Solvothermal preparation of spherical Bi2O3 nanoparticles uniformly distributed on Ti3C2Tx for enhanced capacitive performance

Ti3C2Tx is a promising new two-dimensional layered material for supercapacitors with good electrical conductivity and chemical stability. However, Ti3C2Tx has problems such as collapse of the layered structure and low pseudocapacitance. In this paper, we propose Bi2O3–Ti3C2Tx nanocomposites prepared by a solvothermal method, study the impact of Bi2O3 loading on the phase state and microstructure, and evaluate the electrochemical performance of Bi2O3–Ti3C2Tx. Studies have shown that spherical Bi2O3 particles were uniformly dispersed in the interlayer and surface of Ti3C2Tx, which enlarged the interlayer spacing of the Ti3C2Tx and increased the pseudocapacitance. When the mass percentage of Bi2O3 and Ti3C2Tx was 30% (TB30), the specific capacity of TB30 was as high as 183 F g−1 at a current density of 0.2 A g−1, which was about 2.8 times that of Ti3C2Tx (TB0). Moreover, a typical asymmetric supercapacitor device assembled with TB0 as the positive electrode and TB30 as the negative electrode exhibited a high energy density of 3.92 W h kg−1 and a maximum power density of 36 000 W kg−1 and maintained 77.4% of the initial capacitance after 5000 cycles at a current density of 2 A g−1. Therefore, the Bi2O3–Ti3C2Tx as the negative electrode of supercapacitor has broad application prospects in the field of energy storage.


Introduction
With the rapid development of the global economy, fossil fuel consumption continues to increase, causing serious environmental pollution. The search for efficient, clean and sustainable renewable energy and energy storage technologies has become an important research area. 1 At present, common electrochemical energy conversion and storage technologies include lithium-ion batteries, fuel cells, and supercapacitors. Supercapacitors have wide application potential because of their combined advantages of high power density, fast charging and discharging, long cycle lifetime and environmental friendliness. [2][3][4] The performance of supercapacitors is mainly inuenced by the electrolyte, separator, electrode materials and packaging technology, among which the electrode materials determine the energy density. 5,6 Different electrode materials correspond to different energy storage mechanisms. Supercapacitors can be divided into electrochemical double-layer capacitors (EDLCs) and pseudocapacitors (PCs). EDLCs rely on the electrostatic interactions between the electrode and electrolyte to store charge, and PCs rely on the highly reversible redox reaction on the electrode surface to store energy. 7,8 The ideal electrode material should have a large specic surface area, large interlayer spacing, excellent hydrophilicity, great stability, good conductivity and high pseudocapacitance.
Common electrode materials include carbon materials, metal oxide materials and conductive polymer materials. [9][10][11][12][13] Ti 3 C 2 T x is a new class of electrode material with high specic surface area, high hydrophilicity, good electrical conductivity and high chemical stability, with a layered structure similar to graphene, and has received widespread attention since its discovery in 2011. 14 There are surface defects and porous structure aer the corrosion of Ti 3 C 2 T x by HF. The defects would be benecial for increasing the contact area with the electrolyte. Therefore, the surface defects and porous structure provide large accessible surface area for cation intercalation 15 and abundant active sites for the oxygen reduction reactions, 16 facilitates easy charge-carrier transport, leading to enhanced electrochemical performance. These characteristics provide high electrode double-layer capacitance, pseudocapacitance, and reaction planes, making Ti 3 C 2 T x suitable as an electrode material for supercapacitors. However, studies have found that the collapse of the layered structure and the small pseudocapacitance are the main factors limiting the performance of Ti 3 C 2 T x electrode materials. 17,18 An effective way to improve the performance is to introduce pseudocapacitive materials such as MnO 2 , 19 TiO 2 , 20 and polypyrrole 21 into the Ti 3 C 2 T x interlayer. 22 Enlarging the interlayer spacing of Ti 3 C 2 T x makes it conducive for a variety of ions, such as Na + , K + , NH 4 + , to reversibly enter the material to achieve charge storage and better pseudocapacitance. 