阅读说明：本技术 一种防冻两性离子水凝胶电解质及其制备方法 (Anti-freezing zwitterion hydrogel electrolyte and preparation method thereof ) 是由 刘利彬 杨健波 班青 盖利刚 李学林 于 2020-12-06 设计创作，主要内容包括：本发明属于超级电容器领域,涉及一种新型两性离子聚合物水凝胶电解质及其制备方法和用途。在LiCl盐的存在下,使用SBMA和HEA采用一锅法无规聚合法制备了两性离子型polySH电解质。两性离子聚合物水凝胶电解质的用途,用于温度响应材料和作为储能设备电解质。一锅法制备为水凝胶电解质的大规模应用提供了便利。(The invention belongs to the field of supercapacitors, and relates to a novel zwitterionic polymer hydrogel electrolyte, and a preparation method and application thereof. Zwitterionic polySH electrolytes were prepared using a one-pot random polymerization process using SBMA and HEA in the presence of LiCl salt. Use of a zwitterionic polymer hydrogel electrolyte for temperature responsive materials and as an energy storage device electrolyte. The one-pot method provides convenience for large-scale application of the hydrogel electrolyte.)

1. A preparation method of hydrogel electrolyte comprises the steps of preparing zwitterionic polySH electrolyte by using SBMA and HEA through a one-pot random polymerization method in the presence of LiCl salt; comprises the following steps:

1) dissolving LiCl in deionized water to prepare LiCl solution;

2) dissolving SBMA and HEA in LiCl solution, adding an initiator after stirring, and then placing in an ice bath to stir for 1.5 h;

3) and (4) carrying out ultrasonic treatment after the solution is completely dissolved, then injecting the solution into a mold, and polymerizing in a sealed environment.

2. The method for preparing a hydrogel electrolyte according to claim 1, wherein the concentration of 1 to 7mol L is prepared in the step 1)^-1In LiCl solution.

3. The method for preparing the hydrogel electrolyte according to claim 1, wherein in the step 2), the molar ratio of SBMA to HEA is 1 (3-5); more preferably, the SBMA and HEA are present in a molar ratio of 1: 4.

4. The method for preparing a hydrogel electrolyte according to claim 1, wherein the stirring of step 2) is performed in an ice bath.

5. The method for preparing the hydrogel electrolyte according to claim 1, wherein in the step 2), the initiator is AIBA or APS, and the addition amount of the initiator is 0.5 to 2 wt% of the total mass of the monomers; more preferably, in the step 2), the amount of the initiator added is 1 wt% based on the total mass of the monomers.

6. The method for preparing a hydrogel electrolyte according to claim 1, wherein the solution is stirred in an ice bath for 1 hour, then the initiator AIBA is added, and then the solution is stirred in an ice bath for 1.5 hours.

7. The method for preparing the hydrogel electrolyte according to claim 1, wherein the ultrasound in step 3) is ultrasound for 8-15 min to remove bubbles; more preferably, sonication is carried out for 10min to remove bubbles.

8. The method for preparing a hydrogel electrolyte according to claim 1, wherein the polymerization in the sealed environment in step 3) is performed by sealing and placing in an environment of 30-50 ℃ for 8-16 h; more preferably, the polymerization in the sealed environment in step 3) is carried out by placing the seal in an environment at 38 ℃ for 12 h.

9. The zwitterionic antifreeze hydrogel electrolyte of any of claims 1 to 8, wherein the Raman spectrum is at-SO₃ ^-Wherein S-O stretching vibration is 1044cm^-1～1054cm^-1，-N⁺(CH₃)₂CH in (1)₃The stretching vibration is 2953cm^-1～2957cm^-1(ii) a DSC demonstration with H₂O forms a Li⁺(H₂O)_nA solvated structure; with a 325% stretch at-40 ℃.

10. Use of the zwitterionic polymer hydrogel electrolyte of claim 9 in a temperature responsive material, a strain responsive material, an ionic conductor at low temperatures or as an energy storage device electrolyte.

Technical Field

The invention belongs to the field of supercapacitors, and relates to a novel zwitterionic polymer hydrogel electrolyte, and a preparation method and application thereof.

Background

With the increasing global energy demand, higher requirements are put on the development of efficient energy storage devices. As a novel energy storage device, the super capacitor is widely concerned by people due to high charging and discharging speed and long service life.

The electrolyte comprises liquid electrolyte and solid electrolyte, and is an indispensable component of the super capacitor. The low conductivity of solid electrolytes compared to liquid electrolytes is a major drawback affecting the high performance of energy storage devices. And the polymer hydrogel electrolyte has higher conductivity at room temperature, so that the polymer hydrogel electrolyte gradually becomes a hot spot in the research of high-performance solid-state supercapacitors. However, since large amounts of water in the hydrogel network will necessarily freeze at sub-zero temperatures, the conductivity of the polymer hydrogel electrolyte at 0 ℃ will be greatly reduced.

