Organic Crosslinked Polymer-Derived N/O-Doped Porous Carbons for High-Performance Supercapacitor

Supercapacitors, as a new type of green electrical energy storage device, are a potential solution to environmental problems created by economic development and the excessive use of fossil energy resources. In this work, nitrogen/oxygen (N/O)-doped porous carbon materials for high-performance supercapacitors are fabricated by calcining and activating an organic crosslinked polymer prepared using polyethylene glycol, hydroxypropyl methylcellulose, and 4,4-diphenylmethane diisocyanate. The porous carbon exhibits a large specific surface area (1589 m2·g−1) and high electrochemical performance, thanks to the network structure and rich N/O content in the organic crosslinked polymer. The optimized porous carbon material (COCLP-4.5), obtained by adjusting the raw material ratio of the organic crosslinked polymer, exhibits a high specific capacitance (522 F·g−1 at 0.5 A·g−1), good rate capability (319 F·g−1 at 20 A·g−1), and outstanding stability (83% retention after 5000 cycles) in a three-electrode system. Furthermore, an energy density of 18.04 Wh·kg−1 is obtained at a power density of 200.0 W·kg−1 in a two-electrode system. This study demonstrates that organic crosslinked polymer-derived porous carbon electrode materials have good energy storage potential.


Introduction
Solutions to environmental problems, owing to economic development and the excessive use of fossil energy resources, are urgently being sought [1]. Supercapacitors, as a new type of green electrical energy storage device, have drawn increasing attention, owing to their high power density, fast charging/discharging, excellent reversibility, long life cycle, and environmental friendliness [2][3][4].
Theoretical research on and practical applications of supercapacitors have significantly progressed; however, insufficient energy density and high cost are still challenges requiring resolution [5][6][7]. Electrode materials, which can be divided into carbon materials [8,9], metal oxides [10,11], and conductive polymers [12,13], play an important role as core components in supercapacitors and are a key step in solving the existing problems. Among them, carbon materials are the most widely used electrode materials because of their high specific surface

Synthesis of Organic Crosslinked Polymers
The organic crosslinked polymers were prepared by a one-pot method, which is a minor modification based on our previous report [27]. Briefly, PEG 6000 (12.0 g), MDI (1.0 g), and a certain amount of HPMC were stirred in a three-neck flask containing DMF (80 mL) under argon gas and an oil bath with a constant temperature of 75 • C. The organic crosslinked polymer obtained after 30 h of condensation reflux is referred to as OCLP. The mass of HPMC was 3.5, 4.5, and 5.0 g; therefore, the corresponding organic crosslinked polymers were named as OCLP 3.5 , OCLP 4.5 and OCLP 5.0 , respectively. Figure 1 presents a flowchart of the one-pot method for the preparation of organic crosslinked polymers. ethylene (PTFE), and N, N-dimethylformamide (DMF) were purchased from Aladdin. Analytical-grade potassium hydroxide (KOH) and acetylene black were obtained from Xilong Science Co., Ltd. (Shantou, China). None of the purchased reagents were purified before use. All aqueous solutions were prepared using ultrapure water (deionized water, resistance 18 MΩ cm −1 ).

Synthesis of Organic Crosslinked Polymers
The organic crosslinked polymers were prepared by a one-pot method, which is a minor modification based on our previous report [27]. Briefly, PEG 6000 (12.0 g), MDI (1.0 g), and a certain amount of HPMC were stirred in a three-neck flask containing DMF (80 mL) under argon gas and an oil bath with a constant temperature of 75 °C. The organic crosslinked polymer obtained after 30 h of condensation reflux is referred to as OCLP. The mass of HPMC was 3.5, 4.5, and 5.0 g; therefore, the corresponding organic crosslinked polymers were named as OCLP3.5, OCLP4.5 and OCLP5.0, respectively. Figure 1 presents a flowchart of the one-pot method for the preparation of organic crosslinked polymers.

Preparation of Porous Carbon Materials
The prepared OCLPs were directly carbonized by heating them in a tube furnace at 500 °C for 2 h under a N2 atmosphere at a heating rate of 5 °C /min. The resulting carbon precursors were homogeneously ground with KOH in a mass ratio of 1.0:3.0, then calcined in a tube furnace at 600 °C under a N2 atmosphere for 2 h. The calcined products were stirred with a 1 M hydrochloric acid solution for 2 h, followed by washing with distilled water and anhydrous ethanol sequentially until the filtrate was neutral. The obtained residues were dried in a blast oven at 80 °C for 24 h to obtain porous carbon materials, which were named as COCLP-3.5, COCLP-4.5, and COCLP-5.0, respectively.

