Interface ion-electron conversion enhanced moisture power generation device and power generation apparatus

Abstract

This invention discloses a moisture-generating device and apparatus with enhanced interfacial ion-electron conversion. The moisture-generating device includes a first electrode layer, a first interface layer, a second interface layer, a moisture-generating layer, a third interface layer, a fourth interface layer, and a second electrode layer. The first interface layer is stacked on one side of the first electrode layer and includes a first electrochemically active material. The second interface layer is stacked on the side of the first interface layer away from the first electrode layer and includes a first redox couple. The moisture-generating layer is stacked on the side of the second interface layer away from the first interface layer. The third interface layer is stacked on the side of the moisture-generating layer away from the second interface layer and includes a second redox couple. The fourth interface layer is stacked on the side of the third interface layer away from the moisture-generating layer and includes a second electrochemically active material. The second electrode layer is stacked on the side of the fourth interface layer away from the third interface layer, and the second electrode layer has through-holes.

Description

Technical Field

[0001] This invention belongs to the field of functional materials technology, specifically relating to a moisture power generation device and power generation apparatus with enhanced interfacial ion-electron conversion. Background Technology

[0002] Energy is an indispensable element of social development. The large-scale use of fossil fuels has provided a guarantee for social development, but it has also caused the ongoing threats of energy crises and global warming. Therefore, developing sustainable green energy is one of the most pressing challenges facing social development. Water, as the largest energy carrier on Earth, absorbs one-third of the energy radiated from the sun for dynamic recycling. If only 1% of this energy were collected with a 1% energy conversion efficiency, it would be equivalent to the consumption of crude oil. Therefore, developing new energy conversion technologies using water as an energy source is extremely attractive.

[0003] Moisture-powered electricity generation utilizes the interaction between materials and water molecules to produce electricity. This novel green energy harvesting technology is of great significance for solving energy shortages and environmental pollution problems. However, to date, most research has focused on the functional layer of moist gas-powered devices, with research ideas centered on increasing the number of charge carriers within the functional layer and reducing carrier migration resistance. In reality, the ion-electron conversion process between the functional layer and the electrode materials is what truly inhibits the electrical output performance of moist gas-powered devices. To avoid chemical corrosion, inert materials are often used as current collectors in moist gas-powered devices; however, their extremely high interface voltage and impedance prevent ion current from being effectively converted into electron current, resulting in a significant energy loss in the process. Therefore, there is an urgent need to develop an interface that enhances ion-electron conversion and apply it to moist gas-powered devices to improve the electrical output performance of individual devices. Summary of the Invention

[0004] This invention aims to at least partially solve one of the technical problems in related technologies. Therefore, one object of this invention is to provide a moisture-generating device and apparatus with enhanced interface ion-electron conversion. This moisture-generating device exhibits high ion-electron conversion capability and efficiency at the interface, and realizes a new ion-electron conversion pathway at the interface, resulting in excellent electrical output performance.

[0005] In one aspect of the invention, a moisture-generating device with enhanced interfacial ion-electron conversion is provided. According to an embodiment of the invention, the moisture-generating device includes:

[0006] First electrode layer;

[0007] A first interface layer is stacked on one side of the first electrode layer, and the first interface layer includes a first electrochemical active material.

[0008] A second interface layer is stacked on the side of the first interface layer away from the first electrode layer, and the second interface layer includes a first redox couple.

[0009] A moisture-generating layer is stacked on the side of the second interface layer away from the first interface layer;

[0010] A third interface layer is stacked on the side of the moisture-generating layer away from the second interface layer, and the third interface layer includes a second redox couple.

[0011] A fourth interface layer is stacked on the side of the third interface layer away from the moisture-generating layer, and the fourth interface layer includes a second electrochemically active material.

[0012] The second electrode layer is stacked on the side of the fourth interface layer away from the third interface layer, and the second electrode layer has through holes.

[0013] The interface-enhanced ion-electron conversion humidity power generation device according to the above embodiments of the present invention includes a first electrode layer, a first interface layer, a second interface layer, a humidity power generation layer, a third interface layer, a fourth interface layer, and a second electrode layer. The first and second electrode layers primarily function to collect humidity for power generation output. The second electrode layer has through-holes. This asymmetrical geometric structure of the first and second electrode layers ensures that when the device is placed in a uniform humidity environment, moisture enters the device through the through-holes, forming a humidity gradient inside the device. Mobile ions are formed within the humidity power generation layer. Due to the intrinsic charge of the second electrochemical active material in the fourth interface layer, counterions are adsorbed onto the surface of the second electrochemical active material in the fourth interface layer, forming an electric double layer structure, causing a change in the potential of the second electrode layer. Simultaneously, the mobile ions within the humidity power generation layer migrate directionally under the influence of the humidity field, thereby inducing electron movement in the external circuit to shield the ion charge at the interface, further causing changes in the electrode potential. When moisture permeates the entire moisture-generating layer, due to the intrinsic charge of the first electrochemically active material in the first interface layer, counterions are adsorbed onto the surface of the first electrochemically active material in the first interface layer, forming an electric double layer structure, which causes a change in the potential of the first electrode layer. When the potential difference induced by the electric double layer structure on the first and fourth interface layers is in the same direction as the potential difference induced by the moisture-generating layer, the electrical output performance can be improved. The first electrochemically active material in the first interface layer and the second electrochemically active material in the fourth interface layer can increase the ion storage sites at the interface, greatly reducing the voltage and resistance at the interface between the moisture-generating layer and the first and second electrode layers, thereby promoting the ion-electron conversion at the interface.

[0014] The second interface layer includes a first redox couple, and the third interface layer includes a second redox couple. By introducing the first and second redox couples, electron transfer reactions occur between the second interface layer and the first electrode layer, and between the third interface layer and the second electrode layer, driven by changes in electrode potential induced by the moisture field. On one hand, charge can be stored in the first and second redox couples in this way, and then released to the external circuit during electrical output. On the other hand, it weakens the built-in electric field, promoting directional ion migration within the moisture-generating layer, thus storing more ions. The direction of electron transfer is determined by the electrochemical potential of each layer, from high electrochemical potential to low electrochemical potential. In the open-circuit state, due to the synergistic effect of the moisture field and the double-layer structure, the potential of the first electrode layer increases, and the potential of the second electrode layer decreases. When the potential of the first electrode layer is greater than the potential of the first redox couple, electrons will transfer from the first redox couple to the first electrode layer; when the potential of the second electrode layer is less than the potential of the second redox couple, electrons will transfer from the second electrode layer to the second redox couple. When short-circuited, because the combined potential of the first electrode layer and the first redox couple is higher than the combined potential of the second electrode layer and the second redox couple, electrons will transfer from the second redox couple to the second electrode layer, and further from the second electrode layer to the first electrode layer via the external circuit, and then from the first electrode layer to the first redox couple. Therefore, in both open-circuit and short-circuit conditions, the first redox couple and the first electrode layer, and the second redox couple and the second electrode layer, act as an "electron sponge" for electron storage and release, promoting both ion storage in the open-circuit state and electron release in the short-circuit state.

[0015] The wet gas power generation device improves the ion-electron conversion capability and efficiency at the interface by increasing ion storage sites at the interface between the first and second electrode layers through the first and fourth interface layers, respectively. Furthermore, the second and third interface layers establish a new ion-electron conversion pathway at the interface, weakening the built-in electric field and significantly enhancing the device's electrical output performance. Therefore, this wet gas power generation device exhibits high ion-electron conversion capability and efficiency at the interface and achieves excellent electrical output performance due to the new ion-electron conversion pathway implemented at the interface.

[0016] In addition, the interface ion-electron conversion enhanced wet gas power generation device according to the above embodiments of the present invention may also have the following additional technical features:

[0017] In some embodiments of the present invention, the first electrochemically active material and the second electrochemically active material each independently comprise at least one of the following: a carbon material exhibiting double-layer capacitance behavior, a metal oxide exhibiting pseudocapacitive behavior, a conductive polymer exhibiting pseudocapacitive behavior, a metal oxide exhibiting intercalation behavior, a metal chalcogenide exhibiting intercalation behavior, a metal-organic framework, and a covalent organic framework. This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0018] In some embodiments of the present invention, the moisture-generating layer comprises at least one of carbon materials, polyelectrolytes, metal oxides, metal sulfides, two-dimensional transition metal carbides, zeolites, metal-organic frameworks, covalent organic frameworks, plants, and microorganisms.

