Semi-Interpenetrating Network Anion Exchange Membranes by Thiol–Ene Coupling Reaction for Alkaline Fuel Cells and Water Electrolyzers

In this work, a thiol–ene coupling reaction was employed to prepare the semi-interpenetrating polymer network AEMs. The obtained QP-1/2 membrane exhibits high hydroxide conductivity (162.5 mS cm−1 at 80 °C) with a relatively lower swelling ratio, demonstrating its mechanical strength of 42 MPa. This membrane is noteworthy for its improved alkaline stability, as the semi-interpenetrating network effectively limits the attack of hydroxide. Even after being treated in 2 M NaOH at 80 °C for 600 h, 82.5% of the hydroxide conductivity is maintained. The H2/O2 fuel cell with QP-1/2 membrane displays a peak power density of 521 mW cm−2. Alkaline water electrolyzers based on QP-1/2 membrane demonstrated a current density of 1460 mA cm−2 at a cell voltage of 2.00 V using NiCoFe catalysts in the anode. All the results demonstrate that a semi-interpenetrating structure is a promising way to enhance the mechanical property, ionic conductivity, and alkaline stability of AEMs for the application of alkaline fuel cells and water electrolyzers.


Introduction
Global environmental and energy issues have been greatly exacerbated by the usage of fossil fuels. Currently, people are looking for sustainable and clean energy sources to replace traditional energy sources [1]. Hydrogen energy is a clean and renewable energy source. Fuel cells have promising potential in terms of generating electricity by using clean hydrogen energy [2][3][4]. Moreover, the electrolysis is a clean and efficient method for obtaining hydrogen from water [5][6][7]. The anion exchange membrane fuel cells (AEMFCs) and anion exchange membrane water electrolysis (AEMWE) have several advantages such as fast oxygen reduction reactions, inhibited fuel crossover, and low commercial cost [8,9]. Thus, AEMFCs and AEMWE technologies can be considered eco-friendly and sustainable alternatives to traditional energy sources that can help mitigate the problems caused by global environmental and energy issues [10].
The essential component of AEMFCs and AEMWE is the anion exchange membrane (AEM), which is designed for separating the cathode and anode of the battery, and it is crucial for ion transport [11]. It directly determines the performance of AEMFCs, including service life and power density [12]. Nevertheless, the need to strike a balance between the mechanical properties and ionic conductivity of AEMs presents an urgent challenge. Poly(arylene)-based polymer backbones prepared by an acid-catalyzed polycondensation are popular in the boom of ether-free polymers. The resulting ether-free polymer frameworks are remarkable for their chemical durability, as there are no alkaline-sensitive ether linkages. This offers a promising alternative to traditional AEM materials with ether-free backbones and facile synthetic procedures [13][14][15]. However, large-scale commercialization

Synthesis and Structure Characterization
The preparation route for QP-1/x (1/x = 1:1, 1:2, 1:3) AEMs with the semi-interpenetrating network is shown in Scheme 1. The successful preparation of QC, PAP-N, and PAP-TP-85 was determined using 1 H NMR. The 1 H NMR spectra of QC were obtained, as shown in Figure S1, and the 1 H NMR spectra of PAP-N and PAP-TP-85 are displayed in Figures S2 and S3, respectively. These spectra showed shifts from the arylene protons at 7-8 ppm, as well as shifts from the piperidinium ring and the methyl protons between 2.0 and 3.6 ppm. Additionally, protonation of the piperidine by TFA led to the splitting of signals from the resulting piperidinium protons [16]. The hypercrosslinked polymers QC-DO could not be dissolved in the deuterated reagent due to the occurrence of a cross-linking reaction. Thus, as shown in Figure S4, FT-IR spectroscopy was used to characterize QC-DO. The disappearance of the peak (v = 1639) in QC-DO after the cross-linking reaction provided strong evidence supporting the formation of a covalent cross-linking network [22].

