Cu2Se Nanoparticles Encapsulated by Nitrogen-Doped Carbon Nanofibers for Efficient Sodium Storage.

Cu2Se with high theoretical capacity and good electronic conductivity have attracted particular attention as anode materials for sodium ion batteries (SIBs). However, during electrochemical reactions, the large volume change of Cu2Se results in poor rate performance and cycling stability. To solve this issue, nanosized-Cu2Se is encapsulated in 1D nitrogen-doped carbon nanofibers (Cu2Se-NC) so that the unique structure of 1D carbon fiber network ensures a high contact area between the electrolyte and Cu2Se with a short Na+ diffusion path and provides a protective matrix to accommodate the volume variation. The kinetic analysis and DNa+ calculation indicates that the dominant contribution to the capacity is surface pseudocapacitance with fast Na+ migration, which guarantees the favorable rate performance of Cu2Se-NC for SIBs.

1. Introduction

Sodium-ion batteries (n class="Chemical">SIBs) have garnered tremendous attention due to the low price and abundance of sodium resources, and are considered as one of the promising alternatives to commercial lithium-ion batteries [1,2,3]. However, the large ionic radius of Na+ causes huge volume variation during Na+ insertion/extraction, which results in sluggish reaction kinetics and undesirable electrochemical performance [4,5]. Thus, the exploration of suitable electrode materials is still a great challenge for effective and reversible accommodation of large Na+ for wide-scale practical application of SIBs [6,7].

Among various potential electrode material candidates for n class="Chemical">SIBs, metal selenides have attracted particular attention because of good electronic conductivity and high reversible capacity based on multielectron conversion reactions [8,9]. Lou et al. prepared Cu-doped CoSe2 microboxes with high reversible capacity of 492 mAh g−1, excellent rate capability and long cycling life [10]. Yang and co-workers synthesized a 3D trilayer (CNT/MoSe2/C) as freestanding electrodes with high areal capacity (4.0 mAh cm−2) and promising cycling stability [11]. Compared to MSe2 with high Se content, M2Se such as Cu2Se with an inactive Cu component has the advantages of high electronic conductivity, structural stability and low volume variation during cycling [12,13,14]. However, most of these alternatives suffer from large volume changes during the conversion reaction with unsatisfied electrochemical performances [15,16]. As an effective approach, designing nanostructured materials can increase the active sites and specific surface area, further improving the reaction kinetics and reversible specific capacity [17]. Nevertheless, nanomaterials tend to agglomerate during cycling, which still prevents the long-term cycle life of the batteries. To solve these issues, the common tactic is to synthesize metal selenide/carbon nanocomposites [18]. Nanosized active materials uniformly dispersed in carbon matrix can effectively inhibit aggregation of the nanoparticles and alleviate the volume expansion caused by Na+ insertion [19,20,21].

In this paper, Cu2Se nanoparticles are embedded in 1D n class="Chemical">nitrogen doped carbon nanofibers (Cu2Se-NC). The unique structure of 1D carbon fiber can shorten the Na+ diffusion path with a high contact area between Cu2Se and the electrolyte. Meanwhile, carbon conductive network provides a buffering matrix for the effective accommodation of volume variation and alleviates the aggregation of Cu2Se nanoparticles to maintain the structural integrity during repeated cycling. Based on the these favorable effects, Cu2Se-NC displays a promising rate capability and long-term cycling life for efficient sodium storage.