[0019] In some embodiments of the present invention, the carbon material exhibiting double-layer capacitance behavior includes at least one of porous activated carbon materials, ordered mesoporous carbon, carbide-derived carbon, ordered hierarchical mesoporous / microporous carbon, ordered mesoporous carbon nanofiber bundles, and heteroatom-doped carbon materials. This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0020] In some embodiments of the present invention, the metal oxide exhibiting pseudocapacitive behavior includes at least one of ruthenium-based materials, manganese-based materials, nickel-based materials, and cobalt-based materials. This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0021] In some embodiments of the present invention, the conductive polymer exhibiting pseudocapacitive behavior includes at least one of polyacetylene, polypyrrole, polyaniline, and poly(3,4-ethylenedioxythiophene). This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0022] In some embodiments of the present invention, at least one of the orthorhombic metal oxides Nb₂O₅ (T-Nb₂O₅) and Ni(OH)₂ with intercalation behavior is used. This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0023] In some embodiments of the present invention, the metal chalcogenides with intercalation behavior include at least one of MoS2, MoTe2, MoTe2, and ReS2. This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0024] In some embodiments of the present invention, the metal-organic framework includes at least one of ZIF-8, ZIF-67, MOF-74, MOF-808, and Prussian blue-like compounds. This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0025] In some embodiments of the present invention, the covalent organic framework includes at least one of COF-1, COF-5, ZnP-COF, CuP-COF, Py-Azine COF, and HPB-COF. This improves the ion-electron conversion capability and efficiency at the interface of the wet gas generator.

[0026] In some embodiments of the present invention, the first redox couple and the second redox couple each independently comprise at least one of a metal compound, a halide, and an aromatic compound. This improves the electrical output performance of the wet gas generator.

[0027] In some embodiments of the present invention, the metal compound includes Fe. 2+ / 3+ Cr 2+ / 3+ [Fe(CN)6] 3- / 4- [IrCl4] 2- / [IrCl4] 3- [Ru(bpy)3] 2+ / 3+ At least one of cobalt tri / dipyridyl and metal locene. This can improve the electrical output performance of the wet gas generator.

[0028] In some embodiments of the present invention, the halide includes I3. - / I - and Br2 / Br - At least one of them. This can improve the electrical output performance of the wet gas generator.

[0029] In some embodiments of the present invention, the aromatic compound includes at least one of thiaanthracene, thiaanthracene derivatives, phenazine, phenazine derivatives, phenthiazoline, phenthiazoline derivatives, quinoline, quinoline derivatives, phenol, phenol derivatives, 2,2,6,6-tetramethylpiperidin-1-yloxy derivatives, anthraquinone derivatives, anisole, and bi(di)anisole. This improves the electrical output performance of the wet gas generator.

[0030] In some embodiments of the present invention, the method for preparing the first interface layer includes: mixing the first electrochemical active material, the first conductive agent, the first binder and the first solvent and applying them to one side of the first electrode layer to obtain a non-self-supporting first interface layer.

[0031] In some embodiments of the present invention, the preparation method of the fourth interface layer includes: mixing the second electrochemical active material, the second conductive agent, the second binder and the second solvent and applying them to one side of the second electrode layer to obtain the non-self-supporting fourth interface layer.

[0032] In some embodiments of the present invention, the method for preparing the second interface layer includes: drying a solution containing a first host material and a first redox couple to obtain a self-supporting second interface layer.

[0033] In some embodiments of the present invention, the method for preparing the third interface layer includes: drying a solution containing a second host material and a second redox couple to obtain the self-supporting third interface layer.

[0034] In some embodiments of the present invention, the method for preparing the second interface layer includes: coating or electrochemically depositing a first redox couple on the side of the first interface layer away from the first electrode layer to form a non-self-supporting second interface layer.

[0035] In some embodiments of the present invention, the method for preparing the third interface layer includes: scraping or electrochemically depositing a second redox couple on the side of the fourth interface layer away from the second electrode layer to form the non-self-supporting third interface layer.

[0036] In some embodiments of the present invention, the mass ratio of the first electrochemical active material, the first conductive agent and the first binder is (7-9):(2-0.5):(1-0.5).

[0037] In some embodiments of the present invention, the mass ratio of the second electrochemical active material, the second conductive agent and the second binder is (7-9):(2-0.5):(1-0.5).

[0038] In some embodiments of the present invention, the mass percentage of the first redox couple is 0.005 wt% to 0.3 wt% based on the total mass of the self-supporting second interface layer. This improves the electron transport capability between the second interface layer and the first electrode layer.

[0039] Optionally, based on the total mass of the self-supporting third interface layer, the mass percentage of the second redox couple is 0.005 wt% to 0.3 wt%. This improves the electron transport capability between the third interface layer and the second electrode layer.

[0040] In some embodiments of the present invention, the first host material and the second host material each independently include at least one of carbon materials, polyelectrolytes, metal oxides, metal sulfides, two-dimensional transition metal carbides, zeolites, metal-organic frameworks, covalent organic frameworks, plants, and microorganisms.

[0041] In some embodiments of the present invention, the porosity of the through holes on the second electrode layer is 30% to 80%.

[0042] In some embodiments of the present invention, the thickness of the first interface layer is 5 μm to 100 μm. This increases the number of storage sites at the interface between the first interface layer and the first electrode layer, and reduces ion migration resistance.

[0043] In some embodiments of the present invention, the thickness of the fourth interface layer is 5 μm to 100 μm. This increases the number of storage sites at the interface between the fourth interface layer and the second electrode layer, and reduces ion migration resistance.

[0044] In some embodiments of the present invention, the thickness of the moisture-generating layer is 100 μm to 800 μm. This reduces ion migration resistance and improves the moisture-generating effect.

[0045] In some embodiments of the present invention, the thickness of the second interface layer is 50 μm to 400 μm. This reduces ion migration resistance and improves the electrical output performance of the device.

[0046] In some embodiments of the present invention, the thickness of the third interface layer is 50 μm to 400 μm. This reduces ion migration resistance and improves the electrical output performance of the device.

[0047] In some embodiments of the present invention, the thickness ratio of the second interface layer, the moisture-generating layer, and the third interface layer is 1:(1-2):1. This reduces ion migration resistance and improves the electrical output performance of the device.

[0048] In some embodiments of the present invention, the power generation device outputs electrical energy for a long time in a quasi-continuous manner. The quasi-continuous electrical output is performed at a frequency xy, where x represents the discharge time (1s≤x≤20min), y represents the self-recovery time (1s≤y≤20min), and x:y is 1:(1200~10).

[0049] In a second aspect, the present invention provides a power generation device. According to an embodiment of the invention, the power generation device includes the aforementioned interface ion-electron conversion enhanced moisture power generation device. Therefore, the power generation device exhibits excellent and stable electrical output performance.

[0050] Additional aspects and advantages of the invention will be set forth in part in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. Attached Figure Description

[0051] The above and / or additional aspects and advantages of the present invention will become apparent and readily understood from the description of the embodiments taken in conjunction with the following drawings, in which:

[0052] Figure 1This is a schematic diagram of the structure of a moisture generator with enhanced interface ion-electron conversion according to an embodiment of the present invention;

[0053] Figure 2 This is a top view of the second electrode layer according to another embodiment of the present invention;

[0054] Figure 3 This is a scanning electron microscope image of the MnO2 electrode in Embodiment 1 of the present invention;

[0055] Figure 4 This is the X-ray diffraction pattern of the MnO2 nanoparticles in Example 1 of this invention;

[0056] Figure 5 This is a scanning electron microscope image of the MoS2 electrode in Embodiment 1 of the present invention;

[0057] Figure 6 This is the X-ray diffraction pattern of the MoS2 nanosheets in Example 1 of this invention;

[0058] Figure 7 These are scanning electron microscope images and energy-dispersive X-ray images of the H-PSS thin film of Embodiment 1 of the present invention;

[0059] Figure 8 These are scanning electron microscope images and energy-dispersive X-ray diffraction images of the H-PSS / I thin film of Embodiment 1 of the present invention;

[0060] Figure 9 These are scanning electron microscope images and energy-dispersive X-ray diffraction images of the H-PSS / Fe thin film of Embodiment 1 of the present invention;

[0061] Figure 10 This is the X-ray photoelectron fine energy spectrum of C1s and O1s of Super P in Embodiment 1 of the present invention;

[0062] Figure 11 This is the X-ray photoelectron fine spectrum of Mn 2p and O1s of the MnO2 electrode in Embodiment 1 of the present invention;

[0063] Figure 12 This is the X-ray photoelectron fine spectrum of Mo 3d and S2p of the MoS2 electrode in Embodiment 1 of the present invention;

[0064] Figure 13 This is a solid surface zeta potential diagram of the MnO2 electrode and MoS2 electrode in Embodiment 1 of the present invention;

[0065] Figure 14 This is a schematic diagram of the electric double layer structure of the MnO2 electrode and MoS2 electrode on the H-PSS thin film in Embodiment 1 of the present invention.