12,28 For instance, Yuan et al. 19 successfully introduced MnO 2 , with good pseudocapacitive performance, into the Ti 3 C 2 T x layers, which effectively prevented layer stacking and exhibited higher specic surface area than Ti 3 C 2 T x . The MnO 2 /Ti 3 C 2 T x showed a specic capacitance of 254 F g À1 (0.5 A g À1 ). Zhu et al. 21 studied a new way to enhance structural stability and interlayer spacing of Ti 3 C 2 T x by forming a freestanding and conductive thin lm through intercalating polypyrrole into layered Ti 3 C 2 T x electrodes modied by polypyrrole. The results showed that due to the modication of polypyrrole, the surface capacitance of Ti 3 C 2 T x reached 203 mF cm À2 , and aer long term cycling (20 000 cycles), there was no obvious capacity degradation. Bismuth oxide (Bi 2 O 3 ) is a pseudocapacitive material with excellent comprehensive performance owing to its high theoretical capacitance (1370 F g À1 ), suitable potential window, low cost and non-toxicity. 23 Recent studies have shown that Bi 2 O 3 can be used as an electrode material for supercapacitors. Furthermore, its electrochemical performance has been improved by combining with other electrode materials based on carbon and transition metal oxides, such as carbon nanotubes, 24 graphene 25 and MnO 2 . 26 Thus, we expect that Bi 2 O 3 would show an affinity for Ti 3 C 2 T x -based materials, which has not yet been reported in literature. In this work, we report a series of novel Bi 2 O 3 -Ti 3 C 2 T x nanocomposites prepared by a facile solvothermal reaction. Bi 2 O 3 was evenly loaded onto the interlayer and surface of Ti 3 C 2 T x , which successfully increased the interlayer spacing, stabilized the layered structure, and signicantly improved the electrochemical performance. This work demonstrates that Bi 2 O 3 -Ti 3 C 2 T x nanocomposites have an enhanced performance compared to pure Ti 3 C 2 T x 2. Experimental section 2.1 Fabrication procedures Ti 3 C 2 T x substrate. Initially, 5 g of Ti 3 AlC 2 was slowly immersed in 60 mL of 40 wt% HF solution under magnetic stirring (700 rpm) for 24 h at room temperature. Aer cooling down to room temperature, the reaction products were washed several times with deionized water and absolute ethanol to pH >6. Finally, the products were dried at 60 C for 12 h to obtain Ti 3 C 2 T x matrix material. Bi 2 O 3 -Ti 3 C 2 T x nanocomposite. Bi(NO 3 ) 3 $5H 2 O was used as the bismuth source, with ethylene glycol and ethanol as solvents and Ti 3 C 2 T x as the substrate. Bi(NO 3 ) 3 $5H 2 O and Ti 3 C 2 T x were added into a mixed solution consisting of ethanol and ethylene glycol with 10 min of magnetic stirring and 30 min of ultrasonication to form a suspension. Then, the suspension was transferred into a 100 mL Teon container and placed in a stainless steel autoclave for a solvothermal reaction at 160 C for 5 h. Aer the reaction, the suspension was taken out, washed and dried to form a precursor. Finally, the precursor was put in a tube furnace for annealing at 300 C for 2 h in N 2 atmosphere to obtain the Bi 2 O 3 -Ti 3 C 2 T x nanocomposite. By adjusting the ratio of Bi(NO 3 ) 3 $5H 2 O to Ti 3 C 2 T x , Bi 2 O 3 -Ti 3 C 2 T x nanocomposites with different Bi 2 O 3 contents, i.e., 0%, 10%, 20%, 30% and 40%, were prepared. The resulting samples are referred to as TBn, where T represents Ti 3 C 2 T x , B stands for Bi 2 O 3 , and n is the mass percentage of Bi 2 O 3 and Ti 3 C 2 T x . Table  1 shows the proportion of raw materials used for preparing TBn. Fig. 1 schematically illustrates the preparation steps for the Bi 2 O 3 -Ti 3 C 2 T x nanocomposites. The ionic interaction between negatively charged groups, such as -F, -O, and -OH functional groups at the surface and interlayer of Ti 3 C 2 T x and positively charged Bi 3+ cations, resulting in an even distribution of Bi 3+ on Ti 3 C 2 T x to form Bi 3+ -Ti 3 C 2 T x intermediates. 41 The formation of Bi 2 O 3 -Ti 3 C 2 T x can be achieved during the solvothermal process. The uniform distribution of Bi 2 O 3 at the surface and interlayers of Ti 3 C 2 T x can effectively prevent layer stacking, signicantly increase the contact area between Bi 2 O 3 and Ti 3 C 2 T x , improve the electronic conductivity, and accelerate the rapid transfer of electrolyte ions, resulting in an increase in the electric double layer capacitance and intercalation pseudocapacitance.

