During the last few decades, lithium-ion batteries (LIBs) have been used in almost every facets of people’s daily life, such as portable electronic products, electric vehicles and medical electronics (Tarascon and Armand, 2001; Li et al., 2019a; Ni et al., 2019a; Pu et al., 2021). However, the current graphite anode couldn’t meet the increasing energy demand of advanced equipments due to its low theoretical capacity and poor rate ability (Ni et al., 2019b; Li et al., 2020; Yan et al., 2020). On the other hand, sodium ion batteries (SIBs) are considered as a potential candidate of LIBs in large-scale energy storage systems due to the abundant natural reserves of sodium compared with lithium (Yabuuchi et al., 2014; Nayak et al., 2018). However, due to the mismatch between ionic radius of sodium ion and graphite interlayer (d₍₀₀₂₎ = 0.335 nm), the commerical graphite-type anode of LIBs show very limited capacity for SIBs (Liu and Mustarelli, 2020). Hence, it is very exigent to explore high performance anode materials of LIBs and SIBs (Palacin, 2009). In recent years, transitional metal dichalcogenides (TMDs) with the advantages of low cost and environmental begnity have been regarded as promising candidate anodes for secondary LIBs and SIBs (Peng et al., 2016; Li et al., 2021). In addition, TMDs not only possesses lower activation energy between metal and sulfur than metallic oxides, but also demonstrates much higher theoretical capacity than carbon materials. The low activation energy is beneficial to the conversion reaction during charge/discharge process, while the high theoretical capacity of active material is vital to the energy density of both LIBs and SIBs (Yan et al., 2005; Yuan et al., 2011). Espically, molybdenum sulfide (MoS₂) with a represenative two-dimensional structure demonstrates a superior design flexibility and high theoretical capacity when applied as anode of LIBs and SIBs (Liu et al., 2018; Li et al., 2019b). However, during the cycle process, due to the volume change, dissolution of polysulfides and poor electronic conductivity, the electrode will eventually be powdered, electric contact loss, poor rate capacity and rapid capacity attenuation.

Up to now, various strategies have been developed to improve the electrochemical performance of MoS₂ anode. An effective method is to fabricate nanometer materials, which are easy to release stress. In addition, the nano-scale particle size can effectively shorten the ion diffusion distance and promote the migration of alkali metal ions during the charge and discharge process (Hu et al., 2014; Kang et al., 2017). Another widely used method is to combine with conductive matrix such as amorphous carbon (Balogun et al., 2016). The conductive matrix not only improves the electron transport capacity, but also adapts to the changing volume during the cycle. In addition, heteroatom doping can improve the properties of carbon matrix (Balogun et al., 2016). Heteroatom doping, especially N doping in carbon, can produce extrinsic conductivity, which is beneficial to the contact between carbon and MoS₂. More recently, the synthesis of MoS₂ with few-layered structure has also been drawn extensive attention due to its shorter ion pathway and higher ion diffusion mobility compared with multi-layered structure (Lv et al., 2015). Although much progress has been made so far, the rational utilization of those strategies for both lithium and sodium storage is still highly desirable.

Herein, we reported the fabrication of few-layered MoS₂@N-doped carbon (F-MoS₂@NC) nanohybrids and evaluated its application as anode of LIBs and SIBs. In this unique nanohybrid structure, the MoS₂ nanocrystals effectively promote the transfer of alkali metal ions and also shorten the alkali metal ions diffusion distance, while the N-doped carbon matrix improves the electron transport capacity, inhibits the agglomeration of nanocrystals and reduces the stress when the volume changes greatly. Furthermore, the few-layered MoS₂ structure shortens the ion channel and improves the diffusion mobility of lithium and sodium ion. In consequence, F-MoS₂@NC demonstrates a reversible capacity of 482.6 mA h g⁻¹ at 2000 mA g⁻¹ for LIBs and maintains a reversible capacity of 171 mA h g⁻¹ at of 1,000 mA g⁻¹ after 600 cycles for SIBs. The excellent lithium and sodium storage properties of F-MoS₂@NC should be derived from the synergy between N-doped carbon and few-layered MoS₂ structure.

