Preparation and Performance of a Cu@PtCu/CNF Oxygen Reduction Catalyst Membrane by Electrospinning

A flexible carbon nanofiber film with high conductivity was prepared by electrospinning, and then Cu was uniformly deposited on the fiber film by pulse electrodeposition to prepare Cu nanocrystal/carbon nanofiber film. Cu@PtCu/carbon nanofiber (Cu@PtCu/CNF) catalytic films were synthesized by in-situ substitution reduction. The Cu@PtCu/CNF catalytic film solves the problem of uneven activity of the catalytic layer and can be directly used as the catalytic layer. The morphology and structure were characterized by transmission electron microscopy (TEM), scanning electron microscopy (SEM), X-ray diffraction (XRD), and X-ray photoelectron spectroscopy (XPS). Electrochemical test results show that the Cu@PtCu/CNF catalytic films obtained at the chloroplatinic acid concentration of 0.5 mg·mL–1 (N2) exhibited 2.5 times specific activity when compared with commercial Pt/C catalysts. After 5000 cycles of stability test, the electrochemical surface areas (ECSAs) were still maintained at 80%, and the half-wave potential decreased by 11 mV, which was better than those of commercial Pt/C catalysts.


INTRODUCTION
Proton-exchange membrane fuel cell (PEMFC) is a device that directly converts chemical energy into electrical energy, which can achieve zero pollution and zero emissions in the true sense. 1 Compared with the widely used lithium-ion battery, it has the advantages of short hydrogenation time and long cruising range. The membrane electrode (membrane electrode assembly, MEA) is the core component of the fuel cell. At present, the preparation method of the membrane electrode of the fuel cell is as follows: first, prepare the catalyst slurry; then, directly coat or transfer the slurry onto the proton membrane to obtain the catalyst/proton-exchange membrane module (named catalystcoated membrane, CCM) and finally attach the gas dispersion layer to CCM to obtain membrane electrode (MEA). 2 In this process, the fuel cell catalyst must be an easily dispersible powder material, and it is difficult to achieve precise coordination of electrochemical reaction and mass transfer kinetics due to the "slurry" processing form of the catalytic layer. 3 Electrospinning can be used for large-scale preparation of nanostructured materials such as hollow nanotubes and porous nanofibers by adjusting the parameters of the spinning precursor solution, needle type, and spinning environment. 4 Onedimensional carbon materials such as carbon nanofibers (CNFs) and carbon nanotubes (CNTs) have long-range orientation, good electrical conductivity, high temperature resistance, corrosion resistance, and other properties. 5 They overlap each other to form a three-dimensional network. The structure provides a channel for the transmission of gas and liquid. The long-range continuous ultrathin nanofiber membrane is obtained by electrospinning, and then a carbon membrane is obtained through a certain carbonization treatment process. The catalyst is attached to the carrier fiber membrane to make a catalyst membrane, and the catalyst membrane and the proton-exchange membrane can be directly attached to form a CCM. 6 The cost and stability of proton-exchange membrane fuel cells limit their commercial promotion, and improving the activity and durability of cathode platinum-based catalysts is the main challenge. To this end, many researchers have developed different methods and developed catalysts such as nonprecious metal catalysts, 7 alloyed catalysts, and core−shell structures. 8 Among them, alloying is an effective method that can not only reduce the expensive platinum loading but also increase its activity by changing the extranuclear electron density of atoms on the catalyst surface with other metals. 9 The alloying of Pt-based catalysts can improve the activity of catalysts; at the same time, one-dimensional fibers can overlap each other to form a three-dimensional network structure, which is beneficial to the transport of gas, liquid, and electricity as a catalyst carrier. 10 In this study, carbon nanofiber membranes with specific structures were prepared by electrospinning, and Cu nanocrystals with reducibility and alloy structure with Pt were supported on the carbon membranes utilizing pulse electrodeposition. The deposition and distribution growth regulation process of Cu microcrystals on carbon films were studied, and then Cu@PtCu/carbon nanofiber catalytic films were prepared by the displacement method. The electrospinning method was used to prepare the PAN nanofiber membrane. First, 1.5 g of PAN was added to 13.5 g of DMF to prepare a polymeric precursor solution. Second, the precursor solution was loaded into a 10 mL syringe with a needle inner diameter of 0.41 mm ± 0.02 mm. The distance between the roller and the tip was set to 15 cm and the rotating speed was maintained at 500 rpm. The relative humidity was kept under 40% and the temperature was controlled between 35 and 40°C. The feeding rate was 0.4 mL·h −1 and the nanofibers (NFs) were collected by a piece of carbon paper under a high voltage of 20 kV. The PAN NFs membrane was stabilized for 6 h at 220°C in an air oven and carbonized for 2 h at 1600°C in Ar to prepare the CNF membrane.