Materials characterization
The crystal phases of the products were analyzed by X-ray diffraction (XRD) with Cu Ka radiation (Rigaku, D/max-RB12, Japan). X-ray photoelectron spectroscopy (XPS, PHI-5300) was used to investigate the chemical valence composition of the surface elements of the product. The morphology and particle size distribution of the as-prepared samples were investigated using eld emission scanning electron microscopy (SEM, Zeiss, ULTRA 55, German). Transmission electron microscopy (TEM, FEI, Tecnai G2 F20, USA) was used to investigate the high resolution topography and electron diffraction.

Electrochemical performance measurements
All electrochemical performance measurements were carried out on the electrochemical workstation (CHI760E, Shanghai Chenhua). The working electrode was prepared with TBn and acetylene black, which were ground and mixed uniformly. The mixture was added to an NMP solution with a PVDF content of 60% for ultrasonic dispersion to form a slurry, where the mass ratio of TBn, acetylene black and PVDF was 8 : 1 : 1. The slurry was uniformly coated onto the nickel current collector foam and dried at 80 C for 12 h. The loading of TBn was about 2 mg cm À2 . The electrochemical performance of the single electrodes was evaluated by the typical three-electrode system conguration. The 6 M KOH solution served as the electrolyte, with Ag/ AgCl as the reference electrode, the platinum sheet as the counter electrode, and TBn as the working electrode. Cyclic voltammetry (CV) curves were collected at different scan rates of 5, 10, 20, 50, 100, and 200 mV s À1 , within a voltage window range of À1 to À0.4 V. Galvanostatic charge/discharge (GCD) curves were measured at different current densities of 0.2, 0.5, 1, 2, 5 and 10 A g À1 . Alternating current electrochemical impedance spectroscopy (EIS) was performed between 0.01À100000 Hz at open circuit voltage with an amplitude of 5 mV.
The specic capacity (C m ) values of the working electrodes determined from CV were calculated according to eqn (1), and the C m derived from GCD was calculated according to eqn (2). (1) where C m (F g À1 ) is the specic capacity, I (A) is the current, v (V s À1 ) is the potential scan rate, m (g) is the mass of active materials, DV (V) is the working potential window, and Dt (s) is the discharge time.
Asymmetric supercapacitors (ASC) using the two-electrode system were used for evaluating the electrochemical performance. The outer shell consisted of a CR2032 battery case; the anode and cathode used were TB0 and TB30, respectively, with 6 M KOH as the electrolyte and a polypropylene separator. In order to balance the charge of the two electrodes, the best mass ratio of the anode and the cathode were calculated according to eqn (3).
where m + and m À are the masses of the anode and cathode, respectively. C m+ and C mÀ are the specic capacitance of the anode and cathode, respectively. DU + and DU À are the potential windows of the anode and cathode, respectively. The energy density and power density were calculated according to eqn (4) and (5), respectively.
where E (W h kg À1 ) is the energy density, P (W kg À1 ) is the power density, m (g) is the mass of the active material, DV (V) is the voltage change of the discharge, Dt (s) is the discharge time, and the C m (F g À1 ) was calculated according to the eqn (2).