Morphological Characterization of sIPN AEMs
The microphase morphology of the PAP-TP-85 and QP-1/2 AEMs were evaluated using the SEM. Figure 1A,B showed that all membrane surfaces are smooth. As shown in Figure 1B, the energy dispersive spectroscopy (EDS) test verified the distribution of elemental sulfur in the QP-1/2 AEM, indicating the successful construction of the sIPN network. Both AEMs were yellowish with slight light transmission, as shown in Figure  1C, and have a smooth and dense surface. The QP-1/2 AEM was observed to have good mechanical flexibility. The smooth and dense construction is significant as it inhibits fuel crossover in fuel cells while ensuring excellent dimensional stability [23,24]. Moreover, owing to the uniform and dense distribution of N, the AEMs can combine substantial quantities of OH − , providing a favorable structural guarantee for high ionic conductivity in QP-1/x AEMs. Scheme 1. Preparation route for QP-1/x (1/x = 1:1, 1:2, 1:3) AEMs with semi-interpenetrating network.

Morphological Characterization of sIPN AEMs
The microphase morphology of the PAP-TP-85 and QP-1/2 AEMs were evaluated using the SEM. Figure 1A,B showed that all membrane surfaces are smooth. As shown in Figure 1B, the energy dispersive spectroscopy (EDS) test verified the distribution of elemental sulfur in the QP-1/2 AEM, indicating the successful construction of the sIPN network. Both AEMs were yellowish with slight light transmission, as shown in Figure 1C, and have a smooth and dense surface. The QP-1/2 AEM was observed to have good mechanical flexibility. The smooth and dense construction is significant as it inhibits fuel crossover in fuel cells while ensuring excellent dimensional stability [23,24]. Moreover, owing to the uniform and dense distribution of N, the AEMs can combine substantial quantities of OH − , providing a favorable structural guarantee for high ionic conductivity in QP-1/x AEMs.

Thermal Stability of sIPN AEMs
The thermal stability of AEMs is particularly important since AEMFCs operate at temperatures ranging from 60 to 90 °C, requiring good thermal stability of the AEMs. The thermal decomposition temperature (Td,95, temperature at 5% weight loss) of the prepared AEMs was investigated. The TGA curves of the OHform of the QP-1/x AEMs were tested under N2 atmosphere (Figure 2A). Before testing, the membrane was treated by holding at 100 °C for 10 min to remove moisture. The PAP-TP-85 was decomposed at Td,95 = 167.29 °C, and its weight loss is mainly due to the thermal degradation of the quaternary ammonium group on the molecular chain of PAP-TP-85. The influence of

Thermal Stability of sIPN AEMs
The thermal stability of AEMs is particularly important since AEMFCs operate at temperatures ranging from 60 to 90 • C, requiring good thermal stability of the AEMs. The thermal decomposition temperature (T d,95 , temperature at 5% weight loss) of the prepared AEMs was investigated. The TGA curves of the OH − form of the QP-1/x AEMs were tested under N 2 atmosphere (Figure 2A). Before testing, the membrane was treated by holding at 100 • C for 10 min to remove moisture. The PAP-TP-85 was decomposed at T d,95 = 167.29 • C, and its weight loss is mainly due to the thermal degradation of the quaternary ammonium group on the molecular chain of PAP-TP-85. The influence of hypercrosslinked polymers QC-DO on the thermal stability of QP-1/x AEMs with semi-interpenetrating network structure is shown in the TGA plot. The thermal stability of the quaternary ammonium groups in QP-1/1, QP-1/2, and QP-1/3 anion exchange membranes is better than that of PAP-TP-85 anion exchange membranes. The QC-DO contains numerous OH − ions that can easily form intramolecular and intermolecular hydrogen bonds, the hydrogen bonding can increase the force between ionic groups and chain segments and improve the thermal stability of ionic polymer. In any case, the thermal degradation temperatures for the AEMs were above the operating temperatures of typical alkaline energy devices.