[0066] Figure 15This refers to the changes in electrode potential and the potential difference between the MnO2 electrode and MoS2 electrode in different solutions in Embodiment 1 of the present invention.

[0067] Figure 16 The MnO2 electrode and MoS2 electrode of Embodiment 1 of the present invention are electrode potential-time curves in a humid power generation device and placed in a humid field.

[0068] Figure 17 This is the cyclic voltammetry curve of the working electrode of Embodiment 1 of the present invention, which is a glassy carbon electrode, in H-PSS / I solution and H-PSS / Fe solution;

[0069] Figure 18 These are schematic diagrams of ion migration and electron transfer at the interface and changes in electrode potential at the device of Embodiment 1 of the present invention during open circuit and short circuit processes;

[0070] Figure 19 These are the voltage-time curves and current-time curves of the device in Embodiment 1 of the present invention;

[0071] Figure 20 This is the power density curve of the device in Embodiment 1 of the present invention;

[0072] Figure 21 This is the X-ray photoelectron fine energy spectrum of Mn 2p and O1s of the MnO2 electrode in Embodiment 1 of the present invention after quasi-continuous output and no output;

[0073] Figure 22 This is the fine X-ray photoelectron spectrum of Mo 3d and S2p of the MoS2 electrode in Embodiment 1 of the present invention after quasi-continuous output and no output.

[0074] Figure 23 This refers to the H-PSS / I solution of Example 1 of the present invention and its UV-Vis absorption spectrum during the quasi-continuous output process;

[0075] Figure 24 This refers to the H-PSS / Fe solution of Example 1 of the present invention and its UV-Vis absorption spectrum during the quasi-continuous output process;

[0076] Figure 25 These are the UV-Vis absorption spectra of the H-PSS / I solution and H-PSS / Fe solution in Example 1 of this invention during the non-output process;

[0077] Figure 26 I3 is the aqueous control battery in Example 1 of this invention. - / I - The ultraviolet-visible absorption spectrum during continuous output;

[0078] Figure 27The aqueous control battery of Embodiment 1 of this invention contains [Fe(CN)6]. 3- / 4- The ultraviolet-visible absorption spectrum during continuous output;

[0079] Figure 28 The areal capacitance of the perforated graphite foil, perforated MoS2 electrode, graphite foil and MnO2 electrode in Embodiment 1 of the present invention.

[0080] Figure 29 This refers to the change in electrode potential of the MoS2 electrode and MnO2 electrode in Embodiment 1 of the present invention during discharge and self-charging.

[0081] Figure 30 The device of Embodiment 1 of this invention operates at 100 μA cm⁻¹. -2 The self-recovery process of open-circuit voltage under discharge current density;

[0082] Figure 31 This describes the relationship between the voltage retention rate and current retention rate of the device in Embodiment 1 of the present invention after dehydration and rehydration, and the number of cycles.

[0083] Figure 32 These are the voltage and current of the device in Embodiment 1 of the present invention under different bending angles;

[0084] Figure 33 These are the series voltage-series quantity curves and parallel current-parallel quantity curves of the device in Embodiment 1 of the present invention;

[0085] Figure 34 This is the voltage-time curve of a 4×2 array charging a 4F capacitor during the device assembly process of Embodiment 1 of the present invention;

[0086] Figure 35 This describes the relationship between device voltage, current, 12-hour accumulated charge, and relative humidity in Embodiment 2 of the present invention.

[0087] Figure 36 The power and cumulative output energy ∫I of the device in Embodiment 3 of the present invention at different self-charging times are shown. 2 dt;

[0088] Figure 37 The voltage retention rate, current retention rate, 12-hour accumulated charge, and output energy ∫I of the device in Embodiment 4 of the present invention under different discharge times are shown. 2 dt;

[0089] Figure 38 The output energy ∫I of the device in Embodiment 5 of the present invention under different H-PSS / I thin film thicknesses and H-PSS / Fe thin film thicknesses is... 2 dt - Time curve, voltage and current;

[0090] Figure 39 The output energy ∫I of the device in Embodiment 6 of the present invention under different H-PSS thin film thicknesses is... 2 dt - Time curve, voltage and current;

[0091] Figure 40 These are the voltage and current of the device in Embodiment 7 of the present invention under different redox couple contents;

[0092] Figure 41 These are the area-to-capacitance-frequency curves of the device in Embodiment 8 of the present invention with different MoS2 electrode thicknesses;

[0093] Figure 42 The voltage, current, 12-hour cumulative output charge, and energy ∫I of the device in Embodiment 8 of the present invention under different MoS2 electrode thicknesses are shown. 2 dt;

[0094] Figure 43 These are the voltages and currents of the device in Embodiment 9 of the present invention under different areas;

[0095] Figure 44 These are the voltage and current of the device in Embodiment 10 of the present invention;

[0096] Figure 45 These are the energy-time curves (with a load of 47Ω) and charge-time curves of the device in Comparative Example 1 of this invention during quasi-continuous output and continuous output.

[0097] Figure 46 The devices of Comparative Example 2 of this invention—MnO2 electrode and MoS2 electrode—have voltage-time curves and current-time curves with different interface layers and moisture-generating layers.

[0098] Figure 47 The cumulative charge of the devices in Comparative Example 2 of this invention—MnO2 electrode and MoS2 electrode—with different interface layers and moisture-generating layers over 12 hours;

[0099] Figure 48 These are the voltage-time curves and 12-hour cumulative charge of the device in Comparative Example 3 of this invention under different directional humid air fields;

[0100] Figure 49 The voltage-time curve, current-time curve, charge-time curve, and energy ∫I of the device in Comparative Example 4 of this invention are shown below. 2 dt-time curve;

[0101] Figure 50 The current, 12-hour accumulated charge, and 12-hour accumulated energy ∫I of the devices in Embodiment 1 and Comparative Example 5 of this invention are... 2 dt. Detailed Implementation

[0102] The embodiments of the present invention are described in detail below, and are intended to explain the present invention, but should not be construed as limiting the present invention.

[0103] In one aspect of the invention, a moisture-generating device with enhanced interfacial ion-electron conversion is proposed. According to an embodiment of the invention, reference is made to... Figure 1 The moisture-generating device includes: a first electrode layer 100, a first interface layer 200, a second interface layer 300, a moisture-generating layer 400, a third interface layer 500, a fourth interface layer 600, and a second electrode layer 700.

[0104] According to an embodiment of the present invention, reference Figure 2 The second electrode layer 700 has through holes 710. The first electrode layer 100 and the second electrode layer 700 mainly function to collect moisture for power generation. The asymmetrical geometry of the first electrode layer 100 and the second electrode layer 700 ensures that when the device is placed in a uniform humid environment, moisture will enter the device through the through holes 710 of the second electrode layer 710, forming a moisture gradient inside the device. Furthermore, the porosity of the through holes 710 on the second electrode layer 700 is 30% to 80%, thereby achieving effective moisture penetration and maintaining a high effective area of ​​the second electrode layer 700. It should be noted that this application does not particularly limit the shape and size of the through holes 710; as long as they are within a reasonable range, those skilled in the art can choose them according to actual needs.

[0105] Those skilled in the art will understand that the first electrode layer 100 and the second electrode layer 700 should have good electrical conductivity and good chemical inertness, and be resistant to corrosion by air. For example, the materials of the first electrode layer 100 and the second electrode layer 700 can independently include carbon materials and noble metals, respectively. Carbon materials and noble metals are conventional materials in the art, and those skilled in the art can select them according to actual needs. For example, carbon materials include, but are not limited to, graphite, activated carbon, and carbon nanotubes; noble metals include, but are not limited to, gold, silver, and platinum group metals, such as ruthenium, rhodium, palladium, osmium, iridium, and platinum.

