists in 3D porous nanostructures because of their interconnected structure, which effectively restrains Ostwald ripening effect and preserves their electrochemically surface areas (ECSA). In recent works, we have successfully synthesized the 3D porous noble metal nanostructures by reducing cyanogels with NaBH4 at room temperature. The as-prepared 3D alloy nanostructures generally exhibited enhanced electrocatalytic activity and stability for the MOR, oxygen reduction reaction, ethanol oxidation reaction, and formic acid oxidation reaction, etc27,28,29,30.

Herein, we presented a facile aqueous synthesis of corallite-like PdNi@Pt core-shell nanostructures (PdNi@Pt CSNSs) with 3D porous morphology, which utilized Pd-Ni alloy networks (Pd-Ni ANWs) as a core component synthesized via cyanogel-reduction method, and further conducted the galvanic displacement with K2PtCl4 to generate Pt shell. Electrochemical measurements showed that PdNi@Pt CSNSs had the excellent electrocatalytic activity and stability for the MOR.

Results and Discussion

Synthesis of Pd-Ni alloy networks (Pd-Ni ANWs)

Cyanogel, a coordinate inorganic polymer, is a special class of 3D double-metal cyanide, which can be facily achieved by mixing tetrachlorometalates ([RCl4]2−, R = Sn, Pd, Pt) and cyanometalates ([M(CN)n]2−/3−, (n = 4, 6; M = Pd, Pt, Fe, Co, Ni, Ru) aqueous solutions (equation (1))27,28,29,30,31,32,33. After mixing K2PdCl4 and K2Ni(CN)4 aqueous solutions at room temperature for 10 min, the orange jelly-like K2PdCl4/K2Ni(CN)4 cyanogel generates slowly (Figure 1A). In the inorganic polymer, PdII and NiII atoms uniformly mix and concentrate on the cyanogel's backbone. Once chemical reduction, the close connection between PdII and NiII species effectively facilitate the combination between Pd and Ni crystal nuclei. Moreover, the cyanogel's solid nature restrain the brownian motion of performed crystal nuclei, favouring the formation of Pd-Ni alloy. Furthermore, the 3D backbone of cyanogel can availably serve as a support scaffold to faciliate the formation of the interconnected 3D structure. Thus, the Pd-Ni alloy networks (Pd-Ni ANWs) can be conveniently achieved by cyanogel-reduction route with NaBH4 (details see Experimental Section). As confirmed by scanning electron microscopy (SEM) image, the Pd-Ni products indeed have 3D network-like architectures (Figure 1B). X-ray diffraction (XRD) pattern demonstrates that Pd-Ni ANWs have the face centered cubic (fcc) structure (Figure 1C). No diffraction peaks for single-component Pd or Ni is detected in the XRD pattern. Diffraction peaks at 40.62°, 47.17°, 69.17°, 83.58° and 88.03° shift to higher angle relative to Pd (JCPDS no: 04-1043) and to lower angle relative to Ni (JCPDS no: 04-0850), indicating the formation of Pd-Ni alloy34. Energy dispersive spectrum (EDS) elemental mapping patterns display both Pt and Cu elements uniformly distributed in the whole Pd-Ni ANWs (Figure 1D), confirming the formation Pd-Ni alloy.

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Figure 1.

Figure 1

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(A) Photograph of K2PdCl4/K2Ni(CN)4 cyanogel. (B) SEM image, (C) XRD pattern, and (D) EDS elemental mapping patterns of Pd-Ni ANWs.

Synthesis of PdNi@Pt core-shell nanostructures (PdNi@Pt CSNSs)

Thanks to the discrepancy in the standard reduction potentials different metal couples (E Ni2+/Ni = –0.257 V vs. NHE, E Pd2+/Pd = 0.729 V vs. NHE, E PtCl42−/Pt = 1.249 V vs. NHE), PdNi@Pt core-shell nanostructures (CSNSs) can be easily obtianed by the galvanic displacement reaction between Pd-Ni ANWs and K2PtCl4 in an aqueous solution at room temperature (equation (2) – (3)). In comparision with EDS spercum of Pd-Ni ANWs (Figure S1A), the apperance of Pt element confirms the galvanic displacement reaction between Pd-Ni ANWs and K2PtCl4 (Figure S1B). EDS spercum of PdNi@Pt CSNSs shows that the Pd/Ni/Pt atomic ratio is 61.2:22.6:16.2, in agreement with inductively coupled plasma atomic emission spectrometry (ICP-AES) data (62.0:21.4:16.6). Compared with Pd/Ni atomic ratio in Pd-Ni ANWs (68.0:32.0), the obvious decrease in Ni content indicates Ni element in Pd-Ni ANWs acts as a preferential reductant for the reduction of K2PtCl4 due to its stronger reduction capablity than Pd.