Synthesis of Cu/CNF Membrane.
Pulse electrodeposition was used to deposit Cu nanocrystals on the CNF membrane. The operation process was as follows: first, the working electrode was immersed in the CuSO 4 ·5H 2 O solution for 10 min to make the CNF membrane hydrophilic by electrochemical oxidation. Then, pulse electrodeposition was performed. Reverse pulse oxidation current density was set to 15 mA·cm −2 , while the pulse conduction time (T on ) and turn-off time (T off ) were 100 and 500 μs, respectively. The peak current density was −50 mA·cm −2 , and the pulse deposition time was 20 s. After that, the CNF membrane was quickly immersed in anhydrous ethanol for 10 min to avoid air oxidation. Finally, the membrane was washed with deionized water and dried in a vacuum drying oven at 50°C to obtain the Cu/CNF membrane (Cu/CNFM).
All of the electrochemical tests were carried out by a threeelectrode system in 0.1 M HClO 4 solution at room temperature. For the preparation of catalyst ink, 2 mg of the electrocatalyst was mixed with 1.0 mL of water/isopropanol/Nafion (5 wt %) solution (volume ratios = 5:4:1), followed by sonication for 30 min. Then, 10 μL of the ink was dropped onto a rotating disk electrode (RDE, 5 mm diameter, 0.196 cm 2 ) using as a working electrode. A Pt sheet (1 cm × 1 cm) and a reversible hydrogen electrode (RHE) electrode were used as the counter electrode and the reference electrode, respectively. After saturating the solution with oxygen, cyclic voltammetry (CV) test was performed in the potential ranging from 0.05 to 1.20 V at 10 mV·s −1 . Linear sweep voltammetry (LSV) tests were performed at 20 mV·s −1 . The accelerated degradation test (ADT) was performed in the range of 0.6−1.1 V at a scan rate of 100 mV·s −1 . The commercial JM20 catalyst was measured through the same process to make a comparative analysis.
The electrochemical surface areas (ECSAs) of the catalysts were obtained by calculating the hydrogen adsorption peak area equation where Q H is the charge for H 2 adsorption from 0.05 to 0.4 V vs RHE. 11 The kinetic current density (j k ), mass activity (MA), specific activity (SA) can be calculated by the following equation where j is the measured current density and j d is the measured limiting current density.  Figure 1a shows that the prepared membrane has a smooth surface and can be bent at a right angle, which indicates the flexibility of the CNF membrane. Figure 1b shows that carbon nanofibers are continuous in the long range and can be interlinked to form a three-dimensional network structure, which is conducive to the transmission of gas, liquid, and electricity. Figure 1c shows that the fibers are about 150 nm in diameter, providing a large surface area to support the active material. Figure 1d shows that the cross-sectional thickness of the fiber membrane is about 4 μm, and its use as an integrated catalytic membrane is conducive to reducing the transport distance between the reactants and products, thus reducing the concentration polarization. Figure 2 shows the morphology of Cu/CNFM and Cu@ PtCu/CNFM prepared by different concentrations of chloroplatinic acid. The SEM images show that with the increase in the concentration of chloroplatinic acid, the metal particle coverage rate on the fiber surface increases, and the fiber surface becomes rougher. The increase in the concentration of the Pt 4+ can accelerate the replacement reaction, thus increasing the Ptloading capacity on the fiber surface. Figure 3 shows TEM images at different multiples and highresolution lattice images of Cu@PtCu/CNFM (N2) and commercial catalyst JM20. Figure 3a shows that the surface of each fiber is uniformly covered with metal particles of uniform size, and some of them are distributed in clusters. As shown in Figure 3b, the lattice spacing is measured at about 0.222−0.224 nm. Compared with the crystal plane spacing of the pure Pt catalyst JM20 (0.232 nm), its crystal lattice shrinks, and it is closer to the (111) plane crystal spacing of the PtCu alloy of 0.2191 nm, 13 which indicated the formation of the PtCu alloy.