[0106] According to an embodiment of the present invention, reference Figure 1A first interface layer 200 is stacked on one side of the first electrode layer 100, and the first interface layer 200 includes a first electrochemically active material; a fourth interface layer 600 is stacked on one side of the second electrode layer 700, and the fourth interface layer 600 includes a second electrochemically active material. Due to the intrinsic charge of the second electrochemically active material in the fourth interface layer 600, counterions are adsorbed on the surface of the second electrochemically active material in the fourth interface layer 600, forming a double-layer structure, causing a change in the potential of the second electrode layer 700. Simultaneously, mobile ions within the moisture-generating layer 400 migrate directionally under the influence of the moisture field, thereby inducing electron movement in the external circuit to shield the ionic charge at the interface, further causing a change in the electrode potential. When moisture permeates the entire moisture-generating layer 400, due to the intrinsic charge of the first electrochemically active material in the first interface layer 200, counterions are adsorbed on the surface of the first electrochemically active material in the first interface layer 200, forming a double-layer structure, causing a change in the potential of the first electrode layer 100. When the potential difference induced by the double-layer structure on the first interface layer 200 and the fourth interface layer 600 is in the same direction as the potential difference induced by the wet gas power generation layer, the electrical output performance can be improved. The first electrochemically active material of the first interface layer 200 and the second electrochemically active material of the fourth interface layer 600 can increase the ion storage sites at the interface, greatly reducing the voltage and resistance at the interface between the wet gas power generation layer 400 and the first electrode layer 100 and the second electrode layer 700, thereby promoting the ion-electron conversion at the interface. The first interface layer 200 and the fourth interface layer 700 have good conductivity and ion storage capacity.

[0107] According to embodiments of the present invention, the first electrochemically active material and the second electrochemically active material each independently comprise at least one of the following: a carbon material exhibiting double-layer capacitance behavior, a metal oxide exhibiting pseudocapacitive behavior, a conductive polymer exhibiting pseudocapacitive behavior, a metal oxide exhibiting intercalation behavior, a metal chalcogenide exhibiting intercalation behavior, a metal-organic framework, and a covalent organic framework, thereby improving the ion-electron conversion capability and efficiency at the interface of the wet gas generator. Further, the carbon material exhibiting double-layer capacitance behavior comprises at least one of the following: porous activated carbon material, ordered mesoporous carbon, carbide-derived carbon, ordered hierarchical mesoporous / microporous carbon, ordered mesoporous carbon nanofiber bundles, and heteroatom-doped carbon material; the metal oxide exhibiting pseudocapacitive behavior comprises at least one of the following: ruthenium-based material, manganese-based material, nickel-based material, and cobalt-based material; the conductive polymer exhibiting pseudocapacitive behavior comprises at least one of the following: polyacetylene, polypyrrole, polyaniline, and poly(3,4-ethylenedioxythiophene); the metal oxide exhibiting intercalation behavior comprises at least one of the following: At least one of the orthorhombic metal oxides Nb₂O₅ (T-Nb₂O₅) and Ni(OH)₂; at least one of the metal chalcogenides with intercalation behavior, including MoS₂, MoTe₂, MoTe₂ and ReS₂; at least one of the metal-organic frameworks, including ZIF-8, ZIF-67, MOF-74, MOF-808 and Prussian blue-like frameworks; and at least one of the covalent organic frameworks, including COF-1, COF-5, ZnP-COF, CuP-COF, Py-Azine COF and HPB-COF.

[0108] According to an embodiment of the present invention, the thickness of the first interface layer 200 is 5 μm to 100 μm. The inventors have found that a thickness of 5 μm to 100 μm for the first interface layer 200 can, on the one hand, increase the number of storage sites at the interface between the first interface layer and the first electrode layer, and on the other hand, reduce ion migration resistance, which is beneficial to improving device performance.

[0109] According to an embodiment of the present invention, the thickness of the fourth interface layer 600 is 5 μm to 100 μm. The inventors have found that a thickness of 5 μm to 100 μm for the fourth interface layer 600 can, on the one hand, increase the storage sites at the interface between the fourth interface layer 600 and the second electrode layer 700, and on the other hand, reduce ion migration resistance, which is beneficial to improving device performance.

[0110] According to an embodiment of the present invention, the preparation method of the first interface layer 200 includes: mixing a first electrochemically active material, a first conductive agent, a first binder, and a first solvent and applying the mixture to one side of the first electrode layer 100, followed by drying, thereby obtaining a non-self-supporting first interface layer 200. Further, the first conductive agent includes porous carbon black, carbon nanotubes, or graphene; the first binder includes polyvinylidene fluoride (PVDF), carboxymethyl cellulose (CMC), or styrene-butadiene rubber (SBR) emulsion. It should be noted that the first solvent is a conventional reagent in the art, and those skilled in the art can select it according to actual needs; for example, the first solvent may include N-methylpyrrolidone.

[0111] According to an embodiment of the present invention, the mass ratio of the first electrochemically active material, the first conductive agent, and the first binder is (7-9):(2-0.5):(1-0.5). The inventors have discovered that when the mass ratio of the first electrochemically active material, the first conductive agent, and the first binder is within the above range, the electronic conductivity of the interface layer and the adhesion to the first electrode layer can be improved while ensuring the function of the electrochemically active material.

[0112] According to an embodiment of the present invention, the preparation method of the fourth interface layer 600 includes: mixing a second electrochemically active material, a second conductive agent, a second binder, and a second solvent and applying the mixture to one side of the second electrode layer 700, followed by drying, thereby obtaining a non-self-supporting fourth interface layer 600. Further, the second conductive agent includes porous carbon black, carbon nanotubes, or graphene; the second binder includes polyvinylidene fluoride (PVDF), carboxymethyl cellulose (CMC), or styrene-butadiene rubber (SBR) emulsion. It should be noted that the second solvent is a conventional reagent in the art, and those skilled in the art can select it according to actual needs; for example, the second solvent may include N-methylpyrrolidone.

[0113] According to an embodiment of the present invention, the mass ratio of the second electrochemically active material, the second conductive agent, and the second binder is (7-9):(2-0.5):(1-0.5). The inventors have found that when the mass ratio of the second electrochemically active material, the second conductive agent, and the second binder is within the above range, the electronic conductivity of the interface layer and the adhesion of the second electrode layer can be improved while ensuring the function of the electrochemically active material.

[0114] According to an embodiment of the present invention, a moisture-generating layer 400 is stacked on the side of the second interface layer 300 away from the first interface layer 200. Movable ions are formed within the moisture-generating layer 400, which should have good water absorption and, upon absorbing water, form freely moving charge carriers of the same charge. The main material of the moisture-generating layer 400 includes at least one of carbon materials, polyelectrolytes, metal oxides, metal sulfides, two-dimensional transition metal carbides, zeolites, metal-organic frameworks, covalent organic frameworks, plants, and microorganisms. Further, carbon materials include carbon nanotubes, graphene oxide, carbon black, and porous carbon nanofibers; polyelectrolytes include polyvinyl alcohol, perfluorosulfonic acid, sodium alginate, hydroxyethyl cellulose, and dopamine; and metal oxides include TiO2, SiO2, Al2O3, and Pd. x O y And WO3, etc.; metal sulfides include MoS2, WS2, MoSe2, WSe2, MoTe2 and WTe2, etc.; two-dimensional transition metal carbides include titanium carbide (Ti3C2T). x The following are examples of organic compounds: molybdenum carbide, vanadium carbide, and niobium carbide; zeolites include zeolite, sodium zeolite, chalcogenide, analcime, zeolite, flaking zeolite, mordenite, and clinoptilolite; metal-organic frameworks include at least one of ZIF-8, ZIF-11, Ni3(BTP)2, Zn3(BTP)2, KAUST-8, KAUST-9, MOF-801, and MOF-303; covalent organic frameworks include at least one of triazine COFs and imine COFs; plants include wood, corn stalks, and coconut shells; and microorganisms include sulfur-reducing bacteria, whey protein, and lactoglobulin.

[0115] According to an embodiment of the present invention, the thickness of the moisture-generating layer 400 is 100 μm to 800 μm. The inventors have discovered that when the thickness of the moisture-generating layer 400 is 100 μm to 800 μm, a sufficient number of freely moving charge carriers of the same charge can be formed, and the ion migration resistance within the layer is effectively reduced.

[0116] According to embodiments of the present invention, methods for preparing the self-supporting first interface layer 200 include hydrothermal methods, freeze-drying methods, ionic cross-linking methods, and filtration methods. For example, self-supporting porous graphene foam can be obtained by directly freeze-drying a graphene solution. Further, methods for preparing the self-supporting fourth interface layer 600 include hydrothermal methods, freeze-drying methods, ionic cross-linking methods, and filtration methods.