Characterization
Fourier transform infrared (FTIR) spectroscopy was performed on the samples using a Thermo Fisher (Waltham, MA, USA) Nicolet 6700 spectrometer with KBr pellets. A powder X-ray diffractometer (XRD; D8 Advance Bruker, Billerica, MA, USA) operating at 40 kV and 40 mA with Cu Kα radiation (λ = 0.15406 nm) in the 2θ range of 5-90° with 0.01° step increments was used to analyze the microstructure of the materials. The chemical structure and graphitization of the samples were further characterized using Raman spectroscopy (Horiba JY, Palaiseau, France) at an excitation wavelength of 532 nm. The surface micromorphology of the samples was characterized using scanning electron microscopy

Preparation of Porous Carbon Materials
The prepared OCLPs were directly carbonized by heating them in a tube furnace at 500 • C for 2 h under a N 2 atmosphere at a heating rate of 5 • C/min. The resulting carbon precursors were homogeneously ground with KOH in a mass ratio of 1.0:3.0, then calcined in a tube furnace at 600 • C under a N 2 atmosphere for 2 h. The calcined products were stirred with a 1 M hydrochloric acid solution for 2 h, followed by washing with distilled water and anhydrous ethanol sequentially until the filtrate was neutral. The obtained residues were dried in a blast oven at 80 • C for 24 h to obtain porous carbon materials, which were named as C OCLP-3.5 , C OCLP-4.5 , and C OCLP-5.0 , respectively.

Characterization
Fourier transform infrared (FTIR) spectroscopy was performed on the samples using a Thermo Fisher (Waltham, MA, USA) Nicolet 6700 spectrometer with KBr pellets. A powder X-ray diffractometer (XRD; D8 Advance Bruker, Billerica, MA, USA) operating at 40 kV and 40 mA with Cu Kα radiation (λ = 0.15406 nm) in the 2θ range of 5-90 • with 0.01 • step increments was used to analyze the microstructure of the materials. The chemical structure and graphitization of the samples were further characterized using Raman spectroscopy (Horiba JY, Palaiseau, France) at an excitation wavelength of 532 nm. The surface micromorphology of the samples was characterized using scanning electron microscopy (SEM; SU8010, HITACHI, Tokyo, Japan) and transmission electron microscopy (TEM; Tecnai G2 F20, FEI Company, Hillsboro, OR, USA), and elemental analysis was performed using energy-dispersive X-ray spectroscopy (EDS). The specific surface area and pore structure characteristics of the samples were characterized using a nitrogen adsorption-desorption analyzer (ASIQM0002-4, Quantachrome, Boynton Beach, Florida, Nanomaterials 2022, 12, 2186 4 of 14 USA) at −196 • C. Surface element analysis was performed using X-ray photoelectron spectroscopy (XPS; Thermo Scientific Escalab 250Xi, Waltham, MA, USA).

Electrochemical Measurements
The electrochemical performance of the samples, including galvanostatic chargedischarge (GCD), cyclic voltammetry (CV), and electrochemical impedance (EIS), was measured using a CHI 660E instrument in a three-electrode system. A slurry mixture of carbon material (C OCLP ), acetylene black, and PTFE in a weight ratio of 8:1:1 was applied to nickel foam (2 cm × 2 cm) as the working electrode; platinum and Hg/HgO electrodes were used as the counter and reference electrodes, respectively, in the three-electrode system. The voltage was set to −1-0 V and the electrolyte was 6 M KOH. A symmetric supercapacitor was built for a two-electrode system using the C OCLP , a 1 M Na 2 SO 4 electrolyte, and a voltage range of 0-1.6 V.