Water Uptake, Swelling Ratio, and Ion Exchange Capacity (IEC) of sIPN AEMs
AEMs require an appropriate water uptake (WU) and swelling ratio (SR) to ensure efficient OHconduction. Excessive WU dilutes the concentration of OH -, causing a decrease in ionic conductivity of the membrane. High SR compromises the mechanical properties and dimensional stability of AEM. Figure 2C,D demonstrate that the WU and SR of PAP-TP-85 and QP-1/x AEMs are positively associated with the test temperature. As seen in Figure 2, QP-1/2, and QP-1/3 AEMs exhibit appropriate WU and SR; the semi-

Water Uptake, Swelling Ratio, and Ion Exchange Capacity (IEC) of sIPN AEMs
AEMs require an appropriate water uptake (WU) and swelling ratio (SR) to ensure efficient OH − conduction. Excessive WU dilutes the concentration of OH − , causing a decrease in ionic conductivity of the membrane. High SR compromises the mechanical properties and dimensional stability of AEM. Figure 2C,D demonstrate that the WU and SR of PAP-TP-85 and QP-1/x AEMs are positively associated with the test temperature. As seen in Figure 2, QP-1/2, and QP-1/3 AEMs exhibit appropriate WU and SR; the semiinterpenetrating polymer network plays an important role in maintaining the dimensional stability of membranes. Proper WU and SR promote the generation of hydrated ion phase domains in AEMs that enable efficient ion transport, ensuring good mechanical properties, dimensional stability, and high ionic conductivity.
The IEC values of OH − form QP-1/x AEMs at 25 • C in Table 1. The establishment of semi-interpenetrating networks (sIPN) has been found to be an effective solution to the problem of balancing ionic conductivity and dimensional stability. This is because the increase in the IEC value improves the conductivity of AEMs, but it can adversely affect the alkali stability and mechanical properties of the membrane. Through cross-linking, the IEC value can be increased without negatively impacting the mechanical properties, as the sIPN structure provides additional strength and stability to the membrane.

Mechanical Property and Hydroxide Conductivity of sIPN AEMs
In the operation of energy devices, AEMs should possess excellent mechanical properties since they are mechanically constrained in between GDLs. Therefore, the mechanical properties of QP-1/x AEMs were evaluated using the fracture tension method. Figure 3A illustrates the mechanical properties of QP-1/x and PAP-TP-85 AEMs. The tensile strength of dry membranes and the elongation at break of membranes tended to increase and then decrease upon the inclusion of QC-DO content in the QP-1/x series membranes, as compared to the linear PAP-TP-85 membranes. This suggests that the increase in cross-linking densities leads to an increase in membrane tension. However, if the cross-linking density exceeds a certain threshold, the intermolecular interactions will become too strong, resulting in increased membrane rigidity and decreased elongation at break. Nonetheless, the QP-1/x AEMs met all the necessary mechanical property requirements required by alkaline energy devices.