Hydrogel capacitors have poor resistance to low temperature environments, limiting their application. Therefore, achieving low-temperature anti-freezing performance and improving ionic conductivity of the hydrogel electrolyte are important challenges for expanding the application range of the hydrogel electrolyte. The addition of organic liquids to hydrogels is one method to obtain antifreeze hydrogels. Common organic liquids include ethylene glycol, glycerol, dimethyl sulfoxide, and the like. In these binary/ternary systems, the interaction of the organic liquid with water molecules is believed to be the primary reason for inhibiting the formation of the ice crystal lattice. However, these hydrogels are either not electrically conductive or have low electrical conductivity due to the presence of organic liquids. In addition, the volatility and high pyrophoricity of organic liquids pose a serious safety hazard to organic hydrogel electrolytes.

At present, the research on the antifreeze hydrogel mainly comes from organisms, and components such as antifreeze protein, antifreeze glycolipid and the like can adhere to the surface of an ice tray to inhibit the formation of ice crystals. However, the types of biomimetic substances suitable as antifreeze additives are limited and the applications in energy storage devices are reported to be rare.

Disclosure of Invention

The invention aims to provide a zwitterionic polymer hydrogel electrolyte and a preparation method thereof, aiming at the defects of the prior art. The amphoteric ion polymer hydrogel electrolyte prepared by the invention not only has good antifreezing performance, but also has higher conductivity, especially high conductivity at low temperature.

A preparation method of hydrogel electrolyte comprises the steps of preparing zwitterionic polySH electrolyte by using SBMA and HEA through a one-pot random polymerization method in the presence of LiCl salt; comprises the following steps:

1) LiCl was dissolved in deionized water to prepare a LiCl solution.

2) SBMA and HEA were dissolved in LiCl solution, initiator was added after stirring, followed by stirring in an ice bath for 1.5 h.

3) And (4) carrying out ultrasonic treatment after the solution is completely dissolved, then injecting the solution into a mold, and polymerizing in a sealed environment.

Preferably, in the step 1), the preparation concentration is 1-7mol L^-1In LiCl solution. More preferably, the preparation concentration is 3-7mol L^-1In LiCl solution.

Preferably, in the step 2), the mol ratio of SBMA to HEA is 1 (3-5). More preferably, the SBMA and HEA are present in a molar ratio of 1: 4.

Preferably, the stirring of step 2) is performed in an ice bath.

Preferably, in the step 2), the addition amount of the initiator is 0.5-2 wt% of the total mass of the monomers. More preferably, in the step 2), the amount of the initiator added is 1 wt% based on the total mass of the monomers. Preferably, the initiator is AIBA or APS; more preferably, the initiator is AIBA.

Preferably, in the step 2), the solution is placed in an ice bath and stirred for 1 hour, then the initiator AIBA is added, and then the solution is placed in the ice bath and stirred for 1.5 hours.

Preferably, the ultrasound in the step 3) is performed for 8-15 min to remove bubbles. More preferably, sonication is carried out for 10min to remove bubbles.

Preferably, the polymerization in the sealed environment in the step 3) is that the seal is placed in an environment with the temperature of 30-50 ℃ for polymerization for 8-16 h. More preferably, the polymerization in the sealed environment in step 3) is carried out by placing the seal in an environment at 38 ℃ for 12 h.

The hydrogel obtained by polymerization is abbreviated as polySH-x, wherein x is the molar concentration of LiCl.

The zwitterion antifreezing hydrogel electrolyte prepared by the method is characterized in that Li⁺The ionic conductivity is improved by the jumping migration of the zwitterion group on the polymer chain; in Raman spectrum, -SO₃ ^-Wherein S-O stretching vibration is 1044cm^-1～1054cm^-1，-N⁺(CH₃)₂CH in (1)₃The stretching vibration is 2953cm^-1～2957cm^-1Indicating the presence of zwitterionic groups and being Li⁺A migration-providing site; DSC demonstration with H₂O forms a Li⁺(H₂O)_nThe solvation structure improves the antifreezing performance of the hydrogel electrolyte, and the hydrogel electrolyte has 325 percent of stretching amount at the temperature of minus 40 ℃; has excellent ionic conductivity at low temperature, and can be applied to ionic conductors and energy storage devices.

Use of a zwitterionic polymer hydrogel electrolyte for a temperature responsive material. The application of the zwitterionic polymer hydrogel electrolyte as an energy storage device electrolyte. Use of a zwitterionic polymer hydrogel electrolyte for ionic conductors at low temperatures. Use of a zwitterionic polymer hydrogel electrolyte for a strain responsive material.