Results and discussion
3.1 Morphology and structure Fig. 2(a) shows typical XRD patterns of TB0-TB40. The diffraction peak at 8.8 corresponds to the (002) plane of Ti 3 C 2 T x . 27 Notably, the Ti 3 C 2 T x (002) peaks of the TB10, TB20, TB30 and TB40 were found to gradually shi signicantly to the le with the increase in Bi 2 O 3 . This result indicates that the interlayer spacing of Ti 3 C 2 T x tends to increase due to the successful intercalation of Bi 2 O 3 among the layers of Ti 3 C 2 T x . Diffraction peaks of Bi 2 O 3 (ICDD#: 71-2274) were clearly visible in the spectra of TB10-TB40. 29,30 As the Bi 2 O 3 content increases, the diffraction peak intensity of Bi 2 O 3 was seen to gradually increase. In addition, TB10 can be indexed to the diffraction peaks of metallic Bi (ICDD#: 05-0519), 31 which is attributed to the carbothermal reduction of a small amount of free C atoms in Ti 3 C 2 T x and Bi 2 O 3 in N 2 atmosphere during the heat treatment. 32 Therefore, it can be inferred that the following reactions occur: To further explore the elemental composition of all the samples, XPS analyses were then carried out for TB0-TB40. The XPS survey spectra in Fig. 2(b) show the presence of Ti, C, Bi, and O in the TB10-TB40. The Bi 4f spectra of TB0-TB40 are shown in Fig. 2(c), which exhibit binding energies at 159 eV and 164.3 eV corresponding to the characteristic peaks of Bi 4f 7/2 and Bi 4f 5/2 , suggesting the presence of Bi 2 O 3 . 33 The bare Bi 2 O 3 responds to characteristic Bi 4f 7/2 and 4f 5/2 XPS peaks at 158.7 and 164.0 eV, respectively, acquired by the National Institute of Standards and Technology (NIST) XPS database. The negatively charged functional groups, such as O-, OH-, tend to attract electrons from bridged Bi cations that change the chemical environment and relative electronic distribution of Bi element, resulting in the peak shi of Bi 4f 7/2 and 4f 5/2 XPS peaks to the higher binding energy in Bi 2 O 3 -Ti 3 C 2 T x nanocomposite. 41 Such a phenomenon demonstrates the chemical bonding between Bi 2 O 3 nanoparticles and Ti 3 C 2 T x sheets in Bi 2 O 3 -Ti 3 C 2 T x composite material. The peak intensities increase with the increasing Bi 2 O 3 -Ti 3 C 2 T x mass ratio, from 10% to 40%, consistent with the XRD results in Fig. 2(a). The appearance of the characteristic peaks of F and O can be attributed to the corrosion of Ti 3 C 2 T x by HF to produce a small amount of functional groups such as -F, -OH and -O. 34,35 The C 1s and O 1s high-resolution spectra of TB0ÀTB40 are provided in Fig. S1 in the ESI † for comparision. Fig. S1(a) † shows the high-resolution C 1s XPS spectra of the TB0-TB40. C 1s spectrum of pristine Ti 3 C 2 T x can be tted into four peaks, corresponding to Ti-C-O at 282.2 eV, C-C/C-H at 284.6 eV, C-O at 286.4 eV and C]O at 288.1 eV, respectively. 19 Aer the solvothermal reaction, In the spectra of the composite samples, the Ti-C-O bonds disappear and new Ti-C peaks appear at 281.2 eV. As for the O 1s XPS spectrum of pristine Ti 3 C 2 T x in Fig. S1(b), † the peaks located at 529.8 eV, 530.4 eV, 531.2 eV, 532 eV and 533.6 eV are attributed to Ti-O, TiO 2 , C-Ti-O, C-Ti-OH and adsorbed H 2 O, respectively. 23 The new Bi-O peaks appear at 530.1 eV and the concentration of C-Ti-OH and C-Ti-O in TB10-TB40 decreased aer the solvothermal, indicating that more O combined to form Bi-O bonds. The atomic ratios of Bi, Ti and C in TB0-TB40 are shown in Fig. 2(d). The Bi/Ti and Bi/C ratios tend to increase with the increasing mass of Bi 2 O 3 , consistent with the XRD and XPS results in Fig. 2(a and b). Fig. 3 shows the morphologies of the as-prepared Ti 3 AlC 2 and TB0-TB40. Ti 3 AlC 2 has a ternary layered structure with a particle size of about 8 mm, as shown in Fig. 3(a). Aer the etching treatment to remove Al from Ti 3 AlC 2 by HF, 36 Ti 3 C 2 T x , with a unique accordion structure and a clean surface without impurities, was obtained, as shown in Fig. 3(b). Fig. 3(c-f) displays the structure and morphology of TB10-TB40, in which a large number of spherical Bi 2 O 3 nanoparticles were found uniformly dispersed in the interlayer and on the surface of Ti 3 C 2 T x . A small amount of spherical Bi 2 O 3 nanoparticles were found to have adhered on the surface of the Ti 3 C 2 T x (TB10) in Fig. 3(c). A large number of tiny spherical Bi 2 O 3 nanoparticles were found to be distributed between the layers of Ti 3 C 2 T x (TB20, TB30), as shown in Fig. 3(d and e); this can effectively prevent layer stacking and collapse, exhibit higher specic surface area and improve the performance of the electric double layer capacitance. 