The typical synthesis process of F-MoS₂@NC is demonstrated in Figure 1. As shown, NMD/DAH complex is first simply mixed with DAH in deionized water. Due to the chelating reaction between molybdate anion and dopamine, a uniform orange red solution is obtained. And the weak acidic environment provided by NMD inhibits the self polymerization of DAH. In the subsequent solvothermal process, DAH was partially carbonized, and L-cysteine was used as reducing agent and sulfurizing agent to promote the conversion of NMD to MoS₂. The resulting product was further calcinated at high temperature to improve the crystallinity of MoS₂ and the degree of carbonization to yield F-MoS₂@NC.

The crystalline structure of the synthesized samples was investigated by XRD, as shown in Figure 2A. For bare MoS₂, the diffraction peaks at 13.7°, 33.0°, 39.3°, 58.6° and 69.0° represent the (002), (100), (103), (110) and (201) of 2H MoS₂. While for F-MoS₂@NC, the diffraction peaks at 33.0°, 58.6° and 69.0° represent the (100), (110) and (201) planes of MoS₂. However, the (002) and (103) diffraction peaks of MoS₂ in the sample disappear, which should be due to the inhibition of crystal growth by the presence of carbon. Noting that the absence of (002) diffraction peak indicates the formation of few-layered MoS₂ sheets (Zhou et al., 2015; Hu et al., 2018; Li et al., 2021). Therefore, the addition of N-doped carbon precursor could significantly promote the formation of few-layered MoS₂ in F-MoS₂@NC. It should be noted that the diffraction peak at around 26.5° represented the (002) plane of carbon could not be observed in F-MoS₂@NC, which should be due to the low content and amorphous form of carbon. The XRD results also confirm the successful synthesis of few-layered MoS₂ structure via a facile solvothermal and annealing process. The nitrogen adsorption-desorption and porous characteristic of F-MoS₂@NC were conducted by Brunauer-Emmett-Teller method. The nitrogen adsorption-desorption curves of F-MoS₂@NC-0.4, F-MoS₂@NC-0.8 and F-MoS₂@NC-1.2 (Figure 2B) show a typical hysteresis loop within the P/P₀ range of about 0.3–0.9, indicating they has rich mesoporous structure (Song et al., 2019). Supplementary Table S1 shows the pore volumes and specific surface areas of F-MoS₂@NC. It can be observed that the specific surface area of F-MoS₂@NC increased with pore volume in F-MoS₂@NC and F-MoS₂@NC-0.8 showed largest pore volume and specific surface area. For F-MoS₂@NC electrode, the large specific surface area could effectively enhance the contact between electrode/electrolyte, while the abunant pore volume will provide more ion transport pathways, which are beneficial for lithium and sodium storage (Li et al., 2013; Hou et al., 2017; Zhang et al., 2018).