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The crystal structure of PdNi@Pt CSNSs was explored by XRD. XRD pattern of PdNi@Pt CSNSs shows typical fcc structure (Figure 2A-a), in consistent with XRD pattern of Pd-Ni ANWs (Figure 2A-b). On the one hand, typical XRD peak angles of Pd and Pt are very similar. On the other hand, the Pt shell with small particle size is difficultly detected by XRD. The two factors results in the high similarity in XRD patterns of PdNi@Pt CSNSs and Pd-Ni ANWs19,35,36. Using Debye-Scherrer formula, the average particle size (dXRD) of PdNi@Pt CSNSs is calculated from {111} diffraction peak to be 5.9 nm, smaller than that of commercial Pt black (dXRD = 8.7 nm, Figure S2). The morphology of PdNi@Pt CSNSs was investigated by SEM. SEM image shows the products have the corallite-like 3D porous architectures (Figure 2B), very similar to the morphology of Pd-Ni ANWs (Figure 1B). Since such 3D architecture can essentially facilitate mass transport of fuel molecules, which is highly attractive for electrochemical applications.

Figure 2.

Figure 2

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(A) XRD patterns of (a) PdNi@Pt CSNSs and (b) Pd-Ni ANWs. (B) SEM image of PdNi@Pt CSNSs.

The morphology and structural features of PdNi@Pt CSNSs were further investigated by transmission electron microscopy (TEM). The large area TEM image shows PdNi@Pt CSNSs consist of small and irregular nanoparticles, and these nanoparticles interconnect to generate abundant pores (Figure 3A). High-resolution TEM (HR-TEM) image shows the irregular interconnected nanostructures consist of ca. 7 nm grains (Figure 3B). Selected area electron diffraction (SAED) pattern displays a successive dotted pattern (insert in Figure 3B), demonstrating PdNi@Pt CSNSs are polycrystalline. Magnified HRTEM image shows the lattice fringes with a spacing of 0.227 nm, in consistent with the Pt{111} facets (Figure 3C). The fast Fourier transform (FFT) pattern of the lattice image displays the diffraction spots with 6-fold rotational symmetry (inset in Figure 3C), confirming that PdNi@Pt CSNSs are actually presented by {111} facets. Elemental mapping under scanning transmission electron microscopy mode is a powerful technique to investigate the element distribution of nanostructures. Clearly, the elemental distribution profiles of Pt, Pd and Ni are very similar (Figure 3D). And, EDS line scanning curves also confirm that Pt, Pd and Co elements are evenly distributed through nanostructures (Figure 3E). But it is still hard to decide whether it is core-shell or alloy structures because the reduced Pt shell is a thin layer.

Figure 3.

Figure 3

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(A) TEM image of PdNi@Pt CSNSs. (B) HR-TEM image of PdNi@Pt CSNSs. Insert: SAED pattern. (C) Magnified HR-TEM image taken from region marked by squares in Figure 3B. Insert: FFT pattern. (D) High angle angular dark field-scanning transmission electron microscopy image of PdNi@Pt CSNSs and the corresponding EDS elemental mapping patterns. (E) EDS line scanning profiles of PdNi@Pt CSNSs recorded from Figure 3D.

Fortunately, X-ray photoelectron spectroscopy (XPS) is a surface sensitive technique. XPS measurement shows the Pd:Ni:Pt atomic ratio in PdNi@Pt CSNSs is 50.8:15.3:33.8 (Figure S3). Herein, the Pt content is noticeably higher than that measured by EDS (Pd:Ni:Pt atomic ratio is 61.2:22.6:16.2), demonstrating that PdNi@Pt core-shell nanostructures have been successfully synthesized. Further detaied analysis show the percentages of Pt0 and Pd0 species are 85.5% and 82.7%, respectively (Figure 4A–B), indicating metallic Pt and Pd are predominant in nanostructures. Compared with Pd-Ni ANWs, the Ni 2p signal at PdNi@Pt CSNSs significantly weaken (Figure S4), confirming the galvanic displacement reaction between Ni and K2PtCl4 is predominant for the formation of PdNi@Pt CSNSs. Meanwhile, the Pt 4f binding energies negetively shift ca. 0.15 eV relative to Pt black (Figure S5), which may be ascribed to the compressive strain introduced by PdNi substrate37, and the electron donation induced by Pd and Ni with smaller electronegativity (Pt, 2.28; Pd, 2.20; Ni, 1.91)38.

Figure 4. (A) Pt 4f and (B) Pd 3d XPS spectra of PdNi@Pt CSNSs.