Advantageous effects

The invention relates to the preparation of hydrogel electrolytes of antifreeze polymers (polySH) by random copolymerization of zwitterionic monomers (SBMA) and 2-hydroxyethyl acrylate (HEA) in the presence of LiCl salts (FIG. 1 a). The one-pot method provides convenience for large-scale application of the hydrogel electrolyte. Throughout the system, the anionic and cationic groups on the zwitterionic chains facilitate the dissociation of the lithium metal salts and provide channels for ion migration. And the high-concentration LiCl greatly reduces the freezing point of the hydrogel polymer and ensures the excellent antifreezing property of the electrolyte. In the prior art, the conductivity and the freezing resistance are in a pair of contradiction, and the method for improving the freezing resistance usually reduces the conductivity; the method of the invention can simultaneously improve the frost resistance and the conductivity of the product, and breaks through the limitation of the prior art and the prejudice of the prior art.

The invention constructs an antifreeze hydrogel electrolyte (polySH) by simulating biological macromolecules and introducing zwitterions (such as methacryloyl ethyl sulfobetaine) into a polymer network. In fact, in addition to the antifreeze properties possessed by zwitterions, the electrostatic interaction between zwitterions and salt ions makes it possible for the salts in the system to become very readily dissociated, thereby increasing the number of free ions in the system. In addition, the zwitterion group can provide a migration channel for separated positive ions and negative ions under the action of an applied electric field, so that the conductivity is improved, and the zwitterion group has the concentration of 12.6mS cm at the temperature of-40 DEG C^-1High ionic conductivity. The polySH electrolyte can be stretched to 325% strain and compressed to 75% strain even at-40 ℃, which makes the polySH electrolyte have certain applications in the field of ion conductors and responsive materials.

Drawings

FIG. 1: (a) schematic diagram of polySH hydrogel electrolyte and its network structure.

FIG. 2: (a) DFT calculations of the interaction of different components in the polySH electrolyte. (b) MSD of salt ions in the polySH electrolyte.

FIG. 3: (a) ionic conductivity of polySH, polyHEA and PVA electrolytes. (b) Viscoelastic properties of polySH electrolytes of different LiCl contents. -SO in polySH electrolytes of different salt concentrations₃ ^-(c) and-N⁺(CH₃)₂(d) The raman spectrum of (a).

FIG. 4: (a) raman spectra of water in different polySH electrolytes. (b) DSC results for polySH electrolytes at different LiCl concentrations. (c) MSD of water in different polySH electrolytes. (d) The electrochemical stability windows of the various electrolytes were determined by the LSV method.

FIG. 5: (a) ionic conductivity of the polySH electrolyte at different temperatures.

FIG. 6: the tensile (a) and compressive (b) stress-strain curves of the polySH-7 electrolyte at different temperatures.

FIG. 7: (a) photograph of a polySH-7 electrolyte circuit connected to an LED lamp. (b) The electrical resistance of the polySH-7 electrolyte responds at different temperatures. (c) The electrical resistance response of the polySH-7 electrolyte at-40 ℃ for a continuous stretch release cycle.

FIG. 8: electrochemical performance of polySH supercapacitors at different temperatures: (a) the scanning rate is 100mV s^-1CV curve of time. (b) The current density was 1mA cm^-2GCD curve of time. (c) EIS spectra of the polySH-based supercapacitors at different temperatures. (d) Area specific capacitance of the polySH-based supercapacitor calculated from the GCD curve.

FIG. 9: the polySH-based supercapacitors lit small lamp photographs in a freeze-thaw state.

FIG. 10: (a) capacity retention of the polySH-based supercapacitor after 10 freeze-thaw cycles. (b) Capacity retention of the supercapacitor after 30 days of freezing at-30 ℃. (c) Cycling stability of the polySH-based supercapacitors after 10,000 cycles at different temperatures.

FIG. 11: (a) CV curve of polySH-based supercapacitors at 360 ° twist. (b) The capacitance of the supercapacitor remained the case after 500 twist cycles. (c) The super capacitor lights up a photograph of the LED lamp in the distorted state.

FIG. 12: CV curves of the polySH-based supercapacitor in the heavy-duty state (a) and the perforated state (b). (c) GCD curves of two supercapacitors in series and in parallel.

Detailed Description

Methacryloylethyl Sulfobetaine (SBMA), hydroxyethyl acrylate (HEA), azobisisobutyramidine hydrochloride (AIBA), lithium chloride (LiCl) were purchased from alatin. Polyvinyl alcohol 1799(PVA), polyvinylidene fluoride (PVDF), methyl pyrrolidone (NMP) were purchased from michelin. Carbon cloth is available from taiwan carbon energy company. Activated Carbon (AC) is commercially available from clony, japan. Carbon black is commercially available from alfa aesar.

Name interpretation:

SBMA: methacryloylethyl sulfobetaine;

HEA: hydroxyethyl acrylate;

poly SH: poly (SBMA-HEA) electrolyte;

polyHEA electrolyte: a poly (HEA) electrolyte;

AC: activated carbon;

PVDF: polyvinylidene fluoride;

AIBA: azodiisobutyamidine hydrochloride;

PVA electrolyte: polyvinyl alcohol 1799 electrolyte; PVA-1799 represents polyvinyl alcohol having a degree of polymerization of 1700 and a degree of alcoholysis of 99%.