XPS was used to analyze the chemical bonds on the surface of those samples, as shown in Supplementary Figure S1 and Figure 3. The survey spectra of F-MoS₂@NC (Supplementary Figure S1) confirmed the existence of C, N, Mo, S, and O. The slight oxidation of MoS₂ in ambient environment and the existence of oxygen-containing groups resulted in the distinct oxygen signal which observed in these samples. The C1s highly deconvolution spectra of F-MoS₂@NC-0.8 (Figure 3A) demonstrated two fitting peaks at 284.8 and 284.3 eV, which are attributed to C-N and C-C (Li et al., 2018a; Han et al., 2019; Song et al., 2020a). Besides, the other three fitting peaks at 285.6, 286.8 and 289.0 eV can also be observed, which should be due to the existence of C−O, C=O and O−C=O in the surface of F-MoS₂@NC-0.8 (Quinlan et al., 2016; Li et al., 2018b; Ni et al., 2018; Song et al., 2019; Yue et al., 2019; Han et al., 2020), respectively. The Mo 3 d and S 2s highly deconvoluted spectra of F-MoS₂@NC-0.8 (Figure 3B) showed the three fitted peaks at 235.7, 232.5 and 229.4 eV are related to Mo⁶⁺−O, Mo 3d_3/2 and Mo 3d_5/2 (Feng et al., 2015; Ahn et al., 2018; Lei et al., 2018). It should be noted that the slight surface oxidation of MoS₂ could cause the existence of Mo⁶⁺−O. Besides, the S 2s peak in 226.6 eV could also clearly observed. The two fitting peaks of S 2p_3/2 and S 2p_1/2 could also be clearly observed at 162.2 and 163.4 eV in the highly deconvoluted S 2p spectra of F-MoS₂@NC-0.8 (Figure 3C). In addition, the other fitted peaks at 165.8 eV in the highly deconvoluted are ascribed to SO_x (x = 2–4) (Zhao et al., 2019; Song et al., 2020b). The fitted peaks of pyridinic-N and pyrrolic-N in the highly deconvoluted N 1S and Mo 3p spectrum of F-MoS₂@NC-0.8 (Figure 3D) at 398.1 and 400.8 eV could be observed, as well as the other fitted peak of Mo 3p_2/3 at 395.3 eV, respectively (Ye et al., 2016; Ma et al., 2019). The high deconvolutions of C 1s, Mo 3 d and S 2s, S 2p and N 1S and Mo 3p of F-MoS₂@NC-0.4 and F-MoS₂@NC-1.2 are similar to that of F-MoS₂@NC-0.8, which are shown in Supplementary Figure S2. The TGA at a heating rate of 10°C min⁻¹ in air was employed to characterize the weight contents of MoS₂ and carbon in F-MoS₂@NC. The TGA curves of those samples were shown in Supplementary Figure S3. As shown, the TGA curves demonstrated two weight loss steps that the first step below 200°C and the second step between 300 and 500°C. It should be noted that the evaporation of loss physically adsorbed water result in the first weight loss step, while the continuous combustichon of carbon and the oxidation of MoS₂ between 300 and 500°C should be contributed to the second weight loss step (Wu et al., 2018). Because carbon can burn completely in air, only MoO₃ is produced. The following equation could be used to obtain the exact content of carbon and MoS₂ can be calculated by in F-MoS₂@NC: wt% ( carbon ) = 1 − wt% ( water ) − wt%R × M ( MoS 2 ) / M ( MoO 3 ) (1) wt% ( MoS 2 ) = wt%R × M ( MoS 2 ) / M ( MoO 3 ) (2) where wt% (carbon), wt% (water) and wt% (MoS₂) represent the weight contents of carbon, water and MoS₂, M(MoS₂) and M(MoO₃) are the molecular weight of MoS₂ and MoO₃, wt%R are the residue percentages of F-MoS₂@NC after 650°C. The weight contents of MoS₂ are calculated to be 75.19, 70.09 and 64.67% in F-MoS₂@NC-0.4, F-MoS₂@NC-0.8 and F-MoS₂@NC-1.2 (See details in Supplementary Table S1), respectively.