Mechanical Property and Hydroxide Conductivity of sIPN AEMs
In the operation of energy devices, AEMs should possess excellent mechanical properties since they are mechanically constrained in between GDLs. Therefore, the mechanical properties of QP-1/x AEMs were evaluated using the fracture tension method. Figure 3A illustrates the mechanical properties of QP-1/x and PAP-TP-85 AEMs. The tensile strength of dry membranes and the elongation at break of membranes tended to increase and then decrease upon the inclusion of QC-DO content in the QP-1/x series membranes, as compared to the linear PAP-TP-85 membranes. This suggests that the increase in cross-linking densities leads to an increase in membrane tension. However, if the cross-linking density exceeds a certain threshold, the intermolecular interactions will become too strong, resulting in increased membrane rigidity and decreased elongation at break. Nonetheless, the QP-1/x AEMs met all the necessary mechanical property requirements required by alkaline energy devices. The ionic conductivity of hydroxide ions in the QP-1/x AEMs gradually increased with increasing temperature ( Figure 3B). In addition, increasing the QC-DO content leads to an increase in the number of quaternary ammonium groups in the AEM. This increase The ionic conductivity of hydroxide ions in the QP-1/x AEMs gradually increased with increasing temperature ( Figure 3B). In addition, increasing the QC-DO content leads to an increase in the number of quaternary ammonium groups in the AEM. This increase in groups further enhances the ionic conductivity of the membrane. As a result, the ionic conductivity of the composite membrane exhibits a trend of QP-1/1 > QP-1/2 > QP-1/3 > PAP-TP-85. However, it should be noted that the mechanical properties of QP-1/1 AEM are significantly inferior to QP-1/2 AEM. AFM images provided in Figure S5a-d demonstrated that the microphase separation of the prepared QP-1/x AEMs is uniform and distinct. The darker regions represent the hydrophilic parts, whereas the lighter regions are the hydrophobic regions [25]. A more significant and denser microphase separation is observed in the QP-1/2 AEM ( Figure S5c), promoting rapid ion transport, and thereby increasing the hydroxide ion conductivity. Overall, the performance of QP-1/x AEMs has certain advantages over some previously reported AEMs [26,27]. These results indicate that QP-1/x AEMs hold the potential for fuel cells and water electrolyzers well.

Chemical Stability of sIPN AEMs
The stability of anion exchange membranes (AEMs) under alkaline conditions is a crucial factor for their practical utilization in alkaline energy devices. The degradation mechanisms of AEMs under alkaline conditions involve carbon affinity substitution, Hoffman elimination, and the formation of nitrogen ylides due to the presence of OH − ions [28][29][30]. The ability of AEMs to transfer OH − ions plays a significant role in determining their operational longevity. Therefore, evaluating the resistance to alkali is vital when considering the application of AEMs in fuel cells. Among various AEM options, the QP-1/2 AEM exhibits the highest alkaline stability. Immersion of QP-1/2 AEM in a 2 M NaOH aqueous solution at 80 • C for 600 h did not result in the emergence of new vibrational peaks or the significant disappearance of existing peaks ( Figure 4A). Notably, the stretching vibration peak at 3100 cm −1 , corresponding to the C-H bond on the benzene ring, and the stretching vibration of the C-N bond at 1190 cm −1 remained almost unchanged, highlighting the excellent stability of QP-1/2 AEM under alkaline conditions. Additionally, the stretching vibration peak of C-O at 1300-1000 cm −1 confirms the successful synthesis of sIPN network structured composite membranes.
Molecules 2023, 28, x FOR PEER REVIEW 7 of 14 results indicate that QP-1/x AEMs hold the potential for fuel cells and water electrolyzers well.