19,37 However, when the loading of Bi 2 O 3 continues to increase, the surface of Ti 3 C 2 T x (TB40) was found to be covered by numerous coarse spherical Bi 2 O 3 nanoparticles and the lamellar structure of Ti 3 C 2 T x was no longer obvious, as shown in Fig. 3(f).
To further investigate the composition and microstructure of the Bi 2 O 3 -Ti 3 C 2 T x , the representative nanocomposite, TB30, was characterized by TEM, HAADF-STEM, elemental mapping for Ti, C, O, Bi and HRTEM, as shown in Fig. 4. Fig. 4(a-c) indicates that a large number of spherical Bi 2 O 3 nanoparticles and a small number of coarse spherical Bi 2 O 3 nanoparticles were distributed on the Ti 3 C 2 T x . Spherical Bi 2 O 3 nanoparticles, with an average diameter of 10-50 nm, were distributed between the layers of Ti 3 C 2 T x and coarse spherical Bi 2 O 3 nanoparticles, with an even particle size of around 80-200 nm, were found on the surface of Ti 3 C 2 T x . The particle-size distribution graph has been shown in Fig. S2. † The spherical Bi 2 O 3 nanoparticles have distinct characteristics of high dispersibility and uniformity, consistent with the SEM results. Fig. 4(d) shows lattice fringe spacings of 0.325 nm and 0.938 nm, which correspond to the (À121) plane of Bi 2 O 3 and (002) plane of Ti 3 C 2 T x , 38,39 respectively. Signicant contact was achieved between the Bi 2 O 3 and Ti 3 C 2 T x for more efficient electron transfer, improving the performance of electrochemistry. The spherical Bi 2 O 3 nanoparticles were found to be covered by an amorphous Bi 2 O 3 lm with a thickness of about 2 nm, which is consistent with the ndings by Wu et al. 24 In addition, Fig. S3 † shows a lattice fringe spacing of 0.328 nm, which corresponds to the (012) plane of metallic Bi. 40 This proves that TB30 contains a small amount of Bi metal, which is attributed to the Bi 2 O 3 reduced to metallic Bi by free C in Ti 3 C 2 T x , consistent with the XRD results in Fig. 1(a). Fig. 5(a and b) show the CV curves of TB0 and TB30, respectively, at different scan rates. As shown in Fig. 5(a), the curves of TB0 look approximately like a symmetrical rectangle, which can be attributed to the double electrode layer capacitance of Ti 3 C 2 T x . All the CV curves of TB0 show a similar symmetrical rectangle with the increase in scan rate, indicating superior rate performance of TB0. 42 The CV curves of TB30 show a prominent redox peak, 43 which can be attributed to the introduction of Bi 2 O 3 , according to the following reactions:

Electrochemical performance
The current at the redox peak tends to slightly shi with the increase of the scan rate due to the slightly reduced conductivity resulting from the interfacial resistance between the electrode surface and the electrolyte solution, suggesting a better rate performance of TB30. 44 The CV curves of TB0ÀTB40 obtained at the scan rate of 5 mV s À1 are shown in Fig. 5(c). It can be clearly seen that the CV curves of TB10, TB20, TB30 and TB40 show stronger redox peak currents and a larger integral than TB0, indicating the superior capacitor properties of the Bi 2 O 3 -Ti 3 C 2 T x hybrid electrode. The best capacitance performance is obtained with TB30, i.e., when the mass percentage of Bi 2 O 3 and Ti 3 C 2 T x is 30%. Fig. 6(a and b) show the GCD curves of TB0 and TB30, respectively, at various current densities. The GCD curves of TB0 present a typical symmetrical triangle, while those of TB30 are asymmetrical with voltage plateaus. The shape of the two curves is signicantly different, which can be attributed to the pseudocapacitive characteristics of Bi 2 O 3 . 