For the three-electrode and two-electrode systems, the weight-specific capacitances (F·g −1 ) of the electrode material were calculated based on the GCD curves using Equations (1) and (2), respectively.
where I (A), ∆t (s), ∆V (mV), and m (g) represent the discharge current, discharge time, discharge voltage range, and mass of the active material of a single electrode, respectively. The energy density (E cell ) and power density (P cell ) of the symmetrical supercapacitor were calculated using Equations (3) and (4), respectively.
where C g is obtained from Equation (2), ∆V is the working voltage of the discharge, and ∆t is the discharge time. Figure 2 shows the FTIR spectra of the samples, which indicates that the characteristic absorption peaks for the OCLPs (OCLP 3.5 , OCLP 4.5 , and OCLP 5.0 ) are similar. The peaks around 3438, 1639, 1526, and 1106 cm −1 correspond to the stretching vibration absorption peaks of the -OH, C=O, C-N, and C-O groups, respectively, which is consistent with the organic crosslinked polymer [27]. The above results illustrate that the OCLPs are a type of organic crosslinked polymer.

Structural and Morphological Characterization
The C OCLPs obtained from the OCLPs were characterized using XRD and Raman spectroscopy. Figure 3a summarizes the XRD spectra of the C OCLP-3.5 , C OCLP-4.5 , and C OCLP-5.0 , showing that all the C OCLPs exhibit obvious diffraction peaks at 43 • , corresponding to the (100) crystal planes of the graphite structure. The results indicate that C OCLP-3.5 , C OCLP-4.5, and C OCLP-5.0 have amorphous graphite structures [28,29]. The diffraction peak intensity of the (100) lattice plane for C OCLP-4.5 is the weakest, demonstrating that C OCLP-4.5 has the highest structural disorder [30]. Figure 3b shows that there are two characteristic peaks at 1343 and 1594 cm −1 , corresponding to the D and G peaks of graphite, respectively. The ratio of the areas of the D peak to the G peak (A D /A G ) reflects the order degree of the C OCLP structure [31]. The calculated ratios for C OCLP-3.5 , C OCLP-4.5 , and C OCLP-5.0 are 1.15: 1, 1.18: 1, and 1.13: 1, respectively. This result also illustrates that C OCLP-4.5 has more defects because the D peak represents a defect peak caused by the low symmetry or irregularity of the carbon material [32]. The COCLPs obtained from the OCLPs were characterized using XRD and Raman spectroscopy. Figure 3a summarizes the XRD spectra of the COCLP-3.5, COCLP-4.5, and COCLP-5.0, showing that all the COCLPs exhibit obvious diffraction peaks at 43°, corresponding to the (100) crystal planes of the graphite structure. The results indicate that COCLP-3.5, COCLP-4.5, and COCLP-5.0 have amorphous graphite structures [28,29]. The diffraction peak intensity of the (100) lattice plane for COCLP-4.5 is the weakest, demonstrating that COCLP-4.5 has the highest structural disorder [30]. Figure 3b shows that there are two characteristic peaks at 1343 and 1594 cm −1 , corresponding to the D and G peaks of graphite, respectively. The ratio of the areas of the D peak to the G peak (AD/AG) reflects the order degree of the COCLP structure [31]. The calculated ratios for COCLP-3.5, COCLP-4.5, and COCLP-5.0 are 1.15: 1, 1.18: 1, and 1.13: 1, respectively. This result also illustrates that COCLP-4.5 has more defects because the D peak represents a defect peak caused by the low symmetry or irregularity of the carbon material [32]. The surface morphologies of COCLP-3.5, COCLP-4.5, and COCLP-5.0 were characterized using SEM, as shown in Figure 4. Figure 4 indicates that the three COCLPs are all porous and present a three-dimensional network structure. The number of pores in the COCLP increases with an increase in the amount of HPMC; however, when the HPMC content is increased to 5.0 g, the pore structure is only partially formed, and the number of pores decreases. The result demonstrates that the pore structure of COCLP-4.5 was excellent. Generally, an abundant number of pores can significantly increase the specific surface area of COCLPs,  The COCLPs obtained from the OCLPs were characterized using XRD and Raman spectroscopy. Figure 3a summarizes the XRD spectra of the COCLP-3.5, COCLP-4.5, and COCLP-5.0, showing that all the COCLPs exhibit obvious diffraction peaks at 43°, corresponding to the (100) crystal planes of the graphite structure. The results indicate that COCLP-3.5, COCLP-4.5, and COCLP-5.0 have amorphous graphite structures [28,29]. The diffraction peak intensity of the (100) lattice plane for COCLP-4.5 is the weakest, demonstrating that COCLP-4.5 has the highest structural disorder [30]. Figure 3b shows that there are two characteristic peaks at 1343 and 1594 cm −1 , corresponding to the D and G peaks of graphite, respectively. The ratio of the areas of the D peak to the G peak (AD/AG) reflects the order degree of the COCLP structure [31]. The calculated ratios for