Chemical Stability of sIPN AEMs
The stability of anion exchange membranes (AEMs) under alkaline conditions is a crucial factor for their practical utilization in alkaline energy devices. The degradation mechanisms of AEMs under alkaline conditions involve carbon affinity substitution, Hoffman elimination, and the formation of nitrogen ylides due to the presence of OHions [28][29][30]. The ability of AEMs to transfer OH-ions plays a significant role in determining their operational longevity. Therefore, evaluating the resistance to alkali is vital when considering the application of AEMs in fuel cells. Among various AEM options, the QP-1/2 AEM exhibits the highest alkaline stability. Immersion of QP-1/2 AEM in a 2 M NaOH aqueous solution at 80 °C for 600 h did not result in the emergence of new vibrational peaks or the significant disappearance of existing peaks ( Figure 4A). Notably, the stretching vibration peak at 3100 cm −1 , corresponding to the C-H bond on the benzene ring, and the stretching vibration of the C-N bond at 1190 cm −1 remained almost unchanged, highlighting the excellent stability of QP-1/2 AEM under alkaline conditions. Additionally, the stretching vibration peak of C-O at 1300-1000 cm −1 confirms the successful synthesis of sIPN network structured composite membranes. The residual ionic conductivity of QP-1/x AEMs after a 600 h continuous alkali resistance test was analyzed showing that the residual ionic conductivities first decrease rapidly and then decrease slowly with increasing alkali treatment time. The increase in the contents of QC-DO result in the deterioration of the alkali resistance of the membranes, as the water-swelling ability of the membrane becomes larger and more OHcan enter AEM with water, increasing the probability of contact between OHand quaternary amine groups. The residual ionic conductivity was found to be QP-1/2 > QP-1/3 > PAP-TP-85 > QP-1/1. After 600 h of testing, all AEMs had retained more than 80% of their original ionic conductivities, whereas QP-1/2 AEM exhibited the highest residual ionic conductivity of 83% among the tested membranes ( Figure 4B). In conclusion, QP-1/2 AEM shows obvious advantages in alkaline stability compared with some reported membranes, indicating that The residual ionic conductivity of QP-1/x AEMs after a 600 h continuous alkali resistance test was analyzed showing that the residual ionic conductivities first decrease rapidly and then decrease slowly with increasing alkali treatment time. The increase in the contents of QC-DO result in the deterioration of the alkali resistance of the membranes, as the water-swelling ability of the membrane becomes larger and more OH − can enter AEM with water, increasing the probability of contact between OH − and quaternary amine groups. The residual ionic conductivity was found to be QP-1/2 > QP-1/3 > PAP-TP-85 > QP-1/1. After 600 h of testing, all AEMs had retained more than 80% of their original ionic conductivities, whereas QP-1/2 AEM exhibited the highest residual ionic conductivity of 83% among the tested membranes ( Figure 4B). In conclusion, QP-1/2 AEM shows obvious advantages in alkaline stability compared with some reported membranes, indicating that the alkaline stability of QP-1/2 AEM is sufficient for further operation in AEMFCs.

Fuel Cell and Alkaline Water Electrolysis Applications
For H 2 /O 2 single-cell testing, MEAs were constructed using QP-1/x AEMs, which were operated without backpressure at a flow rate of 1000/1000 mL min −1 A/C and at 80 • C with 100% relative humidified H 2 as fuel and O 2 as oxidant. The MEA's catalyst layer dispersibility was examined using scanning electron microscopy (SEM) and energy dispersive spectrometer (EDS) as shown in Figure 5. Figure 5A reveals that the thicknesses of the cathode and anode catalyst layers were similar with no gaps present between the catalyst layer and AEM, resulting in tight combination. Figure 5B,D show that the catalysts Pt and Ru are uniformly distributed on both sides of the membrane. Figure 5C confirmed the successful construction of the sIPN network by the presence of sulfur elements within the film.

Materials
Cyclen, 3,6-dioxo-1,8-octanedithiol, 2,2-dimethoxy-1,2-diphenylethanone (DMPA), ethyl ether, isopropanol, and allyl bromide were purchased from Aladdin (Shanghai, China). Potassium carbonate, sodium hydroxide, and ethanol, methanol, and dimethyl As depicted in Figure 5E, I-V polarization curves were performed at different temperatures under 1 M KOH. With temperature increase, electrochemical performance is improved. The MEA assembled with QP-1/2 AEM produced the highest current density (1.46 A cm −2 at 2.0 V) at 80 • C, which was mainly attributed to the high OH − ion conductivity of QP-1/2 AEM. Durability testing of MEA was carried out under an electrolysis current of 500 Ma cm −2 at 60 • C using 1 M KOH fed anode and cathode. Figure S6 shows that during the initial several hours, the voltage of the cell slightly increases, possibly because of the catalyst's delamination from the catalyst layer [31]. The voltage then remains constant until 9 h, following which it undergoes a slight increase due to light membrane degradation resulting from the OH − attack, which reduces hydroxide conductivity and results in an increased internal resistance. Thereafter, the voltage remains at an average value of 1.82 ± 0.03 V, with minimal fluctuations that can be ascribed to the dynamic nature of water electrolysis. This may arise due to gas accumulation/release from the surface of the catalysts, water uptake changes in the cathode due to water electrolysis and electroosmotic flux. Additionally, water was manually added to the electrolyte solution to sustain the constant KOH concentration, which may cause mild fluctuations. Despite some slight fluctuations, the voltage remains virtually constant over 10 h, indicating the good stability of QP-1/2 AEM-based alkaline water electrolysis.
The AEMs' exceptional airtightness and gas separation capability is demonstrated by the nearly 1.00 V open circuit voltage (OCV) of all samples [32], as depicted in Figure 5F. The QP-1/2 AEM exhibited the highest peak power density (PPD) of 521 mW cm −2 at a current density of 1157.80 mA cm −2 , which is consistent with previous excellent testing performance, as shown in Figure 5F. Although the PPD of the QP-1/2 AEM is not particularly high when compared to the reported data, single-cell performance depends heavily on the MEA's preparation method, catalyst, ionomer content, and operating conditions. This makes it challenging to compare QP-1/x AEMs' single-cell performance with the current literature. Furthermore, this work is a preliminary exploration of QP-1/x AEMs' feasibility in actual alkaline membrane fuel cell devices, with the MEA preparation and operating conditions not being optimized. The authors anticipate that by optimizing these conditions, QP-1/x AEMs' single-cell performance can yield even better results.