2. Experimental Section

2.1. Preparation of Cu2Se-NC Nanofibers

A solution containing 10 mL dimethylformamide (n class="Chemical">DMF, Aladdin, Shanghai, China), 0.4 g Cu(CH3COO)2·H2O (Aladdin), and 0.8 g polyacrylonitrile (PAN, MW = 150,000, Aldrich, St. Louis, MO, USA) was vigorous stirred for about 12 h, which was then loaded into a 20-mL syringe with 19-G needle for electrospinning. The electrospinning process was applied voltage of 1 kV cm−1 with flow rate of 10 μL min−1. After electrospinning, the collected Cu(AC)2/PAN nanofibers were selenized with Se powder (amass ratio of 1:2) in tube furnace at 500 °C for 4 h (Ar/H2 atmosphere, heating rate: 2 °C min−1) to obtain Cu2Se-NC. The Cu2Se and nitrogen doped carbon nanofibers (NC) were acquired through the similar treatment procedure by using Cu(AC)2 with Se powder and PAN nanofibers, respectively.

2.2. Material Characterization

Field emission scanning electron microscope (FEn class="Chemical">SEM, ZEISS Ultra 55, Carl Zeiss Inc., Oberkochen, Germany) and transmission electron microscope (TEM, JEM-2100F, JEOL Ltd., Tokyo, Japan) were used to observe morphology and structure. X-ray diffraction patterns (XRD, Bruker D8 Advance, Karlsruhe, Germany) and X-ray photoelectron spectroscopy (XPS, PHI 5600, Physical electronics, Chanhassen, MN, USA) were conducted to analyze the phase structure and chemical composition, respectively. Thermal gravimetric analysis (TGA, SDT Q600 TG-DTA, TA Instruments-Waters LLC, New Castle, DE, USA) was performed from room temperature to 600 °C (air, 10 °C min−1).

2.3. Electrochemical Measurements

The slurry composed of 80 wt% active material, 10 wt% n class="Chemical">Super P, 10 wt% polyvinylidene fluoride (PVDF) dispersed in appropriate N-methyl-2-pyrrolidone (NMP) was cast onto copper foil as electrode with active material loading of about 0.8~1.0 mg cm−2. The electrolyte was 1 M NaClO4, which dissolved in a solution of ethylene carbonate (EC) and dimethyl carbonate (DMC) with volume ratio of 1:1 as well as additive of 5 wt% fluoroethylene carbonate (FEC). The electrochemical performances tests were measured by a Neware battery testing system in a voltage window of 0.1~3.0 V. Cyclic voltammetry (CV) and electrochemical impedance spectroscopy (EIS) conducted on an electrochemical workstation (BioLogic VMP3, Bio-Logic, Seyssinet-Pariset, France).

3. Results and Discussion

As shown in Figure 1a, the morphology of the as-electrospun n class="Chemical">Cu(AC)2/PAN is composed of highly uniform and smooth nanofibers with diameter of ~200 nm. The selenized nanofibers maintained the 1D structure, where Cu2Se nanoparticles are uniformly distributed in the carbon nanofibers (Figure 1b,c). The appropriate void space between as-prepared Cu2Se-NC nanofibers is beneficial to the penetration of electrolyte. The low-resolution TEM images reveal that Cu2Se nanoparticles were homogenously embedded in the carbon nanofibers in Figure 1d, and further confirm the structural feature of Cu2Se-NC, agreeing well with the SEM results. A high-resolution TEM (HRTEM) image reveals the crystal phase of Cu2Se possess good crystallinity, and the lattice spacing of 0.204 nm is ascribed to the (220) crystal plane of Cu2Se (Figure 1e). Additionally, the selected area electron diffraction (SAED) of Cu2Se-NC indicates the formation of Cu2Se with polycrystallinity (Figure 1f). SEM image and corresponding EDX mapping results shown in Figure 1g,h reveal the uniform distribution of Cu, Se, N, and C throughout the nanofibers. However, bulk Cu2Se is composed of irregular nanoparticles in the absence of carbon nanofiber support (Figure S1).

Figure 1

(a) SEM image of Cu(AC)2/PAN electrospun nanofibers; (b,c) SEM and (d) TEM images of Cu2Se-NC nanofibers after selenization treatment; (e) HRTEM image of Cu2Se-NC nanofibers. (f) Selected-area electron diffraction patterns of Cu2Se-NC nanofibers. (g) SEM image and (h) corresponding elemental mappings of Cu, Se, N, and C of Cu2Se-NC.