43,45 The GCD curves of TB0-TB40 obtained at a current density of 0.2 A g À1 are shown in Fig. 6(c). It can be seen that the discharge time becomes longer with the increase of Bi 2 O 3 loading. The discharge time of TB10, TB20, TB30 and TB40 was found to be longer than that of TB0, which indicates a high specic capacitance due to the presence of Bi 2 O 3 . The specic capacitance was calculated according to eqn (2); the specic capacitance of TB30 was found to be 2.8 times greater than that of TB0. In addition, the lower capacity of TB40 compared to TB30 can be ascribed to the fact that too many coarse spherical Bi 2 O 3 nanoparticles cover the surface of Ti 3 C 2 T x , which impedes the transport of ions in the electrolyte and weakens the conductivity of Ti 3 C 2 T x . Fig. 6(d) shows the variations in specic capacitance of TB0-TB40 with current density, which were calculated from the GCD  Nanoscale Advances curves according to eqn (2). The specic capacitance values of TB0-TB40 at a current of 0.2 A g À1 were found to be 64.8, 91, 136.1, 183, 164.1 F g À1 , respectively. The specic capacitance value of the TB30 is much higher than that of all the other samples at different current densities and is attributed to a large number of tiny spherical Bi 2 O 3 nanoparticles distributed on the surface and layers of Ti 3 C 2 T x . The spherical Bi 2 O 3 nanoparticles tend to enlarge the spacing between the Ti 3 C 2 T x layers, promote electron transfer, and shorten the diffusion path of ions in the electrolyte. In addition, the TB30 still exhibits a capacity of 129.7 F g À1 (about 70.9% retention) even at a current density of 1 A g À1 , indicating an excellent rate capability for TB30. The specic capacitance calculated at 10 A g À1 is 34.6% of the specic capacitance calculated at 0.2 A g À1 , and can be attributed to the insufficient redox reaction in the active material at high current densities, resulting in a decrease in specic capacitance. 46 The comparison of those Ti 3 C 2 T x -based materials is shown in Table 2. 15,20,22,51 It was clear that the performance of Bi 2 O 3 -Ti 3 C 2 T x (TB30) electrode in this work was higher than those of reported materials. Meanwhile, as shown in Fig. 7(e), the TB30 exhibits acceptable electrochemical stability with the capacitive retention still as high as 79.6% even aer 5000 cycles at 5 A g À1 , and can be attributed to the expansion and contraction of Bi 2 O 3 during the insertion and embedding of electrolyte ions by charging and discharging, resulting in a decrease in the capacity. Nyquist impedance plots of TB0-TB40 are shown in Fig. 6(f). The equivalent series resistance (ESR) of electrodes, which is related to the ionic resistance of the electrolyte, the internal resistance of the active material and the current collector, and the interface contact resistance between the electrode and the electrolyte impedance of the electrolyte, 47 depends on the intercept of the semicircle at the X-axis in the high frequency range. It can be seen that the ESR values of TB0-TB40 are 0.87, 0.79, 0.82, 0.73 and 0.80 U, respectively. Among them, TB30 has the smallest ESR. The charge transfer resistance (R ct ) depends on the arc diameter of the semicircle. 48 The R ct values of TB10, TB20, TB30 and TB40 are much larger than that of TB0, which can be attributed to the poor conductivity of Bi 2 O 3 . Simultaneously, the increase of resistance reveals the successful incorporation of Bi 2 O 3 . The linear region in the low frequency range is related to the diffusion resistance of the ions in the electrolyte. 49 The linear part of TB30 is closest to the vertical, indicating that the electrolyte ion diffusion has the lowest resistance. The above results prove that TB30 has good electrochemical capacitance behavior, consistent with the results shown in Fig. 6(d).