Materials
Cyclen, 3,6-dioxo-1,8-octanedithiol, 2,2-dimethoxy-1,2-diphenylethanone (DMPA), ethyl ether, isopropanol, and allyl bromide were purchased from Aladdin (Shanghai, China). Potassium carbonate, sodium hydroxide, and ethanol, methanol, and dimethyl sulfoxide (DMSO) were purchased from Sinopharm Chemical Reagent Co. (Shanghai, China). The Pt/C catalyst was supplied by Johnson Matthey with 60 wt.% Pt on a Vulcan XC-72 carbon carrier. Deionized water was utilized and filtered by a Millipore system. All chemicals and solvents used in this study were analytically graded and commercially available and were not further purified before use.

Synthesis of Quaternized Cyclen (QC)
To synthesize quaternized cyclen (QC), the cyclen (1.00 g, 5.80 mmol) and allyl bromide (8.43 g, 69.65 mmol) were dissolved in 60.00 mL of acetonitrile, and then potassium carbonate (3.20 g, 23.15 mmol) was added. The reaction was refluxed at 80 • C for 72 h. After cooling to room temperature, the solid precipitate was filtered off, and then the yellow clarified solution was added dropwise to diethyl ether. The solid product obtained was washed several times with diethyl ether and dried under vacuum at room temperature to obtain a light yellow solid named QC. The synthesis route of QC is illustrated in Scheme S1a.

Synthesis of Hypercrosslinked Polymers by QC
The synthesis of hypercrosslinked polymers by QC was performed using a thiolene coupling reaction. Firstly, QC (0.12 mmol, 0.10 g) and 3,6-dioxa-1,8-octanedithiol (0.49 mmol, 0.09 g) were dissolved in DMSO to form a 37.50 wt.% solution. Then, photocrosslinking was initiated by the addition of DMPA (5 wt.%, 9.45 mg), and the mixture was exposed to a UV light at 365 nm for 2 h. The resulting material was named QC-DO. The synthesis route of QC-DO as shown in Scheme S1b.