[0117] According to an embodiment of the present invention, reference Figure 1A second interface layer 300 is stacked on the side of the first interface layer 200 away from the first electrode layer 100, and the second interface layer 300 includes a first redox couple. A third interface layer 500 is stacked on the side of the humidification layer 400 away from the second interface layer 300, and the third interface layer 500 includes a second redox couple. By introducing the first and second redox couples, electron transfer reactions occur between the second interface layer 300 and the first electrode layer 100, and between the third interface layer 500 and the second electrode layer 700, driven by changes in electrode potential induced by the humidification field. On the one hand, charge can be stored in the first and second redox couples in this way, and then released to the external circuit during electrical output. On the other hand, the built-in electric field can be weakened, promoting directional ion migration within the humidification layer 400, thus achieving the storage of more ions. The direction of electron transfer is determined by the electrochemical potential of each layer, from high electrochemical potential to low electrochemical potential. In the open-circuit state, due to the synergistic effect of the humid environment and the double-layer structure, the potential of the first electrode layer 100 increases, while the potential of the second electrode layer 700 decreases. When the potential of the first electrode layer 100 is greater than the potential of the first redox couple, electrons will transfer from the first redox couple to the first electrode layer 100. When the potential of the second electrode layer 700 is less than the potential of the second redox couple, electrons will transfer from the second electrode layer 700 to the second redox couple. In the short-circuit state, since the combined potential of the first electrode layer 100 and the first redox couple is higher than the combined potential of the second electrode layer 700 and the second redox couple, electrons will transfer from the second redox couple to the second electrode layer 700, further transfer from the second electrode layer 700 to the first electrode layer 100 via the external circuit, and then transfer from the first electrode layer 100 to the first redox couple. Therefore, in open circuit and short circuit conditions, the first redox couple and the first electrode layer 100, and the second redox couple and the second electrode layer 700, store and release electrons in the form of an "electron sponge," which promotes the storage of ions in the open circuit state and the release of electrons in the short circuit state.

[0118] According to embodiments of the present invention, the first redox couple and the second redox couple each independently comprise at least one of a metal compound, a halide, and an aromatic compound. Further, the metal compound includes Fe. 2+ / 3+ Cr 2+ / 3+ [Fe(CN)6] 3- / 4- [IrCl4] 2- / [IrCl4] 3- [Ru(bpy)3] 2+ / 3+ At least one of tri / dipyridyl cobalt and metallocene; halides including I3- / I - and Br2 / Br - At least one of the following: aromatic compounds include at least one of thiaanthracene, thiaanthracene derivatives, phenazine, phenazine derivatives, phenthia, phenthia derivatives, quinoline, quinoline derivatives, phenol, phenol derivatives, 2,2,6,6-tetramethylpiperidin-1-yloxy derivatives, anthraquinone derivatives, anisole and bi(bi)anisole.

[0119] According to an embodiment of the present invention, the thickness of the second interface layer 300 is 50 μm to 400 μm. The inventors have found that a thickness of 50 μm to 400 μm for the second interface layer 300 ensures a high content of the first redox couple within the second interface layer, and that the first redox couple and the electrode layer can effectively perform electron transfer, while simultaneously reducing the resistance to ion migration within the membrane. Furthermore, the thickness of the third interface layer 500 is 50 μm to 400 μm, thereby ensuring a high content of the second redox couple within the third interface layer, and that the second redox couple and the electrode layer can effectively perform electron transfer, while simultaneously reducing the resistance to ion migration within the membrane.

[0120] According to an embodiment of the present invention, the thickness ratio of the second interface layer 300, the moisture-generating layer 400, and the third interface layer 500 is 1:(1-2):1. The inventors have found that when the thickness ratio of the second interface layer 300, the moisture-generating layer 400, and the third interface layer 500 is within the above range, it can ensure that the potential change induced by the moisture field is sufficient to drive the effective electron transfer between the redox couple and the electrodes.

[0121] According to an embodiment of the present invention, the preparation method of the second interface layer 300 includes: drying a solution containing a first host material and a first redox couple to obtain a self-supporting second interface layer 300. According to an embodiment of the present invention, the first host material includes carbon materials, polyelectrolytes, metal oxides, metal sulfides, two-dimensional transition metal carbides, zeolites, metal-organic frameworks, covalent organic frameworks, plants, and microorganisms, etc. Further, carbon materials include carbon nanotubes, graphene oxide, carbon black, and porous carbon nanofibers, etc.; polyelectrolytes include polyvinyl alcohol, perfluorosulfonic acid, sodium alginate, hydroxyethyl cellulose, and dopamine, etc.; metal oxides include TiO2, SiO2, Al2O3, Pd, etc. x O y And WO3, etc.; metal sulfides include MoS2, WS2, MoSe2, WSe2, MoTe2 and WTe2, etc.; two-dimensional transition metal carbides include titanium carbide (Ti3C2T). xThe following are examples of organic compounds: molybdenum carbide, vanadium carbide, and niobium carbide; zeolites include zeolite, sodium zeolite, chalcogenide, analcime, zeolite, flaking zeolite, mordenite, and clinoptilolite; metal-organic frameworks include at least one of ZIF-8, ZIF-11, Ni3(BTP)2, Zn3(BTP)2, KAUST-8, KAUST-9, MOF-801, and MOF-303; covalent organic frameworks include at least one of triazine COFs and imine COFs; plants include wood, corn stalks, and coconut shells; and microorganisms include sulfur-reducing bacteria, whey protein, and lactoglobulin.

[0122] According to an embodiment of the present invention, based on the total mass of the self-supporting second interface layer 300, the mass percentage of the first redox couple is 0.005 wt% to 0.3 wt%. The inventors have found that having the mass percentage of the first redox couple within the above range can improve the electron transport capability between the second interface layer 300 and the first electrode layer 100, and ensure a more uniform distribution of the first redox couple within the second interface layer 300.

[0123] According to an embodiment of the present invention, the preparation method of the third interface layer 500 includes: drying a solution containing a second host material and a second redox couple to obtain a self-supporting third interface layer 500. According to an embodiment of the present invention, the second host material includes carbon materials, polyelectrolytes, metal oxides, metal sulfides, two-dimensional transition metal carbides, zeolites, metal-organic frameworks, covalent organic frameworks, plants, and microorganisms, etc. Further, carbon materials include carbon nanotubes, graphene oxide, carbon black, and porous carbon nanofibers, etc.; polyelectrolytes include polyvinyl alcohol, perfluorosulfonic acid, sodium alginate, hydroxyethyl cellulose, and dopamine, etc.; metal oxides include TiO2, SiO2, Al2O3, Pd, etc. x O y And WO3, etc.; metal sulfides include MoS2, WS2, MoSe2, WSe2, MoTe2 and WTe2, etc.; two-dimensional transition metal carbides include titanium carbide (Ti3C2T). x The following are examples of organic compounds: molybdenum carbide, vanadium carbide, and niobium carbide; zeolites include zeolite, sodium zeolite, chalcogenide, analcime, zeolite, flaking zeolite, mordenite, and clinoptilolite; metal-organic frameworks include at least one of ZIF-8, ZIF-11, Ni3(BTP)2, Zn3(BTP)2, KAUST-8, KAUST-9, MOF-801, and MOF-303; covalent organic frameworks include at least one of triazine COFs and imine COFs; plants include wood, corn stalks, and coconut shells; and microorganisms include sulfur-reducing bacteria, whey protein, and lactoglobulin.

[0124] According to an embodiment of the present invention, based on the total mass of the self-supporting third interface layer 500, the mass percentage of the second redox couple is 0.005 wt% to 0.3 wt%. The inventors have found that when the mass percentage of the second redox couple is within the above range, the electron transport capability between the third interface layer 500 and the second electrode layer 700 can be improved, and the distribution of the second redox couple within the third interface layer 500 can be made more uniform.

[0125] According to an embodiment of the present invention, the method for preparing the second interface layer 300 includes: coating or electrochemically depositing a first redox couple on the side of the first interface layer 200 away from the first electrode layer 100, thereby forming a non-self-supporting second interface layer 300. Further, the method for preparing the third interface layer 500 includes: coating or electrochemically depositing a second redox couple on the side of the fourth interface layer 400 away from the second electrode layer 700, thereby forming a non-self-supporting third interface layer 500.