COCLP-3.5, COCLP-4.5, and COCLP-5.0 are 1.15: 1, 1.18: 1, and 1.13: 1, respectively. This result also illustrates that COCLP-4.5 has more defects because the D peak represents a defect peak caused by the low symmetry or irregularity of the carbon material [32]. The surface morphologies of COCLP-3.5, COCLP-4.5, and COCLP-5.0 were characterized using SEM, as shown in Figure 4. Figure 4 indicates that the three COCLPs are all porous and present a three-dimensional network structure. The number of pores in the COCLP increases with an increase in the amount of HPMC; however, when the HPMC content is increased to 5.0 g, the pore structure is only partially formed, and the number of pores decreases. The result demonstrates that the pore structure of COCLP-4.5 was excellent. Generally, an abundant number of pores can significantly increase the specific surface area of COCLPs, The surface morphologies of C OCLP-3.5 , C OCLP-4.5 , and C OCLP-5.0 were characterized using SEM, as shown in Figure 4. Figure 4 indicates that the three C OCLPs are all porous and present a three-dimensional network structure. The number of pores in the C OCLP increases with an increase in the amount of HPMC; however, when the HPMC content is increased to 5.0 g, the pore structure is only partially formed, and the number of pores decreases. The result demonstrates that the pore structure of C OCLP-4.5 was excellent. Generally, an abundant number of pores can significantly increase the specific surface area of C OCLPs , thereby providing more storage sites and transport channels for electrolyte ions. This is beneficial for improving the electrochemical performance [33]. thereby providing more storage sites and transport channels for electrolyte ions. This is beneficial for improving the electrochemical performance [33]. Additionally, Figure 5a further demonstrates that COCLP-4.5 is a porous COCLP. When COCLP-4.5 is used as the electrode material, these disordered microporous structures can provide sufficient active sites for charge storage [34]. Figure 5b-e are element distribution diagrams obtained from the EDS analysis of COCLP-4.5, showing that carbon, nitrogen, and oxygen were uniformly distributed in the carbon framework. Abundant nitrogen and oxygen can introduce pseudocapacitance and enhance the capacitance performance of the Additionally, Figure 5a further demonstrates that C OCLP-4.5 is a porous C OCLP . When C OCLP-4.5 is used as the electrode material, these disordered microporous structures can provide sufficient active sites for charge storage [34]. Figure 5b-e are element distribution diagrams obtained from the EDS analysis of C OCLP-4.5 , showing that carbon, nitrogen, and oxygen were uniformly distributed in the carbon framework. Abundant nitrogen and oxygen can introduce pseudocapacitance and enhance the capacitance performance of the electrode material. Additionally, Figure 5a further demonstrates that COCLP-4.5 is a porous COCLP. When COCLP-4.5 is used as the electrode material, these disordered microporous structures can provide sufficient active sites for charge storage [34]. Figure 5b-e are element distribution diagrams obtained from the EDS analysis of COCLP-4.5, showing that carbon, nitrogen, and oxygen were uniformly distributed in the carbon framework. Abundant nitrogen and oxygen can introduce pseudocapacitance and enhance the capacitance performance of the electrode material. The COCLPs were subjected to N2 adsorption-desorption measurements to explore the pore characteristics. Figure 6 shows that all the COCLPs exhibit obvious type I isotherm characteristics, indicating that these samples are rich in micropores [35]. Table 1 summarizes the pore structure characteristics of the COCLPs, showing that the specific surface area and pore volume of these samples are mainly provided by the micropores and mesopores. Among the three samples, COCLP-4.5 has the largest specific surface area (1589 m 2 ·g −1 ) and the highest pore volume (0.657 cm 3 ·g −1 ), which further confirm that COCLP-4.5 has the best pore structure. Numerous studies have demonstrated that the large specific surface area and rich pore structure of porous carbon material can greatly promote the storage and rapid migration of ions, resulting in the excellent specific capacitance performance of supercapacitors [36,37]. The aqueous electrolytes currently used in supercapacitors are mainly sulfuric acid (H2SO4, acidic), KOH (alkaline), and sodium sulfate (Na2SO4, neutral). The electrolyte ions in these electrolytes mainly exist as hydrated ions (H + , K + , OH − , Na + , The C OCLPs were subjected to N 2 adsorption-desorption measurements to explore the pore characteristics. Figure 6 shows that all the C OCLPs exhibit obvious type I isotherm characteristics, indicating that these samples are rich in micropores [35]. Table 1 summarizes the pore structure characteristics of the C OCLPs , showing that the