Synthesis of the Poly(aryl piperidinium) (PAP) Polymers
The PAP polymers were synthesized in a two-step procedure. The first step involved the synthesis of neutral poly(aryl piperidine) polymers, known as PAP-N. This was carried out using N-methyl-4-piperidone, 2,2,2-trifluoroacetophenone, and p-terphenyl via the method of polyhydroxy alkylation. In the second step, PAP-N was used to synthesize poly(aryl piperidinium) (PAP) by reacting it with iodomethane through the Menshutkin reaction. The synthesis procedure for PAP-N involved dissolving N-methyl-4piperidone, 2,2,2-trifluoroacetophenone, and p-terphenyl in methylene chloride. To this, 1,1,1-trifluoroacetic acid (TFA) and trifluoromethanesulfonic acid (TFSA) were slowly added dropwise at 0 • C. The reaction was continued at this temperature for 24 h. The resulting solution was then added slowly to an aqueous ethanol solution, and the fibrous solid was filtered, washed, and immersed in 1 M K 2 CO 3 at 50 • C for 12 h. Finally, the product was filtered, washed, and dried under vacuum at 60 • C, yielding 90% polymer. The synthesis procedure for PAP-TP-85 involved suspending PAP-TP-N-85 in DMSO, followed by adding methyl iodide and stirring the solution for 12 h at room temperature. The solution was then added dropwise into ether, and the solid was filtered, washed, and dried under vacuum at 60 • C, with a yield of almost 90%. PAP-TP-85 represents PAP based on p-terphenyl, with 85 being the molar ratio between N-methyl-4-piperidone and aryl monomers (in percent), and 15 being the molar ratio between 2,2,2-trifluoroacetophenone and aryl monomers (in percent). The synthesis routes for PAP-N and PAP-TP-85 are shown in Scheme S2.

Preparation of QC-DO/PAP-TP-85 Anion Exchange Membranes
To prepare QP-1/x anion exchange membranes with the semi-interpenetrating network, QC-DO and PAP-TP-85 were weighed according to different mass ratios. For convenience, the prepared QC-DO/PAP-TP-85 composite films were labeled as QP-1/x, with 1/x being the mass ratio of QC-DO to PAP-TP-85 in the composite films (1/x = 1:1, 1:2, 1:3). The obtained QC-DO was formulated into a 5 wt.% DMSO dispersion with DMSO solvent, and a 10 wt.% DMSO solution of PAP-TP-85 was dropped into it. In this process, the hypercrosslinked polymers QC-DO dissolved and formed a stable semi-interpenetrating network structure with the linear polymer PAP-TP-85. After the film-forming solution was ultrasonically defoamed and filtered to remove impurities, it was poured onto a glass plate and baked at 60 • C for 12 h. After the dried QC-DO/PAP-TP-85 film was carefully removed from the glass plate, it was immersed in a 1.00 mol L −1 NaOH solution for ion exchange to exchange I − to OH − . The NaOH solution was changed every 2 h during the ion exchange process, and the completion of ion exchange was detected by HNO 3 and AgNO 3 . Finally, the QP-1/x membranes were washed in N 2 -saturated deionized water to neutral, cut to the desired shape, and then immersed in N 2 -saturated deionized water for backup.