[0126] According to an embodiment of the present invention, the moisture-generating device further includes an encapsulation layer (not shown). Except for the through-holes 710 on the surface of the second electrode layer 700, the encapsulation layer covers the first electrode layer 100, the first interface layer 200, the second interface layer 300, the moisture-generating layer 400, the third interface layer 500, the fourth interface layer 600, and the second electrode layer 700. The unencapsulated through-holes 710 allow moisture to enter the device.

[0127] This moisture-generating device, on the one hand, increases the ion storage sites at the interface between the first electrode layer 100 and the second electrode layer 700 through the first interface layer 200 and the fourth interface layer 600, respectively, thereby improving the ion-electron conversion capability and efficiency at the interface; on the other hand, it achieves a new ion-electron conversion pathway at the interface through the second interface layer 300 and the third interface layer 500, weakening the built-in electric field and significantly improving the device's electrical output performance. Therefore, this moisture-generating device exhibits high ion-electron conversion capability and efficiency at the interface, and achieves a new ion-electron conversion pathway at the interface, resulting in excellent electrical output performance.

[0128] According to an embodiment of the present invention, the power generation device outputs electrical energy in a quasi-continuous manner for a long period of time. That is, after outputting electrical energy for a certain period, it can switch to open-circuit mode, where the device self-recovers to its initial voltage in a humid environment before starting the next cycle of electrical energy output. The quasi-continuous electrical output is performed at a frequency xy, where x represents the discharge time (1s ≤ x ≤ 20min), y represents the self-recovery time (1s ≤ y ≤ 20min), and x:y is 1:(1~120).

[0129] In a second aspect, the present invention provides a power generation device. According to an embodiment of the invention, the power generation device includes the aforementioned interface ion-electron conversion enhanced wet gas power generation device. Therefore, the power generation device exhibits excellent and stable electrical output performance. It should be noted that the features and advantages described above for the interface ion-electron conversion enhanced wet gas power generation device also apply to this power generation device, and will not be repeated here.

[0130] The present invention will now be described with reference to specific embodiments. It should be noted that these embodiments are merely descriptive and do not limit the present invention in any way.

[0131] (1) Select commercially available graphite foil as the first electrode layer.

[0132] (2) The first interface layer is directly coated onto the first electrode layer by a doctor blade. The preparation steps of the first interface layer are as follows:

[0133] MnO2 nanoparticles were selected as the first electrochemically active material, Super P as the conductive agent, and polyvinylidene fluoride (PVDF) as the binder. 10 g of PVDF was dissolved in 500 ml of N-methylpyrrolidone (NMP) and magnetically stirred at room temperature for 24 hours to obtain a binder slurry. An electroactive material slurry was prepared by mixing 70 wt% MnO2 nanoparticles, 20 wt% Super P, and 10 wt% PVDF. Using a 100 μm doctor blade, the electrochemically active material slurry was coated onto a graphite foil and dried in a 60 °C oven to obtain a first interface layer supported on the first electrode layer. The first electrode layer and the first interface layer together are referred to as the MnO2 electrode. The thickness of the dried first interface layer was 12 μm.

[0134] (3) Select commercially available graphite foil as the second electrode layer.

[0135] (4) The fourth interface layer is directly coated onto the second electrode layer by a doctor blade. The preparation steps of the fourth interface layer are as follows:

[0136] MoS2 nanosheets were selected as the second electrochemically active material, Super P as the conductive agent, and polyvinylidene fluoride (PVDF) as the binder. 10 g of PVDF was dissolved in 500 ml of N-methylpyrrolidone (NMP) and magnetically stirred at room temperature for 24 hours to obtain a binder slurry. An electroactive material slurry was prepared by mixing 70 wt% MoS2 nanosheets, 20 wt% Super P, and 10 wt% PVDF. Using a 100 μm doctor blade, the electrochemically active material slurry was coated onto a graphite foil and dried in a 60 °C oven to obtain a fourth interface layer supported on the second electrode layer. The second electrode layer and the fourth interface layer together are referred to as the MoS2 electrode. The thickness of the dried fourth interface layer was 12 μm.

[0137] (5) Using laser, through holes are fabricated on the second electrode layer and the fourth interface layer. The porosity of the through holes is 40%.

[0138] (6) I2 / KI was selected as the first redox couple, and the preparation steps of the second interface layer are as follows:

[0139] A mixed solution, denoted as H-PSS solution, was prepared by uniformly mixing an aqueous dispersion (15 wt%) of poly(4-styrene sulfonic acid) with 0.01 M H₂SO₄ in equal volumes. An aqueous solution containing 1.25 mM I₂ and 5 mM KI was also prepared. - / I - Solution; mix H-PSS solution (10 ml) and I3 - / I - The solution (5 ml) was uniformly mixed at a volume ratio of 2:1, denoted as the H-PSS / I solution. The H-PSS / I solution was placed in a petri dish and dried in an oven at 45°C and 60% RH to obtain a second interfacial layer with a thickness of 370 μm, denoted as the H-PSS / I film. I3 is present within the H-PSS / I film. - / I - The theoretical content is 0.043 wt%.

[0140] (7) Selecting K3[Fe(CN)6] / K4[Fe(CN)6] as the second redox couple, the preparation steps of the third interface layer are as follows:

[0141] A mixed solution, denoted as H-PSS solution, was prepared by uniformly mixing an aqueous dispersion (15 wt%) of poly(4-styrenesulfonic acid) with 0.01 M H₂SO₄ in equal volumes. An aqueous solution containing 5 mM K₃[Fe(CN)₆] and 5 mM K₄[Fe(CN)₆] was also prepared. 3- / 4- Solution; mix H-PSS solution (10 ml) with [Fe(CN)6] 3- / 4- The solution (5 ml) was uniformly mixed at a volume ratio of 2:1, denoted as the H-PSS / Fe solution. The H-PSS / Fe solution was placed in a petri dish and dried in an oven at 45°C and 60% RH to obtain a third interface layer with a thickness of 370 μm, denoted as the H-PSS / Fe film. [Fe(CN)6] is present within the H-PSS / Fe film. 3- / 4- The theoretical content is 0.095 wt%.

[0142] (8) The preparation steps of the moisture-generating layer are as follows:

[0143] A mixed solution, denoted as H-PSS solution, was obtained by mixing 15 wt% of poly(4-styrene sulfonic acid) aqueous dispersion with 0.01 M H2SO4 in equal volumes. The H-PSS solution was placed in a petri dish and dried in an oven at 45 °C and 60% RH to obtain a 740 μm thick moisture-generating layer, denoted as H-PSS film.

[0144] The MnO2 electrode, H-PSS / I film, H-PSS film, H-PSS / Fe film and MoS2 electrode were stacked sequentially, and the other positions except for the through holes of the MoS2 electrode were encapsulated with hot melt adhesive to prepare a moisture power generation device with enhanced interfacial ion-electron conversion (hereinafter referred to as the device).

[0145] The performance of the device prepared in Example 1 was measured, as follows:

[0146] (1) Characterization of each functional layer by scanning electron microscopy, X-ray diffraction and energy-dispersive X-ray spectroscopy

[0147] The morphology and structure of the material were characterized using scanning electron microscopy (SEM), the crystal form of the functional layer material was analyzed using X-ray diffraction (XRD), and the chemical composition of the functional layer was analyzed using energy-dispersive X-ray spectroscopy (EDS). Figure 3 As can be seen, MnO2 nanoparticles and Super P are uniformly dispersed and coated on the graphite foil. The MnO2 nanoparticles are ε-MnO2 (e.g., Figure 4 (As shown). By Figure 5 MoS2 nanosheets and Super P can be seen to be uniformly dispersed and coated on the graphite foil. The MoS2 nanosheets are 2H-MoS2 (e.g., Figure 6 As shown). PSS is uniformly dispersed in the H-PSS film (e.g. Figure 7 (As shown), I3 - / I - Uniformly dispersed in H-PSS / I film (e.g. Figure 8 As shown), [Fe(CN)6] 3- / 4- Uniformly dispersed in H-PSS / Fe thin film (e.g. Figure 9 (As shown).