Morphological and structural characteristics of F-MoS₂@NC-0.8 were studied by SEM and TEM. As exhibited in Figures 4A,B, the spherical product is named F-MoS₂@NC-0.8. After solvothermal treatment and annealing treatment, ∼300 nm spheres with rough surface can be obtained. The surface morphologies of F-MoS₂@NC-0.4 and F-MoS₂@NC-1.2 are similar to that of F-MoS₂@NC-0.8, as shown in Supplementary Figure S4. Besides, the uniformly distributed elements of Mo, S and C in F-MoS₂@NC-0.8 were confirmed by the EDS mapping measurement (Supplementary Figure S5). The element of N could not be detected due to its low weight percentage. The SEM and TEM images of F-MoS₂@NC-0.8 (Figures 4B,C) indicate the microspheres consisting of ultrathin crumpled nanosheets. High resolution TEM image displays F-MoS₂@NC-0.8 (Figure 4D), in which several layers of MoS₂ nanosheets with an enlarged interlayer distance of 1.0 ∼ 1.1 nm (vs. 0.62 nm for pristine MoS₂) can be observed. The expanded few-layered MoS₂ nanosheets effectively promote the transport of electrolyte and ions during charge/discharge process, thus improving the rate performance (Hu et al., 2018). It should be noted that the quantitative data of ion diffusion mobility caused by the few-layered structure was hardly obtained due to the influence of other factors, such as specific surface area and pore structure.

CR 2032 half cells were assembled using F-MoS₂@NC as the counter electrode and characterized to investigate its lithium storage performances. The initial three CV curves of F-MoS₂@NC at a sweep rate of 0.2 mV s⁻¹ in the potential window of 0.005–3 V versus Li/Li⁺ were displayed in Figure 5A. The two peaks of CV curves at 1.38 and 0.76 V in the first scan were related to the decomposition of MoS₂ into Mo and Li₂S and the intercalation of Li⁺ in MoS₂, which indicates the transformation of matter from 2H MoS₂ to 1 T Li_xMoS₂, respectively (Wan et al., 2014). However, these cathodic peaks disappear after the first cycle, which indicates the nonreversible conversion reaction. The peak value located at 0.53 V in the first cathode scan should result from the formation of solid electrolyte interface (SEI) film (Chen et al., 2016). The broad peak located at 1.65 V in the first anodic scan is related to the removal of lithium from the residual lithium intercalation layer (Li_xMoS₂). Besides, the oxidation of Li₂S to S result in another obvious peak at 2.26 V (Zhuang et al., 2015). In the subsequent scanning process, a pair of redox peaks of about 1.76/2.34 V were related to the conversion reaction between Li₂S and S, respectively (Sen et al., 2014). After the second cycle, the cathode/anode peaks are almost kept at the same position, which indicates that it has good electrochemical reversibility. The dicharge/charge profiles of F-MoS₂@NC-0.8 electrode at different cycles were demonstrated in Figure 5B. As shown, the initial discharge/charge specific capacities are 1,160 and 855.1 mA h g⁻¹, respectively. And the coulombic efficiency is about 73.71%. The initial large capacity loss should be attributed to the formation of SEI film in the first cycle (Cao et al., 2013). In the second cycle, the coulombic efficiency is over 95%, which indicates that the SEI film is stable. In addition, the dicharge/charge profiles of F-MoS₂@NC-0.4 and F-MoS₂@NC-1.2 electrode at different cycles are also shown in Figures 8C,D. It can be observed that the F-MoS₂@NC-0.4 and F-MoS₂@NC-1.2 electrode exhibit lower discharge and charge specific capacities than F-MoS₂@NC-0.8 after several cycles. Especially, the F-MoS₂@NC-0.4 electrode dropped rapidly during the cycle process, and indistinct plateau was observed in the 10th cycle, indicating that the F-MoS₂@NC-0.4 electrode had been crushed.