RESULTS AND DISCUSSION
The element distribution of Cu@PtCu/CNFM was analyzed by mapping. As shown in Figure 4, Cu and Pt are uniformly    distributed on the fibers and their locations coincide, indicating that the PtCu alloy structure is formed in the shell layer. The carbon serves as catalyst support and is doped with nitrogen harmoniously. The nitrogen is mainly derived from PAN in the precursor solution. Figure 5 compares the XRD spectra of N1, N2, N3, and Cu/ CNFM. The characteristic peak of Cu@PtCu/CNFM at 41.1 and 47.8°corresponds to the (111) and (200) crystal planes of PtCu alloy. 14 In addition, with the increase in the concentration of Pt 4+ , the characteristic peak of PtCu in the XRD pattern becomes sharp, indicating that the grain size increases due to the high concentration of Pt 4+ , which easily reduces the active surface area of the catalyst. In addition, the characteristic peak of the copper oxide facies phase in N1 indicates that the oxide layer on the surface of copper nanocrystals cannot be removed under the low concentration of chloroplatinic acid. However, when the concentration of chloroplatinic acid increases to 0.5 mg·mL −1 , the characteristic peak of the copper oxide disappears, indicating that the increase in the concentration of chloroplatinic acid is conducive to the etching of Cu oxide.      To characterize the chemical valence state of Pt in different electrocatalysts, XPS was performed. The result shows that the Pt 4f 7/2 of N1 (71.54 eV) and N2 (71.59 eV) samples shift toward lower binding energy relative to JM20 (71.95 eV) ( Figure 6). This is because the formation of an alloy structure of Pt and Cu changes the electronic structure on the surface of the active substance. The transfer of the Cu surface electron to the Pt surface can enhance the peak potential of oxygen reduction and inhibit the oxidation of Pt, which is conducive to the positive regulation of catalytic activity of the catalyst. 14b The fitting data of different states of Pt is shown in Table 1. Among them, the increase in Pt(0) is generally beneficial to the improvement in catalytic activity. Table 1 shows that the Pt(0) content of N1 is less than that of N2, and its Pt(IV) content is higher, indicating that the reduction degree of Pt in N1 is not as high as that of Pt in N2, and Pt is more attached to the membrane surface in the form of ion adsorption. This is due to the fact that some Cu nuclei oxide layers are not eroded and opened under N1 concentration (discussed in XRD analysis), which reduces the reduction degree of Pt. However, when the concentration is too high (N3), the content of Pt(0) decreases instead, which may be due to the consumption of large amounts of Cu nanocrystalline nuclei in the early stage of the replacement reaction. The replaced Pt constantly covers the surface of Cu nanocrystals, which slows down the reaction in the later stage and makes it difficult to reduce the adsorbed Pt 4+ .
It can be seen from Figure 7 that the *OH adsorption peaks of N1 (0.809 V), N2 (0.803 V), and N3 (0.792 V) have a positive shift relative to JM20 (0.766), which reflects that they have a lower chemical adsorption energy for *OH. This is conducive to the increase in oxygen reduction activity. The ECSA results calculated by normalization are shown in Table 2. The table shows that the ECSA of JM20 (84 m 2 ·g −1 ) is higher than that of N1 (36 m 2 ·g −1 ), N2 (37 m 2 ·g −1 ), and N3 (34 m 2 ·g −1 ), which is due to the smaller diameter of active nanometal particles of JM20. It is worth mentioning that the CV curve of N2 does not have the oxidation peak of Cu crystals at 0.25 V, indicating that the shell structure formed in the PtCu alloy has good coverage of the internal Cu, which can effectively prevent the loss of Cu cores and help maintain its activity during the operation.
The electrochemical properties of each sample are shown in Table 2. It shows that the onset potential (E on ) and the half-wave potential (E 1/2 ) of the as-prepared catalysts are higher than that of JM20. Meanwhile, the values of MA of N1 (0.090 A·mg −1 ), N2 (0.087 A·mg −1 ), and N3 (0.082 A·mg −1 ) are higher than that of JM20 (0.080 A·mg −1 ). Among them, the electrochemical properties of N2 are the best, and the excellent performance of the sample can be explained by the appropriate Pt−Cu ratio, which can increase the electron-donating ability of Pt nanoparticles and promote the ORR process.
The electrochemical stability of a catalyst is an important index. The decreasing trend of the ECSA calculated for JM20, N1, N2, and N3 catalysts is shown in Figure 8. It shows that the ECSA of each sample decreases during ADT. The ECSA values of self-made catalysts decreased by 26, 19, and 12%, respectively, lower than that of JM20 (29%). The best durability of N3 may be due to the low reducibility of Pt on the N3 surface (as analyzed in XPS), which can be reduced in the cyclic stability test and partially offset the negative effects caused by Ostwald ripening. Figure 8 shows the CV curves and LSV curves of JM20, N1, N2, and N3 before and after 5000 cycles. After 5000 cycles, the E 1/2 of N1, N2, and N3 shifted negatively by 9, 11, and 22 mV, respectively, lower than that of JM20 (43 mV), and the CV curves of N1 and N2 coincide well with those before the cycles, indicating the better stability of N1 and N2, which is beneficial to its application in practical fuel cells. However, the decline in E 1/2 of N3 is relatively large, which may be because the lack of Cu made it difficult to form an alloy structure at this stage.

CONCLUSIONS
The Cu@PtCu/CNFM prepared at the concentration of 0.5 mg·mL −1 chloroplatinic acid has the best catalytic performance, with the mass specific activity 1.125 times and the area specific activity 2.5 times as much as those of JM20, and has the best electrochemical stability. After 5000 cycles of ADT, its ECSA only dropped by 19%, better than those of commercial catalysts. This study provides a new method to prepare an integrated catalytic layer with high electrochemical performance.