APS: ammonium persulfate.

Electrochemical testing

The ionic conductivity was measured by Electrochemical Impedance Spectroscopy (EIS) using an electrochemical workstation (CHI 660E). The polySH electrolyte was first placed between two steel plates, then the electrolyte was stabilized at different temperatures for 5h, and then subjected to EIS testing. Three measurements were made for each sample to reduce errors. Ionic conductivity (σ, mS cm)^-1) The following formula is used to obtain:

here, R is the resistance (Ω), and S is the contact area (cm) of the electrolyte²) And L is the thickness (cm) of the test electrolyte.

The electrolyte linear voltammetry curve (LSV) is obtained by testing in a range of-1.2-1.3V by taking Ag/AgCl as a reference electrode. The electrochemical performance of the capacitor was measured on a CHI660E electrochemical workstation with a two-electrode system. Cyclic Voltammetry (CV) was obtained over different scan ranges in the voltage range 0-1V. Electrochemical Impedance Spectroscopy (EIS) was measured by 10mV in the range of 0.01Hz to 100 kHz. Charge-discharge cycles (GCD) were measured in the range of 0-1V using different current densities. Cycling stability 10000 cycles in GCD. Before testing, the super capacitor equipment is respectively placed at different temperatures and is stabilized for 5h_sp(mF cm^-2) The calculation formula is obtained by GCD calculation, and is as follows:

wherein I is applied current (m)A) Δ t is the discharge time (S), S_deviceIs the total area (cm) of the capacitor electrode²) And Δ V represents a discharge voltage (V).

Mechanical Property test

Tensile testing was performed using a universal testing instrument (Hensgrand, WDW-02, China). The electrolyte sample is a cylinder with a diameter of 5mm and a length of 40mm, and the strain rate is 100mm min^-1. The compression test adopts a cylindrical sample with the diameter of 10mm and the height of 15mm, the compression strain is 75 percent, and the compression speed is 10mm min^-1. All samples were stable at low temperature for 24 hours prior to low temperature testing.

The T-peel test was carried out at room temperature with a tensile speed of 100mm min-1 using a universal tester. One electrode of the supercapacitor was fixed, and the other electrode was peeled off to cover an area of 4mm × 65 mm.

Rheological measurements an ARES-G2 rheometer was used with parallel plates 25mm in diameter. First, using an angular frequency of 10rad s^-1Dynamic strain scanning in the range of 0.1-100% determines the linear viscoelastic region. Frequency sweep between 0.1-100rad s^-1Is carried out in the frequency range of (1%) with a constant strain.

Other characterizations

The Raman spectra were recorded using a LabRAM tHR800 Raman spectrometer (HORIBA JY, France) with a laser excitation wavelength of 532 nm. Differential scanning calorimetry (D-supercapacitor) using a TAQ-10D supercapacitor instrument at a temperature ranging from-80 deg.C to 50 deg.C and a heating rate of 10 deg.C for min^-1The mass of each sample is 5-10 mg.

Example 1

Preparation of PolySH hydrogel electrolyte

Zwitterionic polySH electrolytes were prepared using a one-pot random polymerization process using SBMA and HEA in the presence of LiCl salt. First, LiCl was dissolved in deionized water (8ml) to prepare 3mol L^-1In LiCl solution. Then 0.75g of SBMA and 1.25g of HEA (total mass 2g, molar ratio 1:4) were dissolved in 8ml of LiCl solution, the solution was stirred in an ice bath for 1 hour, then 0.02g of initiator AIBA (corresponding to 1% by weight of the total mass of the monomers) was added, and the mixture was placed inStir in ice bath for 1.5 h. After the solution is completely dissolved, the solution is subjected to ultrasonic treatment for 10min to remove bubbles, and then the precursor solution is injected into a mold, sealed and placed in an environment at 38 ℃ for polymerization for 12 h. The hydrogel obtained by polymerization is abbreviated as polySH-3, wherein 3 is the molar concentration of LiCl.

Assembled super capacitor

Preparing an activated carbon electrode: activated carbon AC, conductive carbon black and PVDF (mass ratio 8:1:1) were dispersed in NMP to prepare a uniform dispersion slurry. And coating the slurry on carbon cloth, putting the carbon cloth in a vacuum oven at 80 ℃ for 24h, and drying to obtain the AC electrode. The loading of active material on each electrode was about 2.5mg cm^-2.