The galvanostatic cycling performances of bare MoS₂, F-MoS₂@NC-0.4, F-MoS₂@NC-0.8 and F-MoS₂@NC-1.2 are shown in Figure 6. The poor cycle performance of bare MoS₂ can be observed in Figure 6 and the reversible capacity decreases rapidly during the cycle process. Even though the bare MoS₂ exhibits inferior cycling stability compared to some porous material, such as metal oxides and amorphous carbon, it possesses lower activation energy and high theoretical capacity and the inferior cycling stability of bare MoS₂ could be improved by the specific strategy employed in this work. When MoS₂ and N-doped carbon are combined together, compared to bare MoS₂, the F-MoS₂@NC hybrid exhibits improved cycle performance. And the cycle performances of F-MoS₂@NC are related to the proportion of N-doped carbon. With the increase of N-doped carbon content, the cycle performance is improved. However, with the further increase of N-doped carbon content, the cycle performance decreases slightly. The optimal value of N-doped carbon is 27.81%. The F-MoS₂@NC-0.8 electrode exhibited a highest reversible capacity of 608.6 mA h g⁻¹ at 100 mA g⁻¹after 100 cycles. The higher capacity of F-MoS₂@NC-0.8 than F-MoS₂@NC-0.4 and F-MoS₂@NC-1.2 should be due to the suitable carbon content, larger specific surface area and more mesoporous, the enhanced contact between electrode/electrolyte, as well as the transport path of lithium ion can be reduced. Figure 6B displays the rate performance of F-MoS₂@NC-0.8. As shown, the F-MoS₂@NC-0.8 electrode was tested at the current densities of 100, 200, 500, 1,000, 2000 and 5,000 mA g⁻¹, which displayed high reversible capacities of 814.5, 738.3, 617.6, 566.0, 482.6 and 287.4 mA h g⁻¹, respectively. It should be noted that a high reversible capacity of 758.3 mA h g⁻¹ can be obtained even when the current density is restored to 100 mA g⁻¹, which indicates its excellent rate performance.

CV measurements at a series of scan rates from 0.2 to 2 mV s⁻¹ were performed to explore the electrochemical kinetics of F-MoS₂@NC-0.8 electrode and the possible reasons for its excellent rate performance, as shown in Figure 7A. It can be observed that the shape of CV curves at different scan rates are similar. In addition, with the increase of the scanning rate, the current intensity in CV curves increases continually. In general, several mechanisms are involed in this electrochemical behavior during cycling process. The following equation can be used to analyzed the total charge stored behavior based on the CV data at different scan rates (Jiang and Liu 2019): i = av b (3) Log ( i ) = blog ( v ) + log ( a ) (4)

In those equation, i and v represents the measured current density and the scan rate, while a and b are constants, respectively. It should be noted that a value of b of 0.5 indicates the charge storage mechanism of complete diffusion control and a value of b of 1 indicates that the charge storage process of capacitance behavior dominates. The curves obtained by plotting log i versus log v are used to calculate the b value (Figure 7B). In fact, the slope of the curves represents the b value. When the potentials are 0.9, 1.2, 1.5, 1.8, 2.1 and 2.4 V, the b values are 0.72, 0.83, 0.8, 0.83, 0.75 and 0.59, respectively. In addition, the ratio of capacitance contribution to diffusion control contribution is calculated based on the equation: i = k 2 v 1 / 2 + k 1 v

In this equation, k₁ and k₂ are constants, which can be obtained by the modified equation i_(v)/v^1/2 = k₁v^1/2 + k₂. While i _(v) and v represents the current density at a fixed potential and the scan rate, respectively. According to the above analysis, the ratio of capacitance contribution and diffusion control at different scan rates were calculated, as shown in Figure 7C. With the increasement of scan rate from 0.2 to 2 mV, the capacitance contribution also increases from 39.1% to 67.0%. It is worth noting that the high ratio of capacitance contribution is beneficial for its superior rate performance due to the improved lithium-ion diffusion and rapid electron transfer in pseudocapacitive process compared with diffusion controlled process.