specific surface area and pore volume of these samples are mainly provided by the micropores and mesopores. Among the three samples, C OCLP-4.5 has the largest specific surface area (1589 m 2 ·g −1 ) and the highest pore volume (0.657 cm 3 ·g −1 ), which further confirm that C OCLP-4.5 has the best pore structure. Numerous studies have demonstrated that the large specific surface area and rich pore structure of porous carbon material can greatly promote the storage and rapid migration of ions, resulting in the excellent specific capacitance performance of supercapacitors [36,37]. The aqueous electrolytes currently used in supercapacitors are mainly sulfuric acid (H 2 SO 4 , acidic), KOH (alkaline), and sodium sulfate (Na 2 SO 4 , neutral). The electrolyte ions in these electrolytes mainly exist as hydrated ions (H + , K + , OH − , Na + , and SO 2− 4 ). Based on Table 1, it can be found that the C OCLPs obtained can meet the fast migration requirements of these electrolyte ions, thereby significantly improving the conductivity of carbon-based electrodes and enhancing their electrochemical performance.  . Based on Table 1, it can be found that the COCLPs obtained can meet the migration requirements of these electrolyte ions, thereby significantly improving the ductivity of carbon-based electrodes and enhancing their electrochemical performanc  Further analysis of the surface electronic states and elemental compositions of COCLPs samples was performed using XPS. Figure 7a shows that there are three peak the spectra of all the samples. The binding energies of the three peaks are 285, 400, 532 eV, corresponding to C 1s, N 1s, and O 1s, respectively. The results also prove carbon, nitrogen, and oxygen are present in the three samples. Table 2 lists the sur element contents of the three samples. These samples are mainly a carbon-based fra work with oxygen and nitrogen. Fine analyses of the C 1s, N 1s, and O 1s spectra of C 4.5 are performed using the peak differentiation fitting method, as shown in Figure 7 The C 1s spectrum (Figure 7b) can be matched by four peaks at 284.8, 285.7, 286.8, 289.0 eV, corresponding to the C-C, C-N, C-O, and COOR groups, respectively [38]. N 1s spectrum, shown in Figure 7c, is deconvoluted into four peaks of 398.8, 400.3, 40 and 402.4 eV, corresponding to pyridinic-N (N-6) (11.70%), pyrrolic-N (N-5) (52.1 quaternary-N (N-Q) (29.79%), and oxidized N (N-X) (6.38%), respectively. In particu the pyridinic-N and pyrrolic-N contents reach 63.83%. A high content of N-6 and N beneficial for introducing pseudo-capacitance and providing electrochemically ac sites and quaternary nitrogen (N-Q) can effectively improve the conductivity of C and promote electron transfer in the carbon matrix [35,39]. The deconvoluted O 1s p displayed four peaks at 531.2, 532.3, 533.3, and 534.2 eV, representing the oxygen at in the C=O, C-O/C-OH, COOR, and N-O groups, respectively (shown in Figure  [ 35,39]. According to a previous report [40], the oxygen groups are evenly distribute the carbon framework, which can improve the interfacial tension between the carb based porous material and electrolyte to reduce the interfacial resistance. Further analysis of the surface electronic states and elemental compositions of the C OCLPs samples was performed using XPS. Figure 7a shows that there are three peaks in the spectra of all the samples. The binding energies of the three peaks are 285, 400, and 532 eV, corresponding to C 1s, N 1s, and O 1s, respectively. The results also prove that carbon, nitrogen, and oxygen are present in the three samples. Table 2 lists the surface element contents of the three samples. These samples are mainly a carbon-based framework with oxygen and nitrogen. Fine analyses of the C 1s, N 1s, and O 1s spectra of C OCLP-4.5 are performed using the peak differentiation fitting method, as shown in Figure 7b [38]. The N 1s spectrum, shown in Figure 7c, is deconvoluted into four peaks of 398.8, 400.3, 400.8, and 402.4 eV, corresponding to pyridinic-N (N-6) (11.70%), pyrrolic-N (N-5) (52.13%), quaternary-N (N-Q) (29.79%), and oxidized N (N-X) (6.38%), respectively. In particular, the pyridinic-N and pyrrolic-N contents reach 63.83%. A high content of N-6 and N-5 is beneficial for introducing pseudo-capacitance and providing electrochemically active sites and quaternary nitrogen (N-Q) can effectively improve the conductivity of C OCLPs and promote electron transfer in the carbon matrix [35,39]. The deconvoluted O 1s peak displayed four peaks at 531.2, 532.3, 533.3, and 534.2 eV, representing the oxygen atoms in the C=O, C-O/C-OH, COOR, and N-O groups, respectively (shown in Figure 7d) [35,39]. According to a previous report [40], the oxygen groups are evenly distributed in the carbon framework, which can improve the interfacial tension between the carbon-based porous material and electrolyte to reduce the interfacial resistance.