The X-ray diffraction (XRD) pattern of as-prepared Cu2Se-NC is displayed in Figure 2a. The major diffraction peaks at 26.8, 31.0, 44.5, 52.6, 64.7 and 81.9° are ascribed to (111), (200), (220), (311), (400) and (422) lattice planes of n class="Chemical">Cu2Se (JCPDS No. 65-2982), which proves successfully synthesis of Cu2Se phase. In addition, a sharp and strong (220) peak indicates significantly crystallinity and in good agreement with the HRTEM and SAED characterization for Cu2Se–NC. As shown in the thermogravimetric analysis (TGA, Figure 2b), the weight change could be divided to several steps: (i) the temperature between 30 to 120 °C is likely due to the evaporation of water remaining; (ii) the 49.4% weight loss from 340 to 410 °C is attributed to the carbon combustion; (iii) the range of 410~550 °C could be estimated from the oxidation of Cu2Se into CuO, whereby the content of 29% is Cu2Se for Cu2Se–NC composite [22]. The elemental composition and valence state of Cu2Se–NC were investigated by XPS analysis (Figure S2a). In the high-resolution Cu 2p spectrum (Figure 2c), the peaks at 952.4 and 932.6 eV are attributed to Cu+ in Cu2Se, and the peak at 954.4 and 934.6 eV could be assigned to the presence of Cu2+ in surface oxidized CuO [15,23]. For the XPS spectrum of Se 3d (Figure 2d), two major peaks located at 55.5 eV (Se 3d3/2) and 54.2 eV (Se 3d5/2) are ascribed to Cu-Se bonds [24]. The O 1s spectra (Figure S2b) shows the peaks with binding energies of 532.4, 531.4 and 530.6 eV can be associated with absorbed water, C–O bond and Cu–O bond for Cu2Se–NC, respectively [25]. The N 1s spectrum (Figure S2c) is deconvoluted into representative peaks centered at 401.5, 400.0, 398.9 and 398.3 eV, attributing to oxidized-N, graphitic-N, pyrrole-N and pyridine-N, further confirming the successful nitrogen doping into Cu2Se–NC composite [26]. The C 1 s region (Figure S2d) is assembled in four components for the C–O (289.2 eV), C–N (286.3 eV), sp3 C–C (285.2 eV) and sp2 C=C bonds (284.6 eV) [27]. The existence of a carbon framework can improve the electronic conductivity and inhibit effectively volume expansion, which is favorable for fast electron transfer and structural stability during repeated cycling.

Figure 2

(a) XRD pattern of Cu2Se-NC; (b) TGA spectra of Cu2Se-NC; XPS spectra of (c) Cu 2p; (d) Se 3d of the Cu2Se-NC, respectively.

Figure 3a displays the CV curves of the n class="Chemical">Cu2Se-NC. At around 0.21 and 0.85 V of reduction process in the initial CV curve, there are obviously irreversible peaks, corresponding to the irreversible reduction of electrolyte and the formation of solid electrolyte interphase (SEI) film [28]. In the subsequent cycles, the broad reduction peak at ~0.7 V might be assigned to the formation of Na2Se, and the two oxidation peaks at 0.45 and 1.55 V are assigned to the extraction of Na+ from Na2Se. The CV curves are well overlapped from the second cycle, demonstrating excellent electrochemical reversibility of the Cu2Se–NC electrode. Figure 3b shows the charge–discharge profiles of the initial four cycles of Cu2Se–NC electrode at a current density of 0.1 A g−1. The Cu2Se–NC electrode yields a first discharge/charge specific capacity of 412/192 mAh g−1, which was higher than those of Cu2Se (Figure S3, 322/189 mAh g−1) and NC (Figure S4, 269/73 mAh g−1). The initial Coulombic efficiency of Cu2Se–NC electrode is 46.6%, which is consistent with the CV test results [29]. The cycling performance of the Cu2Se–NC, Cu2Se and NC anode for SIBs at a current density of 0.1 A g−1 is shown in Figure 3c. Cu2Se–NC maintains a reversible capacity of 172 mAh g−1 after 200 cycles. However, the capacity of Cu2Se is sharply decreased to 10 mAh g−1 from 189 mAh g−1 after 10 cycles, suggesting 1D carbon fiber network provides more stable structure networks for accommodation of volume expansion to ensure cycling stability. The specific capacity of NC is only 70 mAh g−1 due to the sluggish reaction kinetics of NC for SIBs.