Assembling the super capacitor: two AC electrodes with the same load area (0.5cm multiplied by 1.2cm) are taken and respectively covered on two sides of the electrolyte to form a sandwich structure to prepare the super capacitor. And then, one drop of the polySH electrolyte precursor solution is respectively dropped on the electrodes at both sides of the supercapacitor to wet the electrodes, thereby bonding the electrodes and the electrolyte more firmly. The total thickness of the prepared supercapacitor was about 1mm, and the thickness of the polySH electrolyte was 0.4 mm. The prepared capacitors were sealed with tape to prevent moisture evaporation prior to electrochemical testing.

Example 2

The procedure is otherwise the same as in example 1, except that the LiCl concentration in the hydrogel is varied. Zwitterionic polySH electrolytes were prepared using a one-pot random polymerization process using SBMA and HEA in the presence of LiCl salt. First, LiCl was dissolved in deionized water (8ml) to prepare 7mol L^-1In LiCl solution. Then 0.75g of SBMA and 1.25g of HEA (total mass 2g, molar ratio 1:4) were dissolved in 8ml of LiCl solution, the solution was stirred in an ice bath for 1h, then 0.02g of initiator AIBA (corresponding to 1% by weight of the total mass of the monomers) was added, followed by stirring in an ice bath for 1.5 h. After the solution is completely dissolved, the solution is subjected to ultrasonic treatment for 10min to remove bubbles, and then the precursor solution is injected into a mold, sealed and placed in an environment at 38 ℃ for polymerization for 12 h. The hydrogel obtained by polymerization is abbreviated as polySH-7, wherein 7 is the molar concentration of LiCl.

Different amounts of LiCl were dissolved in deionized water (8ml) to prepare 1-7mol L of different concentrations^-1The polymerized hydrogel is abbreviated as polySH-x, wherein x is the molar concentration of LiCl. .

Comparative examples 1 to 2

For comparison, we also prepared a polyHEA electrolyte and a PVA electrolyte, the preparation method being the same as in example 1. The polyHEA electrolyte is obtained by polymerization using only the HEA monomer, and the preparation method thereof is the same as the above-described preparation method of the polySH electrolyte. The polyHEA-based supercapacitor uses polyHEA as an electrolyte and is prepared in the same manner as a polySH electrolyte supercapacitor. The PVA-based supercapacitor uses PVA as an electrolyte and is prepared by the same method as a polySH electrolyte supercapacitor.

The PVA electrolyte was obtained by dissolving in a high temperature water bath 2g PVA in 8ml LiCl solution (1-7mol L)^-1) Then the mixture is placed in a water bath at 85 ℃ to be stirred, and a PVA electrolyte is obtained after the PVA is completely dissolved.

Analysis of results

As shown in FIG. 1, the anionic and cationic groups present on SBMA are simultaneously with Li⁺And Cl^-The binding site facilitates the dissociation of the lithium salt. To verify this hypothesis, Density Functional Theory (DFT) calculations were performed on the system. Figure 2a shows the optimal configuration of SBMA fragments using LiCl salt. Before addition of the lithium salt, the anions and cations on SBMA will interact with the cations and anions on other SBMAs due to electrostatic effects (ESBMA-SBMA: -4.025Kcal mol)^-1) An internal salt is formed to maintain the neutrality of the system. After addition of LiCl, the reaction mixture is reacted with-N⁺(CH₃)₂SO₃ ^-Comparison of-SO₃ ^-Li⁺The binding energy of (E) is lower (-18.15 Kcalamol)^-1) Description of-SO₃ ^-More prone to binding with Li + (fig. 2 a). Thus, the introduction of amphoteric groups does promote the dissociation of LiCl and is Li⁺Provides site support. The mechanism of ion transport in the polySH electrolyte was studied by molecular dynamics. It is generally believed that, for polymer electrolytes, Li⁺Can migrate hopping by successive complexation and dissociation with polar groups such as O, S, N on the polymer chain. As shown in FIG. 2b, in the polySH and polyHEA electrolytes, Li⁺And Cl^-Mean Square Displacement (MSD) of (a) is linear with time interval. In polySH electrolytes, Li⁺And Cl^-Is greater than the polyHEA electrolyte, indicating a faster rate of ion diffusion in the polySH electrolyte, which is facilitated by the presence of zwitterionic groups in SBMA, providing channels for ion migration. Taking SO into account₃ ^-And Li⁺Lower binding energy and Li⁺Faster diffusion rate, Li⁺Should be transported in SO₃ ^-The position of the group undergoes successive complexation and decomposition (FIG. 1 e). More importantly, Li⁺Can be reacted with H₂The O molecules combine to form Li⁺(H₂O)_nAnd (5) structure. Therefore, the migration of Li ions is also in conjunction with Li⁺(H₂O)_nThe solvating structure is relevant, which also contributes to the antifreeze properties of the polySH, which have been verified by Raman, Differential Scanning Calorimetry (DSC) and molecular modeling.