Electrochemistry Measurements
The electrochemical performances of the electrode materials were evaluated usi three-electrode system. Figure 8a shows the CV plots of the different COCLPs (COCLP-3.5, C 4.5, and COCLP-5.0) at a sweep rate of 5 mV·s −1 . All the samples display a typical rectang shape, indicating that the capacitive behavior of these materials is mainly electric dou layer capacitance. Concurrently, these curves have a broad peak in the voltage windo −0.8 to −0.3 V, which is caused by the oxidation-reduction reaction of nitrogen and oxy atoms contained in these samples during the charge and discharge process. Moreover pseudo-capacitance introduced by the redox reaction can significantly increase the cific capacitance of carbon electrodes. The COCLP-4.5 sample exhibits the largest encir area of the CV curve among the three samples, which also illustrates that COCLP-4.5 ha highest specific capacitance. Figure 8b shows the constant GCD curves for the COCLPs current density of 1 A·g −1 . The GCD curves for the three samples are all quasi-isosc triangle shapes, indicating that the capacitance is mainly electric double-layer capacit (EDLC), and the slight deformation is attributed to the existence of pseudo-capacita According to Equation (1), the specific capacitances of COCLP-3.5, COCLP-4.5, and COCLP-5.0 current density of 1 A·g −1 are 302, 503, and 330 F·g −1 , respectively. This result shows the specific capacitance of COCLP-4.5 is the largest, owing to its large specific surface (1589 m 2 ·g −1 ) and pore volume (0.657 cm 3 ·g −1 ). Figure 8c presents the CV curves for C 4.5 at different scanning rates. It reveals that the COCLP-4.5 still maintains a quasi-rectang

Electrochemistry Measurements
The electrochemical performances of the electrode materials were evaluated using a three-electrode system. Figure 8a shows the CV plots of the different C OCLPs (C OCLP-3.5 , C OCLP-4.5 , and C OCLP-5.0 ) at a sweep rate of 5 mV·s −1 . All the samples display a typical rectangular shape, indicating that the capacitive behavior of these materials is mainly electric double-layer capacitance. Concurrently, these curves have a broad peak in the voltage window of −0.8 to −0.3 V, which is caused by the oxidation-reduction reaction of nitrogen and oxygen atoms contained in these samples during the charge and discharge process. Moreover, the pseudo-capacitance introduced by the redox reaction can significantly increase the specific capacitance of carbon electrodes. The C OCLP-4.5 sample exhibits the largest encircled area of the CV curve among the three samples, which also illustrates that C OCLP-4.5 has the highest specific capacitance. Figure 8b shows the constant GCD curves for the C OCLPs at a current density of 1 A·g −1 . The GCD curves for the three samples are all quasi-isosceles triangle shapes, indicating that the capacitance is mainly electric double-layer capacitance (EDLC), and the slight deformation is attributed to the existence of pseudo-capacitance. According to Equation (1), the specific capacitances of C OCLP-3.5 , C OCLP-4.5 , and C OCLP-5.0 at a current density of 1 A·g −1 are 302, 503, and 330 F·g −1 , respectively. This result shows that the specific capacitance of C OCLP-4.5 is the largest, owing to its large specific surface area (1589 m 2 ·g −1 ) and pore volume (0.657 cm 3 ·g −1 ). Figure 8c presents the CV curves for C OCLP-4.5 at different scanning rates. It reveals that the C OCLP-4.5 still maintains a quasi-rectangular shape at scan rates of 5-50 mV·s −1 , indicating that the good pore structure of C OCLP-4.5 enables the rapid migration of electrolyte ions to result in its good rate capability. Figure 8d presents the GCD curves for C OCLP-4.5 at current densities of 0.5-20 A g −1 , showing that the GCD curve does not exhibit a significant IR drop at a high current density of 20 A·g −1 . Therefore, it demonstrates that the C OCLP-4.5 has a high conductivity, good rate capability, and electrochemical reversibility. The specific capacitances are calculated as 522, 503, 432, 396, 363, and 319 F·g −1 at current densities of 0.5, 1, 2, 5, 10, and 20 A·g −1 , respectively. Comparing the electrochemical performance of C OCLP-4.5 with that of the references, the result is listed in Table 3. According to Table 3, the electrochemical performance of C OCLP-4.5 is better than that of other electroactive materials reported in the literature. This is attributed to the unique network structure and rich N/O content of the crosslinked polymer fabricated in this study.  