Characterization
The morphologies of the samples were observed by scanning electron microscopy (SEM, Hitachi S-4700, Tokyo, Japan) fitted with an energy dispersive spectrometer (EDS) detector and via HRTEM (FEI Tecnai G2 F20, Hillsboro, OR, USA). Prior to the test, the samples were sprayed with gold in a vacuum. The infrared spectra were measured on a PerkinElmer-6700 (Glen Waverley, Australia), at a measurement range of 4000-600 cm −1 with a resolution of 4 cm −1 . 1 H NMR spectra were recorded on a Varian 400 MHz spectrometer using CDCl3, or DMSO-d 6 . The thermal stabilities of the AEMs were determined by thermogravimetric analysis (TGA, Universal Analysis 2000) from 30 • C to 800 • C at a heating rate of 10 • C min −1 under an N 2 atmosphere. The stress and elongation of the AEMs were measured with an Instron 5900 system, and the tensile rate was measured at 5 mm min −1 .
To calculate the water uptake (WU) and swelling ratio (SR) of the AEMs, the weight and length of the wet membranes were determined after wiping the extra water. The AEMs were first dried under vacuum at 80 • C until their weight remained constant. Subsequently, the dried AEMs were soaked in deionized water for 24 h at different temperatures. The test results of the AEMs were then obtained using Equations (1) and (2) to characterize their WU and SR, respectively.
Here, W w and W d denote the weights of wet and dried AEMs, while L w and L d denote their respective lengths.
Samples were analyzed using a standard titration approach to determine their ion exchange capacity (IEC). The IEC could be calculated using Equation (3).
Here, C represents the concentration of NaOH solution, V 1 and V 2 are the volumes of HCl and NaOH solutions used to soak the AEMs and titrate, respectively, and M d is the mass of the dried AEMs.
To determine the ionic conductivity (σ) of the AEMs, four-probe AC impedance spectroscopy was performed using CHI660C electrochemical equipment with a frequency range of 1 Hz to 1 × 10 6 Hz. AC impedance measurements were obtained in ultrapure water saturated with N 2 , and the ion conductivity of the membrane (mS cm −1 ) was calculated using Equation (4).
Here, L (cm) represents the distance between the two electrodes, R (kΩ) is the AC impedance of the AEMs, and S (cm 2 ) is the AEMs' cross-sectional area.
The alkaline resistance of the AEMs was evaluated by measuring changes in ionic conductivity before and after immersion in 1 M NaOH solution at 60 • C, over a total test time of 600 h (measured every 120 h at 80 • C).
The performance of the QP-1/2 AEM for water electrolysis was also considered. Pt/C and NiCoFe were used as the cathode catalyst and the anode catalyst, respectively. The catalyst loadings were controlled at 0.5 mg cm −2 for both the electrodes and the active area was 1 cm −2 . The MEA prepared by the hot-pressed method was assembled into a water electrolysis cell. The polarization curve was collected at 40, 50, 60, 70, and 80 • C by the voltage sweep method, and the potential was increased at a rate of 5 mV s −1 . The durability was evaluated at 60 • C by feeding a 1 M aqueous KOH solution into both the electrodes at a flow rate of 3 mL min −1 and applying a constant current density of 500 mA cm −2 .
The catalyst ink was prepared by mixing Pt/C catalyst (cathode, 60 wt.%, Johnson Matthey) or PtRu/C (anode, 40 wt.% of Pt and 20 wt.% of Ru), ionomer (5 wt.% in DMSO), water, and isopropanol at a concentration of 3 wt.%. The ratio of catalyst ionomer was set to 4:1. The PAP-BP-100 ionomer was used for the anode and cathode catalyst layers [14]. After being sonicated for 3 h while keeping the bath temperature lower than 5 • C, the ink was sprayed on the cathode and anode of the AEM to obtain a catalyst-coated membrane (CCM). The noble metal loadings at the cathode and anode were 0.5 mg cm −2 Pt and 0.5 mg cm −2 Pt/Ru, respectively. Finally, fuel cell performance was measured on a Fuel Cell Test System under 100% RH at 80 • C, and the flow rate of H 2 /O 2 was 1 L min −1 without backpressure.

Conclusions
A series of QP-1/x anion exchange membranes (AEMs) was prepared by incorporating hypercrosslinked polymers QC-DO as the framework material and PAP-TP-85 as the primary anion carrier. The introduction of QC-DO in AEMs resulted in apparent microphase separation within the membranes. The semi-interpenetrating polymer network guarantees satisfying mechanical properties and dimensional endurance, as well as high ionic conductivity. The obtained QP-1/x AEMs were proven to be smooth and tough, demonstrating the positive effect of hypercrosslinked polymers QC-DO on the mechanical properties of the AEM. The enhanced alkaline stability is noteworthy due to the effective limitation of hydroxide attack by the semi-interpenetrating network. Notably, the ionic conductivity and fuel cell peak power density of QP-1/2 AEMs were measured to be 162.5 mS cm −1 and 521 mW cm −2 . Moreover, alkaline water electrolyzers based on QP-1/2 AEM demonstrated a current density of 1460 mA cm −2 . The QP-1/x AEMs with the semi-interpenetrating network have great potential for alkaline membrane fuel cells and water electrolyzers.