The ionic conductivity of the polySH electrolyte was determined at room temperature at various salt concentrations. For comparison, we also measured the conductivity of the polyHEA and the conventional PVA electrolyte, and the relevant data are shown in table 1. As shown in fig. 3a, at a certain salt concentration, the conductivity of the polySH electrolyte is higher than that of the polyHEA. As the salt concentration increases, the conductivity of the polySH electrolyte also increases. When the LiCl concentration reaches about 5mol L^-1When a threshold is observed, indicating anions and cations with Li⁺And Cl^-The binding of (c) is saturated. The conductivity of the polySH electrolyte is 146mS cm at room temperature^-1It is stated that the introduction of the amphoteric group is indeed Li⁺Provides a migration channel, greatly improves Li⁺The migration rate of (2). In addition, compared to conventional PVA electrolytes, the polySH electrolyte has higher conductivity, indicating that the polySH electrolyte has potential for application to energy storage devices.

TABLE 1 Ionic conductivities of polySH, polyHEA and PVA electrolytes

The addition of salts also changes the rheological properties of the polySH electrolyte. First at 10rad s^-1The linear viscoelastic region of the polySH electrolyte was measured in the range of 0.1 to 100% under strain. All subsequent viscoelasticity tests were performed at a strain of 1% to ensure the effectiveness of linear viscoelasticity and sufficient sensitivity. As shown in fig. 3b, the storage modulus G' of each polySH electrolyte is greater than the loss modulus G ", indicating that the electrolyte is primarily elastically deformed, exhibiting solid state behavior. As previously described, in the absence of LiCl, electrostatic interactions between anions and cations on the SBMA chains can increase the degree of crosslinking of the network to some extent, thereby giving the highest modulus to the polySH-0 hydrogel. The modulus of the polySH electrolyte gradually decreases as the salt concentration increases. The change in the mechanical modulus of the electrolyte indicates that LiCl disrupts the interaction between the cationic and anionic groups, reducing the crosslink density of the polymer network. To further understand the interaction of ionic groups on the polymer chains with salt ions, we performed raman spectroscopy studies on the polySH electrolyte. The S ═ O stretching vibration increased from 1044cm with the salt concentration increased from polysH-0 to polysH-7, -SO3-^-1Gradually changing to 1054cm^-1，-N⁺(CH₃)₂CH in (1)₃The stretching vibration is gradually changed from 2953cm-1 to 2957cm^-1(FIGS. 3c,3 d). The change in these peaks indicates that the electrostatic balance between the original anion and cation in the zwitterion is disrupted and a new electrostatic balance between the anion and cation occurs.

The added LiCl not only interacts with the polySH polymer chains but also influences the structure of the solvent water in the system. The most intuitive manifestation of this effect is the lowering of the freezing point of the electrolyte. As shown in FIG. 4a, Raman spectra show H at different LiCl concentrations₂The stretching vibration of O-H in O is changed. 3230cm^-1The peak at which hydrogen bonds between water molecules were present was gradually reduced, and accordingly, 3420cm^-1The asymmetric elastic band of (A) gradually increases with the increase of LiCl concentrationSharp and the corresponding peak is displaced by a certain amount. These changes indicate that the added LiCl breaks the hydrogen bonds between water molecules and reacts with H₂O forms a Li⁺(H₂O)_nA solvated structure. It is generally accepted that the water state in hydrophilic polymer hydrogels can be divided into at least two broad categories: non-freezable binding water and freezable water. Non-frozen water, which is produced due to the interaction of water with other components in the system, does not exhibit a phase change in calorimetric analysis. The DSC method can measure the relative content of water in different states, and provides a tool for quantitative analysis of the frozen state of the polySH electrolyte. As can be seen from FIG. 4b, in the absence of LiCl, polySH-0 has similar melting properties to pure water, with a melting peak near 0 ℃ indicating that a large amount of freezable water is contained in the polySH-0 hydrogel. After introduction of LiCl, the melting peak of water in the polySH electrolyte begins to shift towards sub-zero temperatures as the LiCl concentration increases. The calculation formula of the content of the freezable water in the polySH electrolyte is as follows:

in the formula, W_fIs the freezable water content, Δ H, in the electrolyte_mIs the enthalpy of fusion of freezable water in the electrolyte, obtained by integrating the DSC melting peak, Δ H_m0Is the melting enthalpy, Δ H, of pure water_m ⁰＝333.5J g^-1。W_H2OIs the relative content of water in the electrolyte, W_H2O＝m_H2O/m_total. The freezable water content of the polySH-0 hydrogel was calculated to be 80.5%. The freezable water content of the polySH-5 electrolyte gradually dropped to 8.2%. Interestingly, no melting peak was found in the thermogram of polySH-7, indicating that almost no freezable water was present in the polySH-7 electrolyte in the temperature range of-80 to 50 ℃. These data indicate that the higher the LiCl concentration, the lower the amount of freezable water in the electrolyte. In conclusion, the addition of LiCl does disrupt the freezing process of water, especially at high concentrations, and the effect on lowering the freezing point of the hydrogel electrolyte is more pronounced.