Figure 8e presents the EIS curves for C OCLPs and the equivalent circuit model (the inset of Figure 8e), showing that C OCLP-4.5 has the lowest R ct (internal charge transfer resistance) and R s (contact resistance with the electrolyte) among the three materials. That is, in the high-frequency region, the R ct of C OCLP-4.5 is 0.042 Ω, lower than those of C OCLP-3.5 (0.152 Ω) and C OCLP-5.0 (0.183 Ω). The low R s demonstrates that the electrolyte ions are readily transferred to the surface of the C OCLP-4.5 electrode [48]. Additionally, the linear curve of C OCLP-4.5 is almost vertical in the low-frequency region. The EIS results illustrate that the structure of C OCLP-4.5 is beneficial for charge transfer and the efficient diffusion of electrolyte ions. For supercapacitors, the cycling stability is a significant parameter to estimate their practical application. Figure 8f shows that C OCLP-4.5 retains 83% of its initial specific capacitance value after 5000 cycles at a current density of 5 A g −1 . The surface morphology of C OCLP-4.5 after cycling was characterized by SEM, as shown in Figure 9. Compared with the C OCLP-4.5, before (Figure 4b) shows that the pore structure of C OCLP-4.5 has some damage and collapses after 5000 cycles.
A symmetric supercapacitor was constructed using C OCLP-4.5 to evaluate its practical application. Figure 10a shows the CV curves for the symmetric supercapacitor at different scan rates. The curves maintained a quasi-rectangular shape at a scan rate of 50 mV·s −1 . A slight deformation indicates that the electrochemical behavior of a symmetric supercapacitor is a combination of the EDLC and pseudocapacitance. Figure 10b shows that the GCD curves for the symmetric supercapacitor increased with an increasing current density from 1 to 20 A·g −1 . Based on Equation (2), the specific capacitance of C OCLP-4.5 is 203 F·g −1 at 1 A·g −1 and its specific capacitance remains 150 F·g −1 at 10 A·g −1 , demonstrating a good rate capability even at high current densities for the symmetric supercapacitor. Figure 10c shows the cycle stability curve at a current density of 10 A·g −1 . It displays that the capacitance retention of the device is 84.0% after 5000 cycles, reflecting good cycling stability. Figure 10d indicates that the symmetric capacitor obtains an energy density of 18.04 Wh·kg −1 at a power density of 200.0 W·kg −1 based on Equations (3) and (4), significantly higher than those reported in recent years (13. [25], 10.83 [49], 13.60 [50], 7.00 [51], 13.86 [52], 10.60 [53], and 15.50 Wh·kg −1 [54]). Specifically, the symmetric supercapacitor device successfully powers up a light-emitting diode (the inset of Figure 10d). As shown in the video (see Supplementary Materials File S1), the light-emitting diode can last for a while. Obviously, the N/O-doped porous C OCLPs are expected to be used in supercapacitors. 396, 363, and 319 F·g −1 at current densities of 0.5, 1, 2, 5, 10, and 20 A·g −1 , respectively. Comparing the electrochemical performance of COCLP-4.5 with that of the references, the result is listed in Table 3. According to Table 3, the electrochemical performance of COCLP- 4.5 is better than that of other electroactive materials reported in the literature. This is attributed to the unique network structure and rich N/O content of the crosslinked polymer fabricated in this study.    