[0148] (2) Analysis of functional groups and surface charge of each functional layer

[0149] The elemental dispersion within the functional layers was investigated using X-ray photoelectron spectroscopy, and the surface charge of the material was evaluated using a Zeta potential analyzer. Figure 10 It can be seen that Super P has carboxyl and hydroxyl groups, which will produce fixed negatively charged -COO- and -O- groups. The fine X-ray photoelectron spectroscopy of Mn 2p on the MnO2 electrode shows Mn 2p belonging to Mn(Ⅳ). 3 / 2(BE = 642.03 eV) and Mn 2p 1 / 2 The bimodal property of (BE=653.66eV); through the analysis of Mn 2p 3 / 2 Deconvolution of the peaks yields the relative contents of Mn(Ⅳ) and Mn(Ⅲ); in the fine X-ray photoelectron spectrum of the O1s of the MnO2 electrode, the peak with a binding energy of 529.13 eV belongs to lattice oxygen (Mn-O), while the peaks at 530.63 eV and 531.90 eV belong to surface-adsorbed oxygen (C-OH, HOH) (physically adsorbed water) (such as... Figure 11 (As shown). In the fine X-ray photoelectron spectrum of Mo 3d in the MoS2 electrode, two peaks with binding energies of approximately 229.43 eV and 232.58 eV are associated with Mo(Ⅳ)3d in 2H-MoS2. 5 / 2 and 3D 3 / 2 Consistent. In the fine X-ray photoelectron spectrum of S2p, the two peaks with binding energies of 162.25 eV and 163.44 eV can be attributed to S2p in 2H-MoS2. 3 / 2 and 2p 1 / 2 (like Figure 12 (As shown). The Zeta potential of the MnO2 electrode is 31 mV, and the Zeta potential of the MoS2 electrode is -9 mV (as shown). Figure 13 (As shown).

[0150] (3) The effect of the asymmetric surface charge of MnO2 and MoS2 electrodes on electrical output performance

[0151] When the device is placed in a high-humidity environment, the moisture-generating layer absorbs moisture, and mobile cations can form within the H-PSS film. Since the MoS2 electrode surface carries a negative charge, cations are adsorbed onto its surface (e.g., ...). Figure 14 As shown), its electric double layer causes changes in electrode potential, similar to changes in solution (e.g. Figure 15 (As shown). Meanwhile, cations (H... + The directional migration of MnO2 leads to the movement of electrons in the external circuit to shield ionic charges, further causing changes in electrode potential. When water permeates the entire H-PSS film, due to the positive charge (31mV) on the MnO2 electrode surface, the polyanions (-SO3)... - ) are adsorbed on the surface of the MnO2 electrode (e.g. Figure 14 As shown), this further widens the potential difference (e.g. Figure 15 (As shown).

[0152] (4) Potential measurement of each interface layer and electrode layer

[0153] When two phases come into contact, electrons always transfer from the side with higher chemical potential to the side with lower chemical potential; therefore, determining the potentials of each interface layer and electrode layer is necessary. The electrode potentials of the MnO2 electrode and the MoS2 electrode on the H-PSS film and in a humid field are 1.31V and 0.53V, respectively (e.g., ...). Figure 16 (As shown). In the H-PSS membrane solution, I3 - / I - and [Fe(CN)6 ]3- / 4- The potentials are 0.67V and 0.63V respectively (e.g. Figure 17 As shown). The potential distribution illustrates that, under open-circuit conditions and a humid gas field, the increased potential difference between the MnO2 and MoS2 electrodes causes charge transfer between the electrodes and the redox couples within the interface layer (e.g., ...). Figure 18 (As shown): I3 - / I - A reduction reaction occurs, transferring electrons to the MnO2 electrode.

[0154] [Fe(CN)6] 3- / 4- Oxidation occurs, and electrons are gained from the MoS2 electrode. This form of electron transfer can participate in the charge balance at the wet power generation layer / electrode interface, weakening the built-in electric field and increasing the number of directionally migrating ions, thus enabling the storage of more ions on the electrode. Furthermore, due to the MnO2-I3... - / I - The side potential is higher than that of MoS2-[Fe(CN)6]. 3- / 4- Lateral potential (e.g.) Figure 18 As shown in the diagram, under short-circuit conditions, the electron transfer directions at the interface are reversed, resulting in an increase in output current. Therefore, in both open-circuit and short-circuit conditions, the redox couple acts as an "electron sponge," playing a dual role in promoting power generation (e.g., ...). Figure 18 (As shown).

[0155] (5) Electrical output performance of moisture generator with enhanced interfacial ion-electron conversion

[0156] To better utilize the "electron sponge" effect of the redox couple, a quasi-continuous operation mode was designed. When the device is exposed to a humid environment, it self-charges to its open-circuit voltage within 20 minutes, then discharges for 10 seconds with current flowing through an external load. After 20 minutes, the device voltage returns to its open-circuit voltage, and the next discharge cycle begins. Quasi-continuous discharge can be achieved by changing the external circuit connection. Therefore, a 1×1 cm² device can achieve an open-circuit voltage of 0.79V and a current of 7.44mA at 98% relative humidity. -2 short-circuit current (e.g.) Figure 19 As shown), 6.69 W / m was obtained under a 47Ω load. -2Maximum power density (e.g.) Figure 20 (As shown). By further simplifying and splitting the system, the effects of electrodes, redox couples, and humidity fields on electrical output performance can be isolated. The contributions of the asymmetric electroactive material, the asymmetric redox couple, and the humidity field to the voltage are 71.2%, 5.5%, and 23.3%, respectively, and their contributions to the accumulated charge are 37.25%, 12.75%, and 50.00%, respectively.

[0157] (6) Changes in electrochemically active materials in the interface layer during the power output process

[0158] Depend on Figure 21 It can be seen that the ratio of Mn(Ⅲ) to Mn(Ⅳ) after quasi-continuous output remains unchanged compared to when there is no output, indicating the stability of the MnO2 electrode. Similarly, the lattice oxygen and adsorbed oxygen also show no significant changes (e.g., Figure 21 shown). Mo(Ⅳ)3d 5 / 2 Mo(Ⅳ)3d 3 / 2 S2p 3 / 2 and S2p 1 / 2 The peak positions did not change significantly compared to when there was no output, indicating the stability of the MoS2 electrode (e.g., Figure 22 (As shown).

[0159] (7) Changes of redox couple in the interface layer during the electrical output process

[0160] The changes in redox couples in H-PSS / I membrane solutions and H-PSS / Fe solutions during a quasi-continuous output process were detected using UV-Vis absorption spectroscopy. MnO2 and MoS2 electrodes were immersed in H-PSS / I membrane solutions and H-PSS / Fe solutions, respectively. Due to the strong absorption of the H-PSS solution, only I3 was detected. - (357nm) and [Fe(CN)6] 3- (420nm) (e.g.) Figure 23 and Figure 24 As shown in the figure, both peaks satisfy the quantitative requirements of the Lambert-Beer law. Figure 23 and Figure 24 As shown, I3 - and [Fe(CN)6] 3- The absorbance did not change significantly during the quasi-continuous output process, and was similar to that of the blank control group with no output (e.g. Figure 25 (As shown). In an aqueous cell with the same redox couple and electrodes, I3 - / I - and [Fe(CN)6] 3- / 4- The peak values ​​all changed significantly after the same discharge time (e.g. Figure 26 , Figure 27As shown in the figure, this further demonstrates that the redox couple in the device, unlike the unidirectional discharge of a flow battery, performs bidirectional electron transfer at the interface in the form of an "electron sponge".

[0161] (8) Changes in ion storage sites in the interface layer

[0162] The capacitance of the MnO2 electrode and the MoS2 electrode is much greater than that of the original graphite foil (e.g., Figure 28 As shown in the figure, this indicates that the ion storage capacity of the electrode interface is significantly improved after coating the graphite surface with MnO2 nanoparticles and MoS2 nanosheets.

[0163] (9) Self-recovery of device electrical output performance

[0164] Moisture-induced ion migration allows the electrode potential to quickly recover to its pre-output state after switching to the open-circuit state (e.g., Figure 29 (As shown). Furthermore, its voltage recovery capability can be further demonstrated using a constant current charge-discharge method, at a discharge current density of 100 μA cm⁻¹. -2 When the device voltage is reduced to 0V, the device can self-charge to an open-circuit voltage of 0.6V, and maintains good self-recovery performance after multiple discharge-recharge cycles (e.g., Figure 30 (As shown).

[0165] (10) Cyclic stability of device electrical output performance

[0166] The electrical signal generated by the device is induced by charge separation caused by the directional migration of ions in a humid environment. However, due to the thermal motion of ions, anions and cations in the humidification layer will eventually tend to be evenly distributed, and the electrical signal will inevitably disappear within a certain time. Therefore, after quasi-continuous discharge for 5 hours, the device can be reactivated by removing the humidification field and completely drying the humidification layer. When the reactivated device is exposed to the humidity field again, its voltage and current will recover, and it will maintain a stable output after multiple dehumidification-re-hygroscopic cycles (e.g., ...). Figure 31 (As shown).