Figure 3

(a) Cyclic voltammograms of the Cu2Se–NC for the initial four cycles; (b) Charge/discharge curves of the Cu2Se–NC; (c) Cycling performance and of the Cu2Se–NC and Cu2Se and NC at 0.1 A g−1; (d) Rate capability of the Cu2Se–NC at various current densities; (e) Long cycling performance of the Cu2Se–NC at 2 A g−1.

The rate performance of the Cu2Se–NC, n class="Chemical">Cu2Se and NC anode is illustrated in Figure 3d. The Cu2Se–NC electrode exhibits a high specific capacity of 193, 176, 148, 126, and 99 mAh g−1 at the current densities of 0.1, 0.2, 0.5, 1, and 2 A g−1. The specific capacity of 188 mAh g−1 can be obtained, when current density is returned to 0.1 A g−1, revealing the outstanding reversibility of the Cu2Se-NC. While the capacity of Cu2Se and NC decreases to only 3 and 24 mAh g−1 at 2 A g−1, indicating a significant enhancement of the electrochemical performance resulting from nanosized-Cu2Se embedded 1D nitrogen doped carbon nanofibers. Moreover, as depicted in Figure 3e, the Cu2Se–NC also exhibits favorable long-term cycling performance. After activation for five cycles, the Cu2Se–NC anode shows capacity retention of 99% (101 mAh g−1) after 2000 cycles, further implying the strong stability of the 1D nanofiber structure.

The kinetic analysis was investigated to further explain the excellent rate capability of Cu2Se–NC. Figure 4a depicts the CV n class="Chemical">curves at various sweep rates (from 0.2 to 1.0 mV s−1). The relationship between the peak current (i.e., mA) and sweep rate (v, mV s−1) and obeys the equation of i = av that b value of 0.5 or 1.0 implies diffusion-controlled or capacitive-controlled processes, respectively [30,31]. The b value is identified by the slopes of log (i) vs. log (v) in Figure 4b. The Cu2Se–NC possesses high b values for both cathodic (0.86, 0.84) and anodic (0.74, 0.78) peaks, indicating the surface capacitive-controlled processes. This is responsible for the fast reaction kinetics and ensures considerable rate performance. To qualify the predominated storage capacity contribution, the capacity can be divided into capacitive (k1) and diffusion (k2) according to i = k (i/υ) [32,33]. As shown in Figure 4c, the capacitive contributions of Cu2Se–NC at 0.6 mV s−1 are calculated as 64.9%, which indicates that Cu2Se–NC possesses fast Na+ intercalation/deintercalation. Furthermore, Figure 4d displays the surface pseudocapacitive contribution in the Cu2Se–NC increases to 72.6% as the sweep rate elevates to 1.0 mV s−1. The high ratio of surface capacitive contribution is beneficial to the rate performance, which agrees with the favorable rate capability of Cu2Se–NC (Figure 3d).

Figure 4

(a) CV curves at various scan rates of the Cu2Se-NC (0.2, 0.4, 0.6, 0.8 and 1.0 mV s−1); (b) log(i)-log(v) plots of the Cu2Se-NC; (c) capacitive contribution and diffusion contribution at 0.6 mV s−1; (d) capacitive and diffusion contribution versus scan rate of Cu2Se-NC.