To further study Li⁺Interaction of H2O, we performed MSD simulations of several electrolytes at room temperature to understand the diffusion properties of water molecules. As shown in fig. 4c, MSD is linear with time interval. The slope of the curve decreases with increasing LiCl concentration, indicating that diffusion of water molecules is more limited at high LiCl concentrations. The diffusion coefficient of water molecules was calculated from MSD, and a high diffusion coefficient of 19.08X 10 of water molecules was observed due to the absence of LiCl in polySH-0^-5cm²s^-1. With increasing LiCl concentration, the water molecule diffusion coefficient of polySH-7 gradually decreases to 0.4X 10^-5cm²s^-1And is only 2.1% of polySH-0. Proves Li in the electrolyte⁺(H₂O)_nThe formation of a solvating structure and the reduction of the content of the freezable water enable the polySH electrolyte to have good antifreezing performance. The state of water in the polymer hydrogel is also reflected in the electrochemical stability window of the electrolyte. As shown in FIG. 4d, the electrochemical window of the polySH electrolyte measured by Linear Sweep Voltammetry (LSV) widened from 2.0V for polySH-0 to 2.2V for polySH-7 with increasing LiCl concentration. Li⁺And H₂The binding of the O molecule reduces the activity of the water molecule, thereby inhibiting the decomposition of the water molecule under high pressure.

The addition of LiCl greatly influences the water molecule and polymer structure in an electrolyte system, so that the polySH electrolyte has good frost resistance and high ionic conductivity at low temperature. Fig. 5 shows the trend of the change in conductivity of the polySH electrolyte at different temperatures. It can be seen that the curve is divided into two ranges: an above-zero temperature and a below-zero temperature. At above-zero temperatures, the conductivity of all electrolytes slowly decreases with decreasing temperature because all electrolytes are in a non-frozen state at this time. Within the subzero temperature range, the conductivity of the polySH-1 and polySH-3 electrolytes decreases faster, while the conductivity of the polySH-5 and polySH-7 electrolytes decreases less. In addition, in the temperature range below zero degree, the ion conductivity and the absolute temperature reciprocal are in a linear relation, and the conductivity of the electrolyte obeys the arrhenius law. The activation energy of each electrolyte in the subzero temperature range is calculatedAs the salt concentration increases, the activation energy of the electrolyte decreases. For example, the activation energy of polySH-1 is from 33.5kJ mol^-19.5kJ mol down to polySH-7^-1. The activation energy is an energy barrier that ion migration must overcome, and the smaller the activation energy, the easier ion migration. Thus, the conductivity of polySH-1 is from 0.11mS cm^-1Increased to 12.6mS cm^-1. The high-concentration LiCl improves the antifreezing property of the electrolyte, so that the low-temperature conductivity of the electrolyte can reach 12.6mS cm at the temperature of minus 40 DEG C^-1. More importantly, the polySH-7 electrolyte can still maintain good flexibility at-40 ℃. The polySH-7 electrolyte can be stretched to a strain of 325%, slightly above the strain at room temperature (FIG. 6 a). Meanwhile, the compressibility curve of the electrolyte was similar to that at room temperature when compressed to 75% strain (fig. 6b), indicating that the polySH-7 electrolyte maintained good mechanical properties and stability at low temperature. In conclusion, at the temperature of minus 40 ℃, the low-temperature conductivity of the electrolyte is 11-13 mS cm^-1. The electrolyte can be stretched to a strain of 300-350% at-40 ℃. The compressibility curve of the electrolyte when compressed to 75% strain is similar to that at room temperature.

The polySH electrolyte has good conductivity and flexibility at low temperature, so that the polySH electrolyte can be used as a low-temperature conductor. After connecting the polySH-7 to the LED lamp circuit, the LED lamp can be lit at a low temperature, with a brightness comparable to that at room temperature (fig. 7 a). polySH electrolytes may also be used as temperature responsive materials due to changes in conductivity at different temperatures. As shown in FIG. 7b, the polySH-7 electrolyte was sealed and placed at a temperature ranging from-40 ℃ to 40 ℃ and the change in resistance was recorded. We have found that the resistance of the polySH-7 electrolyte changes significantly when the temperature changes, and remains stable when the temperature remains constant. After completing one high-low temperature cycle, the resistance of the polySH-7 electrolyte can still be restored to the original state, and excellent resistance reversibility is shown. Unlike most reported strain sensors with operating temperatures above 0 ℃, the polySH-7 electrolyte can be released by stretching at-40 ℃ at a constant rate, with a corresponding uniform resistance change and with a good symmetry shape (fig. 7 c). The resistance change remains stable even over several consecutive stretch-release cycles, which is of great significance for low temperature strain sensor applications.