Since the much larger size of sodium ions than lithium ions, the high-performance anode of LIBs often demonstrate poor sodium-ion storage performance when applied as anode of SIBs. Increasingly, the as-prepared F-MoS₂@NC based on the strong combination of MoS₂ and N-doped carbon shows excellent sodium storage performance. As shown in Figure 8A, the initial three CV curves were employed to analyze the redox behaviors of F-MoS₂@NC-0.8 for SIBs. The CV measurements were performed at a scan rate of 0.2 mV s⁻¹ in the potential range of 0.005–3 V. Similar to that of LIBs, the two peaks of CV curves in the first scan at 0.91 and 0.03 V were related to the decomposition of MoS₂ into Mo and Na₂S and the intercalation of Na⁺ in MoS₂, which indicates the transformation of matter from 2H MoS₂ to 1 T Na_xMoS₂, respectively (Wang et al., 2014; Wang et al., 2015). However, these cathodic peaks disappear after ths first cycle, which indicates the irreversibility of the conversion reaction. In addition, the peak located at 0.42 V in the first cathode scan should be due to the formation of SEI film on the surface of F-MoS₂@NC (Yan et al., 2015). For the first anodic scan, the oxidation of Na₂S and the formation of polysulfides caused the obvious peak of CV curves at 1.75 V (Li et al., 2018c). In the second scan, the new peaks are at 1.6 and 0.65 V, which should be realted with the formation of Na₂S and the sodium storage of Mo atoms, respectively (David et al., 2014). After the second cycle, the cathode/anode peaks are almost kept at the same position, which indicates that it has good electrochemical reversibility. Figure 8B shows the dicharge/charge profiles of F-MoS₂@NC-0.8 electrode at different cycles. It can be observed that the initial discharge/charge specific capacities are 391.0 and 626.2 mA h g⁻¹, and the coulombic efficiency is about 62.44%. The large capacity loss should be attributed to the SEI formation during the first cycle, similar to that of LIBs. In the subsequent cycle, the coulombic quickly reaches over 90%, which indicates the high stability of SEI film. In addition, the dicharge/charge profiles of F-MoS₂@NC-0.4 and F-MoS₂@NC-1.2 electrode at different cycles are also shown in Figures 5C,D. It can be observed that the F-MoS₂@NC-0.4 and F-MoS₂@NC-1.2 electrode exhibit lower discharge and charge specific capacities than F-MoS₂@NC-0.8 after several cycles. Especially, the F-MoS₂@NC-0.4 electrode dropped rapidly during the cycle, indicating that the F-MoS₂@NC-0.4 electrode was crushed. In addition, the specific discharge/charge profiles of F-MoS₂@NC electrode as anode of LIBs at 20th, 30th, 40th, 50th, 60th, 70th, 80th, 90th, and 100th cycle were also shown in Supplementary Figure S6. For F-MoS₂@NC-0.4 electrode, the discharge/charge platform was almost completely disappeared in those cycles, while for F-MoS₂@NC-0.8 and F-MoS₂@NC-1.2 electrodes, the discharge/charge platform could still be observed even at 100th cycle. The more distinct discharge/charge platform of F-MoS₂@NC-0.8 and F-MoS₂@NC-1.2 electrodes than F-MoS₂@NC-0.4 should be due to their higher structural stability during cycling process.

The galvanostatic cycling performances of F-MoS₂@NC-0.4, F-MoS₂@NC-0.8, F-MoS₂@NC-1.2 and bare MoS₂ as anode of SIBs are shown in Figures 9A,B. Similar to the LIBs presented above, the F-MoS₂@NC-0.8 electrode exhibited a highest reversible capacity of 241.7 mA h g⁻¹ after 100 cycles at 50 mA g⁻¹, while the F-MoS₂@NC-0.4, F-MoS₂@NC-1.2 electrode and bare MoS₂ deliver lower reversible capacities of 95.3, 222.0 and 16.2 mA h g⁻¹, respectively. The best sodium storage performance of F-MoS₂@NC-0.8 in these electrodes should be related to its suitable content of carbon, larger specific area and more abundant mesoporous. In addition, the morphologies of F-MoS₂@NC-0.8 electrode after process were also investigated by SEM. As shown in Supplementary Figure S7, the F-MoS₂@NC-0.8 electrode could still maintain spherical structure after cycling process, indicating its structure stability. The rate performance of F-MoS₂@NC-0.8 was also shown in Figure 9C. As shown, the F-MoS₂@NC-0.8 electrode exhibits reversible capacities of 368.4, 333.3, 278.2, 248.2, 206.6 and 131.2 mA h g⁻¹ at 50, 100, 250, 500, 1,000 and 2,500 mA g⁻¹. In addition, when the current density is restored to 50 mA g⁻¹, a high reversible capacity of 333.7 mAh g⁻¹ could be obtained. Those results indicated its excellent rate performance. The long cycle performance of the electrode is of great significance to the practical application of SIBs. As shown in Figure 9D, the F-MoS₂@NC-0.8 electrode under the high current density of 1,000 mA g⁻¹, the electrode can still output 171.0 mA h g⁻¹ after 600 cycles, and the coulomb coefficient is close to 100%, which indicates that the electrode has good structural stability and long-term cycle stability in the process of rapid charge discharge.