The EIS curves and equivalent eln class="Chemical">ectrical circuit of Cu2Se–NC and Cu2Se are shown in Figure 5 and inset. Before cycling, the charge-transfer resistance (R) of Cu2Se–NC and Cu2Se is 1225 and 242 Ω, which decreases to 130 Ω and increases 466 Ω after 100 cycles, respectively. The decrease in resistance of Cu2Se-NC electrode is due to the activation process during repeated cycling, resulting in faster electron transfer for SIBs. In contrast, the R of the Cu2Se increased significantly R after cycles, which might be ascribed to cracking and pulverization of Cu2Se caused by volume expansion. The diffusivity coefficient of sodium ions (D) is obtained by EIS measurements based on D = R(2n) and Z′ = R equations [34]. Here, ω is the low range angular frequency of EIS, and b is the Warburg factor that is the slope of the line Z′ ~ ω. Obviously, the slope b of Cu2Se–NC is much lower than that of Cu2Se after cycled, and the sodium-ion diffusion coefficient of Cu2Se–NC and Cu2Se are calculated as ~3.4 × 10−21 and 5.4 × 10−22 cm2 s−1, respectively. The higher D of Cu2Se–NC electrode indicates fast diffusion kinetics for sodium storage.

Figure 5

EIS data of Cu2Se–NC and Cu2Se electrodes at a current density of 0.1 A g−1 (a) before cycling, (b) after 100 cycles; the relationship plot between Z′ and ω in the low-frequency region of (c) before cycling, (d) after 100 cycles.

To further prove the structural stability of the electrode, we investigate the morphologies of the n class="Chemical">Cu2Se–NC and Cu2Se electrode before and after 100 cycles. As illustrated in Figure 6a,b, the cycled Cu2Se–NC electrode is flat with regular nanofibers, which is similar to their original morphology (Figure S5a,b). Meanwhile, the EDS mapping of the cycled Cu2Se–NC electrode in Figure S6 shows uniform distribution of Cu, Se, N, and C in the nanofiber, demonstrating superior structural integrity during long-term cycling. In contrast, Figure 6c and d shows that the structure of cycled Cu2Se has collapsed into dense and massive bulk, which is in accordance with the rapid capacity decay. These results represent that 1D carbon fiber networks can maintain the superior structural integrity and strong tolerance of volume changes. Ex situ XRD analysis is performed to identify the Na-storage mechanism (Figure S7). The Cu2Se (220) peak could be detected in the pristine Cu2Se-NC electrode. When it is discharged to 0.1 V, two new peaks at 43.3° and 44.1° ascribe to (111) plane of Cu (JCPDS No. 04-0836) and (042) plane of Na2Se (JCPDS No. 47-1699), which indicates the insertion of Na+ into Cu2Se and the formation of Cu and Na2Se. After recharging to 3 V, the XRD pattern displays similar signals for Cu peak, which might be attributed to the irreversible reactions. Moreover, the Cu2Se (220) peak could not restore to the pristine state that could be due to crystalline Cu2Se to amorphous state, providing more active sites and fast reaction kinetics.

Figure 6

SEM images of (a,b) Cu2Se-NC and (c,d) Cu2Se electrode after 100 cycles.

4. Conclusions

In summary, Cu2Se–NC was successfully fabricated and evaluated as anode materials for n class="Chemical">sodium storage. Corresponding CV kinetic analysis and DNa+ calculation indicates the Cu2Se–NC possesses dominant surface pseudocapacity contribution and fast Na+ migration, which ensures favorable rate performance for SIBs. Moreover, the carbon fibers networks afford a conductive and protective layer for the effective accommodation of volume changes to ensure their superior long cycle life. Thus, the as-prepared Cu2Se–NC electrode displays enhanced sodium storage properties with the high reversible capacity of 172 mAh g−1 (0.1 A g−1), considerable rate capability of 99 mAh g−1 (2 A g−1) and ultra-long cycling stability (99% capacity retention over 2000 cycles).