Our polySH electrolyte was also assembled into a solid supercapacitor, using activated carbon electrodes to evaluate electrochemical performance. The charged groups and polar groups in the zwitterions enable the electrolyte to be tightly combined with the electrodes, damage to the structure of the supercapacitor is reduced, and the electrochemical performance of the supercapacitor at low temperature is effectively improved. 100mV s in the range of-40 ℃ to 40 DEG C^-1The CV curve of (a) is shown in FIG. 8 a. At 60 ℃, the CV curve maintains a rectangular shape similar to room temperature. Due to the unique water-retaining property of the zwitterionic hydrogel, the super capacitor has good performance at high temperature. The CV curve shows a tendency to gradually deform as the temperature decreases. Furthermore, the GCD curve is in the shape of a regular inverted triangle with a small voltage drop (0.1V) only at-30 deg.C (FIG. 8 b). The EIS curves at different temperatures reflect the mobility of the ions. It can be seen that the EIS curve is almost parallel to the imaginary axis in the low frequency region, indicating that the polySH electrolyte has good ion diffusion behavior (fig. 8 c). At 25 c, the supercapacitor had a series resistance of 6.3 Ω, and this value increased to 12.2 Ω at-30 c and decreased to 5.9 Ω at 60 c. The change in temperature affects the diffusion rate of the electrolyte ions and thus the electrochemical performance of the supercapacitor. It is noteworthy that the supercapacitors also exhibited a small interfacial resistance, only 1.8 Ω at 25 ℃, indicating adequate contact between the electrodes and the electrolyte and a faster rate of charge transfer.

Area specific capacitance values at different current densities were calculated from the GCD curve (fig. 8 d). At 25 ℃, the specific capacitance of the super capacitor is 1mA cm^-2At a time of 171mF cm^-2At 5mA cm^-2At a time of 152mF cm^-2And the voltage is weakened by only 11%, thus the good multiplying power performance of the super capacitor is illustrated. When the temperature is increased to 60 ℃ or decreased to-30 ℃, the area specific capacitance is changed to 178mF cm^-2And 134mF cm^-2Approximately 104% and 78% at 25 ℃, indicating good electrochemical performance at extreme temperatures. As shown in fig. 9, an "QLU" type LED bulb (operating voltage 2.5V) can be illuminated in series by three super capacitors. After being frozen for 24 hours at low temperature, the super capacitor can still be positiveThe operation is normal. After the super capacitor is unfrozen, the brightness of the LED bulb is not obviously changed compared with the initial state. This indicates that low temperatures do not cause irreversible damage to the supercapacitor. To further confirm the antifreeze performance of the supercapacitor, the electrochemical performance of the supercapacitor was measured at 25 ℃ and-30 ℃ several times. As shown in fig. 10a, the specific capacitance can still be restored to the original level after thawing at room temperature. The capacitance of the supercapacitor was the same as at room temperature even after 10 freeze-thaw cycles (fig. 10 a). More importantly, when the supercapacitor is placed at a low temperature of-30 ℃ for more than 30 days, the capacitance of the supercapacitor only drops to 95.5% of the original capacitance (fig. 10 b). The cycling stability was tested at different temperatures. As shown in FIG. 10c, after 10000 cycles, the capacity retention of the supercapacitor at-30 ℃, 25 ℃ and 60 ℃ was 71%, 81% and 76.4%, respectively. This excellent cycling performance indicates that the polySH-based supercapacitor can operate at low and high temperatures for long periods of time.

The solid-state super capacitor has good flexibility besides anti-freezing performance, can avoid structural damage in practical application, and prolongs the service life. As shown in fig. 11a, the CV curve shows almost the same capacitance behavior as the initial state after twisting the polySH-based supercapacitor by 360 °. The capacity retention of the supercapacitor was 78.5% even after 500 twist cycles (fig. 11 b). After the super capacitor is connected into the circuit, the brightness of the LED lamp before and after the super capacitor is distorted does not change obviously (FIG. 11c), which shows that the electrochemical performance is not affected by large deformation. This is not only due to the flexibility of the entire supercapacitor, but also due to the good adhesion between the electrodes and the electrolyte, so that the supercapacitor can maintain structural integrity in the face of deformations. When loaded 4000 times its own weight, the capacitance of the polySH-based supercapacitor increases slightly, probably due to the shortened ion transport path in the electrolyte under high load (fig. 12 a). The good mechanical properties of the polySH electrolyte enable the supercapacitor to avoid short circuits during heavy loading. In addition, when our supercapacitor was punctured by sharps, the supercapacitor still worked properly and remained capacitively stable (fig. 12 b). In practical applications, higher voltages and higher energy densities can be achieved by connecting multiple supercapacitors in series and parallel. In our work, two supercapacitors in series showed a voltage window of 2.0V compared to a single supercapacitor, and when connected in parallel, the discharge time increased almost 2 times (fig. 12 c). Therefore, the antifreezing property and good mechanical strength of the polySH electrolyte expand the application field of the energy storage device.