Figure 4

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Methanol oxidation reaction

To study the coverage of Pt shell on PdNi@Pt CSNSs, cyclic voltammetry (CV) tests were performed in N2-purged 0.5 M H2SO4 solution. As revealed by Figure 5A, the oxide reduction peak of PdNi@Pt CSNSs (0.55 V) shifts positively ca. 90 mV compared to that of Pd-Ni ANWs (0.46 V), very close to that of Pt black (0.56 V), confirming a complete Pt shell has formed on Pd-Ni ANWs surface19. According to hydrogen adsorption−desorption method27, the ECSA of PdNi@Pt CSNSs and Pt black are measured to be 32.5, and 17.8 m2 g−1, respectively. The durabilities of PdNi@Pt CSNSs and Pt black were investigated by continuous cyclic voltammetry running. After continuous 1000 cycles, PdNi@Pt CSNSs and Pt black lost 13.5% and 32.5% of their initial ECSA, respectively (Figure 5B). Since PdNi@Pt CSNSs keep the 3D interconnected structure from the core of Pd-Ni ANWs, the particular 3D structure effectively restrains Ostwald ripening effect24,25,26, and contributes to an enhanced electrochemical stability.

Figure 5.

Figure 5

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(A) Cyclic voltammograms of PdNi@Pt CSNSs, Pd-Ni ANWs and Pt black in N2-saturated 0.5 M H2SO4 solution at a sweep rate of 50 mV s−1.(B) ECSA vs. cycle numbers of PdNi@Pt CSNSs and Pt black.

The electrocatalytic activities of Pd-Ni ANWs, Pt black and PdNi@Pt CSNSs for the MOR were investigated by CV in acidic media. No anodic current for the MOR is observed at Pd-Ni ANWs (Figure S6), indicating that Pd-Ni ANWs has no electrocatalytic activity for the MOR in acidic media. However, the obvious anodic peak for the MOR are found at both Pt black and PdNi@Pt CSNSs (Figure 6A). The onset oxidation potential of the MOR at PdNi@Pt CSNSs negatively shifts ca. 100 mV than that at Pt black, indicating that PdNi@Pt CSNSs are more kinetically effective electrocatalysts. At 0.6 V potential, Pt mass activity on PdNi@Pt CSNSs is 965 mA mg−1, much higher than that on Pt black (161 mA mg−1) and previous reports (such as Pt-Co alloy networks27: 392 mA mg−1, and FePtPd nanowires4: 450 mA mg−1), indicating that the Pt utilization can be remarkably improved by using PdNi@Pt CSNSs as electrocatalysts. Chronoamperometry technique was further carried out to investigate the electrocatalytic performance of electrocatalysts for the MOR (Figure 6B). The rate of current decay is exponential and after a long time a pseudo steady state is reached. In whole process, the MOR current on PdNi@Pt CSNSs is higher than that on Pt black, showing their high activity. The long-term stability (δ) is evaluated by measuring the linear current decay using the equation (4)27:

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Where I0 is the at the start of polarization back extrapolated from the linear current decay, and (dI/dt)t>500 s is the slope of the linear portion of the current decay. According to the equation (4), the loss rates of PdNi@Pt CSNSs and Pt black MOR activities are 0.07 and 0.12% s−1, demonstrating that PdNi@Pt CSNSs have an improved stability compared to Pt black.

Figure 6.

Figure 6

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(A) The Pt metal mass-normalized cyclic voltammograms for PdNi@Pt CSNSs and Pt black in solution of 0.5 M methanol + 0.5 M H2SO4 at 50 mV s−1. (B) Chronoamperometry curves for PdNi@Pt CSNSs and Pt black in solution of 0.5 M methanol + 0.5 M H2SO4 for 3000 s at 0.6 V potential.

Besides the effect of electrocatalyst's self-stability on durability, the effect of COads poison on electrocatalyst's durability was also investigated by CO-stripping tests. In comparison with Pt black, the onset oxidation potential and oxidation peak potential of pre-adsorbed CO at PdNi@Pt CSNSs negatively shift ca. 90 and 70 mV, respectively (Figure 7). The result demonstrates that the PdNi core has a significant effect in changing the CO tolerance of electrocatalysts. According to the d-band center theory39,40, the change in Pt 4f binding energy at PdNi@Pt CSNSs is responsible for effective removal of COads, which contributes to improved durability for the MOR. Moreover, the PdNi core can be oxidized at lower potential than Pt shell to provide OH species, which also facilities the valid removal of CO at PdNi@Pt CSNSs due to bifunctional mechanism.

Figure 7. Cyclic voltammograms of pre-adsorbed CO at PdNi@Pt CSNSs and Pt black modified electrodes in 0.5 M H2SO4 solution at 50 mV s−1.