The electrochemical reaction kinetics of F-MoS₂@NC-0.8 as anode of SIBs was also studied. CV measurements at a series of scan rates from 0.2 to 2 mV s⁻¹ were performed, which are shown in Figure 10A. With the increase of scanning rate, the cathode peak and anode peak become wider and the current increases. Similar to that of LIBs, the curves obtained by plotting log i versus log v are used to calculate the b value. When the potentials are 0.9, 1.2, 1.5, 1.8, 2.1 and 2.4 V, the b values are 0.74, 0.78, 0.74, 0.64, 0.8 and 1.00 (Figure 10B). According to the Eq. 3, the ratio of capacitance contribution to diffusion control contribution is calculated. As shown in Figure 10C, the ratio of capacitive contributions are 42.0, 50.7, 55.7, 59.2, 62.9, 66.5 and 69.7% at 0.2, 0.4, 0.6, 0.8, 1.0, 1.5 and 2.0 mV s⁻¹. The results show that with the increasement of scan rates, the rate of capacitance contribution increases continually, which will enhance the rate capability and long period stability of the system due to the improved ion diffusion and rapid electron transfer in pseudocapacitive process.

The excellent lithium and sodium storage performances of F-MoS₂@NC should be due to few-layered structure of MoS₂ and its reasonable hybridization with N-doped carbon matrix, which makes the hybrid materials have good performance as anode materials for LIBs and SIBs. Firstly, the strong combination of N-doped carbon and ultra-small MoS₂ nanocrystals could improve the conductivity of hybrid materials, enhance the electrochemical reaction kinetics during cycling and reduce the stress caused by volume change. Secondly, the few-layered MoS₂ structure also shortens the ion channel and improves the ion diffusion mobility. Finally, because of the large specific surface area, abundant mesoporous structure and capacitance controlled electrochemical behavior, the hybrid F-MoS₂@NC materials demonstrates excellent electrochemical behavior for both lithium and sodium storage properties.

In summary, F-MoS₂@NC hybrids were synthesized through a facile solvothermal and annealing process. The XRD, SEM and TEM results confirm its few-layered MoS₂ structure, while the XPS measurement shows the existence of N-doped carbon. In fact, the existence of N-doped carbon could not only boost the formation of few-layered MoS₂ structure, but also effectively its lithium and sodium storage performance. Firstly, the few-layered MoS₂ structure could shorten the ion pathway and improve the ion diffusion mobility compared with multi-layered structure. Secondly, the N-doped carbon emhances the electron transport capacity, inhibits the agglomeration of nanocrystals and reduces the stress of MoS₂ during charge/discharge process. In addition, the relative large specific surface area and abundant also enhance the contact between electrode/electrolyte, while the abunant pore volume will provide more ion transport pathways. In consequence, a high reversible capacity of 482.6 mA h g⁻¹ at a 2000 mA g⁻¹ could be obtained for LIBs. As for SIBs, F-MoS₂@NC hybrids could also maintain a reversible capacity of 171 mA h g⁻¹ after 600 cycles at 1,000 mA g⁻¹. The F-MoS₂@NC hybrids should be full of potential anode for both LIBs and SIBs.