In order to further study the Bi 2 O 3 -Ti 3 C 2 T x nanocomposite for practical applications, an asymmetric supercapacitor (ASC) was constructed, 50 with TB0 and TB30 as the positive and negative electrodes, respectively. Fig. 7(a) shows the CV curves  of the TB0//TB30 ASC at different scan rates. It can be seen that the shape of the CV curves of the TB0//TB30 ASC remained the same at different scan rates, implying excellent rate capacity and good reversibility, indicating the good synergistic effect of the electrochemical behavior of both TB0 and TB30 electrodes. The GCD curves of TB0//TB30 ASC at various current densities are shown in Fig. 7(b). The non-linearity of the curve is due to the redox reaction that occurred during the charging and discharging process. The specic capacitance of the TB0//TB30 ASC at different current densities in Fig. 7(c), indicates that the capacitive retention is still as high as 79.1% even aer the current density is increased from 0.2 A g À1 to 1 A g À1 , and the specic capacitance is reduced from 28.2 F g À1 to 22.3 F g À1 . In addition, the specic capacitance calculated at 10 A g À1 is 11 F g À1 with a capacitive retention of 39%, which is attributed to the insufficient redox reaction in the active material at high current density, resulting in a decrease in specic capacitance. This is consistent with the trend of the capacitive retention of TB30. Meanwhile, as shown in Fig. 7(d), the TB0//TB30 ASC exhibits acceptable electrochemical stability with the capacitive retention still as high as 77.4% even aer 5000 cycles at 2 A g À1 and higher than those of reported devices such as Ni(OH) 2 -CNT//Bi-Bi 2 O 3 -CNT based ASC (72.9%/1000 cycles at 1 A g À1 ), 24 PPy-Ti 3 C 2 T x //PPy-Ti 3 C 2 T x based SC (73.68%/4000 cycles at 1 A g À1 ). 52 To further illustrate the overall electrochemical characteristics of the TB0//TB30 ASC, a Ragone plot of the TB0//TB30 ASC was carried out and compared with that of other reported devices based on the a two-electrode conguration in Fig. 7(d) and Table 3. [53][54][55][56][57][58] The highest energy density of the TB0//TB30 ASC is 3.92 W h kg À1 at a power density of 720 W kg À1 , and the highest power density of the TB0//TB30 ASC is 36 000 W kg À1 at an energy density of 1.53 W h kg À1 . The energy density and power density of our device is higher than that of many reported Ti 3 C 2 T x -based and carbon-based SC and ASC devices. The Fig. 7(f) shows that three TB0//TB30 ASC coin cells in series could power a green light-emitting diode (LED, 3 V, 20 mA). Based on above mentioned results, it can be conclued that Bi 2 O 3 -Ti 3 C 2 T x is a promising electrode material for supercapacitors in the future.

Conclusions
In this study, we prepared Bi 2 O 3 -Ti 3 C 2 T x nanocomposites by a solvothermal method. The spherical Bi 2 O 3 nanoparticles were uniformly distributed on the surface and layers of Ti 3 C 2 T x , which effectively prevented layer stacking and increased the inter-layer spacing. When the mass percentage of Bi 2 O 3 and Ti 3 C 2 T x was 30% (TB30), the best capacitance performance was obtained. The specic capacitance of TB30 was 2.8 times that of TB0 at 0.2 A g À1 , which was attributed to the outstanding