Figure 7

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In summary, we successfully synthesized the jelly-like K2PdCl4/K2Ni(CN)4 cyanogel. Due to 3D characteristic backbone and double-metal properties of the cyanogel, Pd-Ni ANWs were obtained facilely through a simple NaBH4-reduction method at room temperature. This simple, mild and template-free cyanogel-reduction route was an attractive choice for the synthesis of the porous double metal alloy nanomaterials. Then, we utilized galvanic displacement to prepare PdNi@Pt CSNSs without any surfactant. Electrochemical measurements demonstrated that PdNi@Pt CSNSs showed enhanced electrocatalytic activity and durability for the MOR compared to Pt black, owing to the unique interconnected structure and the synergistic effect between PdNi core and Pt shell, such as electronic effect and bifunctional mechanism. This work demonstrated that PdNi@Pt CSNSs were indeed promising anodic electrocatalyst for the DMFCs.

Methods

Fabrication of PdNi ANWs and PdNi@Pt CSNSs

In a typical synthesis of PdNi ANWs, 4 mL of 50 mM K2PdCl4, and 2 mL of 50 mM K2Ni(CN)4 aqueous solutions were added into a 25-mL beaker for 10 min to generate the K2PdCl4/K2Ni(CN)4 cyanogel. Then 6 mL of 0.05 g mL−1 NaBH4 solution was dropwise added into the beaker and the K2PdCl4/K2Ni(CN)4 cyanogel was reacting violently to obtain the black Pd-Ni ANWs after 2 h. Afterwards separated with centrifugation at 18000 rpm for 8 min, dried in a vacuum oven at 45°C for 12 h, Pd-Ni ANWs were finally achieved. In a typical synthesis of PdNi@Pt CSNSs, 8 mg Pd-Ni ANWs were suspended in 20 mL water by ultrasonic concussion. Then, 0.5 mL of 0.05 M K2PtCl4 aqueous solution was added into Pd-Ni ANWs suspension at 60°C. After stirring for 6 h, the PdNi@Pt CSNSs were obtained and further separated by centrifugation at 18000 rpm for 8 min, and dried in a vacuum oven at 40°C overnight.

Characterization

The morphology and surface structure of samples were observed by JSM-2010 scanning electron microscopy (SEM) and JEOL JEM-2100F transmission electron microscopy (TEM). The composition and crystal structure of samples were investigated by energy dispersive spectrum (EDS) technique, Leeman inductively coupled plasma atomic emission spectrometry (ICP-AES), Thermo VG Scientific ESCALAB 250 X-ray photoelectron spectroscopy (XPS), and Model D/max-rC X-ray diffraction (XRD) diffractometer. The binding energy was calibrated by means of the C 1s peak energy of 284.6 eV.

Electrochemical tests

All electrochemical experiments were performed in an all-Teflon three-electrode cell by using a CHI 660 C electrochemical analyzer (CH Instruments, Shanghai, Chenghua Co.) at 30 ± 1°C. A platinum wire reacts as the auxiliary electrode, a saturated calomel electrode (SCE) reacts as reference electrode, and a catalyst modified glassy carbon electrode works as the working electrode. All potentials in this study were reported with respect to SCE. Working electrodes were prepared by sonicating the catalyst powder in water at 1.4 mg mL−1 for at least 1 h, and dispersing a 4 μL droplet onto a 3 mm glassy carbon electrode. The specific loading of total metal and Pt on the glassy carbon electrode (3 mm diameter) was about 80 μg cm−2 and 13.3 μg cm−2, respectively. CO-stripping tests were performed according to our previously reported procedure.

Supplementary Material

Supplementary Information

Supplementary Information

srep07619-s1.doc (318.5KB, doc)

Acknowledgments

This research was sponsored by National Natural Science Foundation of China (21473111, 21376122 and 21273116), Natural Science Foundation of Jiangsu Province (BK20131395), United Fund of NSFC and Yunnan Province (U1137602), Industry-Academia Cooperation Innovation Fund Project of Jiangsu Province (BY2012001), the National Basic Research Program of China (973 Program, 2012CB215500), Fundamental Research Funds for the Central Universities (GK201402016) and a project funded by the Priority Academic Program Development of Jiangsu Higher Education Institutions.

Footnotes

Author Contributions X.L. and G.X. designed the experiments and performed the materials synthesis, characterization and electrochemical measurements. Y.T. and Y.C. wrote the main manuscript text. T.H. and W.X. supervised the project, and all authors participated in the review of the manuscript.

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Supplementary Materials

Supplementary Information

Supplementary Information

srep07619-s1.doc (318.5KB, doc)

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