Figure 8e presents the EIS curves for COCLPs and the equivalent circuit model (the inset of Figure 8e), showing that COCLP-4.5 has the lowest Rct (internal charge transfer resistance) and Rs (contact resistance with the electrolyte) among the three materials. That is, in the high-frequency region, the Rct of COCLP-4.5 is 0.042 Ω, lower than those of COCLP-3.5 (0.152 Ω) and COCLP-5.0 (0.183 Ω). The low Rs demonstrates that the electrolyte ions are readily transferred to the surface of the COCLP-4.5 electrode [48]. Additionally, the linear curve of COCLP-4.5 is almost vertical in the low-frequency region. The EIS results illustrate that the structure of COCLP-4.5 is beneficial for charge transfer and the efficient diffusion of electrolyte ions. For supercapacitors, the cycling stability is a significant parameter to estimate their practical application. Figure 8f shows that COCLP-4.5 retains 83% of its initial specific capacitance value after 5000 cycles at a current density of 5 A g −1 . The surface morphology of COCLP-4.5 after cycling was characterized by SEM, as shown in Figure 9. Compared with the COCLP-4.5, before (Figure 4b) shows that the pore structure of COCLP-4.5 has some damage and collapses after 5000 cycles. A symmetric supercapacitor was constructed using COCLP-4.5 to evaluate its practical application. Figure 10a shows the CV curves for the symmetric supercapacitor at different scan rates. The curves maintained a quasi-rectangular shape at a scan rate of 50 mV·s −1 . A slight deformation indicates that the electrochemical behavior of a symmetric supercapacitor is a combination of the EDLC and pseudocapacitance. Figure 10b shows that the GCD curves for the symmetric supercapacitor increased with an increasing current density from 1 to 20 A·g −1 . Based on Equation (2), the specific capacitance of COCLP-4.5 is 203 F·g −1 at 1 A·g −1 and its specific capacitance remains 150 F·g −1 at 10 A·g −1 , demonstrating a good rate capability even at high current densities for the symmetric supercapacitor. Figure 10c  Wh·kg at a power density of 200.0 W·kg based on Equations (3) and (4), significantly higher than those reported in recent years (13. [25], 10.83 [49], 13.60 [50], 7.00 [51], 13.86 [52], 10.60 [53], and 15.50 Wh·kg −1 [54]). Specifically, the symmetric supercapacitor device successfully powers up a light-emitting diode (the inset of Figure 10d). As shown in the video (see Supplementary Materials File 1), the light-emitting diode can last for a while. Obviously, the N/O-doped porous COCLPs are expected to be used in supercapacitors.

Conclusions
In this study, a network-structured organic crosslinked polymer was used as a carbon source to obtain N/O-doped porous COCLPs. The results indicated that the COCLP-4.5 obtained by optimizing the raw materials exhibited an excellent electrochemical performance. For instance, the specific capacitance of COCLP-4.5 was as high as 522 F·g −1 at a current density of 0.5 A·g −1 , and still exhibited 309 F·g −1 at 20 A·g −1 in a three-electrode system. Furthermore, the symmetric capacitor achieved an energy density of 18.04 Wh·kg −1 at a power density of 200.0 W·kg −1 . The COCLPs benefitted from the net structure of organic crosslinked polymers to form hierarchical porous carbon and the pseudocapacitance introduced by heteroatoms. Therefore, the method for fabricating carbon material proposed in this study provides a new strategy for the development of electrode materials with high electrochemical performance.

Conclusions
In this study, a network-structured organic crosslinked polymer was used as a carbon source to obtain N/O-doped porous C OCLPs. The results indicated that the C OCLP-4.5 obtained by optimizing the raw materials exhibited an excellent electrochemical performance. For instance, the specific capacitance of C OCLP-4.5 was as high as 522 F·g −1 at a current density of 0.5 A·g −1 , and still exhibited 309 F·g −1 at 20 A·g −1 in a three-electrode system. Furthermore, the symmetric capacitor achieved an energy density of 18.04 Wh·kg −1 at a power density of 200.0 W·kg −1 . The C OCLPs benefitted from the net structure of organic crosslinked polymers to form hierarchical porous carbon and the pseudocapacitance introduced by heteroatoms. Therefore, the method for fabricating carbon material proposed in this study provides a new strategy for the development of electrode materials with high electrochemical performance.