[0167] (11) Flexibility of the device

[0168] The device exhibits excellent flexibility, maintaining a stable power output even after being bent at 45° (e.g., Figure 32 (As shown).

[0169] (12) Device integration performance

[0170] The integration of components is a key factor in meeting practical power requirements. Connecting 30 1×1cm components in series can generate a 22V voltage; the series voltage increases linearly with the number of components connected in series (e.g., ...). Figure 33As shown). Connecting 40 1×1cm devices in parallel can generate a current of 390mA, and the parallel current increases linearly with the number of devices connected in parallel (e.g.). Figure 33 As shown in the figure, this demonstrates that the device has good integration performance.

[0171] (13) The integrated device group charges other energy storage devices.

[0172] By fabricating a 1×1cm device into a 4×2 integrated device group (four in series, then two in parallel), a 4F capacitor can be charged to 0.43V within 100 hours. Figure 34 (As shown).

[0173] Example 2

[0174] The main difference between Example 2 and Example 1 is that the ambient humidity for induced electrical output is different.

[0175] from Figure 35 It can be seen that as the relative humidity decreases from 98% to 23%, the open-circuit voltage decreases from 0.79V to 0.67V, the short-circuit current decreases from 7.44mA to 2.97mA, and the cumulative output charge over 12 hours decreases from 0.86C to 0.16C. This is because relative humidity directly affects the intensity of the humidity field, which in turn affects the electrode potential and its recovery, thus further affecting the bidirectional reaction capability of the redox couple. Therefore, the voltage, current, and cumulative output charge over 12 hours all decrease with decreasing relative humidity.

[0176] Example 3

[0177] The main difference between Example 3 and Example 1 is that the self-charging time is different.

[0178] Under a fixed discharge time (10s) and different self-charging times, the output power is highest when the self-charging time is 15 minutes (e.g., Figure 36 (As shown). This is because the longer the self-charging time, the more electrons are transferred between the redox couple and the electrode interface. These electrons can transfer in the opposite direction in the next discharge cycle, thus improving the electrical output performance. The subsequent power decrease is because the self-charging time has a greater effect on the power (slope) than on ∫I 2 The effect of dt ( Figure 36 (Illustration). As the self-charging time increases, ∫I 2 dt 12h The increasing number of electrons further demonstrates that the directions of electron transfer between the redox couple and the electrode interface differ during discharge and self-charging processes (e.g., ...). Figure 36 (As shown).

[0179] Example 4

[0180] The main difference between Example 4 and Example 1 is the discharge time.

[0181] Under a fixed self-charging time (20 min) and different discharge times, the voltage and current holding ratios continuously decrease with increasing discharge time. This is because the electron transfer during the self-charging phase cannot offset the energy loss during the discharge phase (e.g., ...). Figure 37 As shown). The cumulative discharge charge and energy continuously decrease over 12 hours (as shown). Figure 37 As shown in the figure, this further illustrates the reduced discharge capability of the device.

[0182] Example 5

[0183] The main difference between Example 5 and Example 1 is that, with a fixed H-PSS film thickness (740 μm), the thicknesses of the H-PSS / I film and the H-PSS / Fe film are different. Specifically, the ratios of the thicknesses of the H-PSS / I film, H-PSS film, and H-PSS / Fe film are 1:2:1, 2:2:2, 3:2:3, and 5:2:5, respectively.

[0184] Depend on Figure 38 It can be seen that with the increase of the thickness of H-PSS / I and H-PSS / Fe films, the voltage change is not significant, while the current first decreases, then increases, and then decreases again. The initial decrease in current is mainly due to the increase in ion migration resistance. The subsequent increase is because the increase in thickness leads to an increase in the redox couple content in the film, i.e., an increase in the number of redox couples participating in the reaction during self-charging. Then, the continued increase in thickness causes an increase in ion migration resistance, thereby reversing the positive effect caused by the increase in redox couple content, and thus the current decreases accordingly.

[0185] Example 6

[0186] The main difference between Example 6 and Example 1 is that, with a fixed H-PSS / I film and H-PSS / Fe film thickness (370 μm), the thickness of the H-PSS film is different. Specifically, the ratios of the thickness of the H-PSS / I film to the thickness of the H-PSS film to the thickness of the H-PSS / Fe film are 1:1:1, 1:2:1, 1:3:1, and 1:4:1, respectively.

[0187] Depend on Figure 39 It can be seen that as the thickness of H-PSS increases, the voltage, current, and cumulative discharge energy all first increase and then decrease. The output performance of the H-PSS / I film thickness:H-PSS film thickness:H-PSS / Fe film thickness ratio of 1:2:1 is better than other thickness ratios. When the thickness ratio is too small, the H-PSS film cannot effectively block the I3 in the H-PSS / I film and H-PSS / Fe film. - / I - and [Fe(CN)6]3- / 4- The direct reaction between them. When the thickness ratio is too large, the increase in the thickness of the H-PSS film will hinder water permeation and increase the resistance to ion migration.

[0188] Example 7

[0189] The main difference between Example 7 and Example 1 is that the I3 in the H-PSS / I solution and the H-PSS / Fe solution is different. - / I - Solution and [Fe(CN)6] 3- / 4- The solution concentrations are different. Specifically, 10 ml of H-PSS solution is mixed with 5 ml, 10 ml, 15 ml, and 20 ml of I3, respectively. - / I - Solution and [Fe(CN)6] 3- / 4- The solutions were mixed to obtain H-PSS / I solution and H-PSS / Fe solution.

[0190] from Figure 40 It can be seen that as the content of redox couples increases, the voltage decreases continuously, while the current first increases and then decreases. The decrease in voltage is due to the enhanced electron transfer at the interface between the redox couple and the electrode. The enhanced electron transfer reaction leads to an initial increase in the output current, but the continuous decrease in voltage leads to a decrease in the current.

[0191] Example 8

[0192] The main difference between Example 8 and Example 1 is that the thickness of the MoS2 electrode is different, that is, the thickness of the fourth interface layer is different. The thicknesses of the fourth interface layer are 12μm, 16μm, 20μm and 24μm respectively.

[0193] Electrode capacity affects ion storage at the interface, thus influencing electrical output performance. As the thickness of the MoS2 electrode increases, the MoS2 electrode capacity continuously increases (e.g., ...). Figure 41 As shown in the figure, with the increase of MoS2 electrode thickness, the voltage did not change significantly, the current first increased and then decreased, and the discharge capacity decreased (e.g.). Figure 42 (As shown). The initial increase in current is due to the increase in ion storage sites on the electrode, but the continuous increase in electrode thickness leads to an increase in the resistance to ion migration in the electrode, thereby affecting ion storage and reducing the current.

[0194] Example 9

[0195] The main difference between Example 9 and Example 1 is that the device area is different; the device area is 2 cm². -2 4cm -2 6cm -2 and 8cm -2 .

[0196] As the device area increases, the voltage remains almost constant, while the current initially increases and then remains constant (e.g., ...). Figure 43 (As shown). The current cannot continue to increase because the rate of moisture penetration in different parts of the device is difficult to achieve uniformity over a large area.

[0197] Example 10

[0198] The main difference between Example 10 and Example 1 is that the first electrochemical active material is CuFeTBA, and the second electrochemical active material is activated carbon.

[0199] like Figure 44 As shown, the maximum output voltage of Example 10 is 0.27V and the maximum output current is 2.07mA.

[0200] Comparative Example 1

[0201] The main difference between Comparative Example 1 and Example 1 is that the output method is different, that is, the recovery time is zero, which is recorded as continuous output.

[0202] The output energy and output charge (e.g.) were compared under continuous output and quasi-continuous output conditions. Figure 45 (As shown). The output energy of the quasi-continuous output maintains a stable linear increase, while the output energy of the continuous output quickly reaches a plateau, and the same phenomenon appears in the output charge. It is worth noting that the output charge at 120,000s has reached 1.4C, which is much higher than the limit charge calculated by the redox couple unidirectional reaction (0.02C), indicating that the discharge of the device is different from the discharge of the battery based on the redox couple unidirectional reaction.

[0203] Comparative Example 2

[0204] The main difference between Comparative Example 2 and Example 1 is that the interface layer and the moisture-generating layer are different.

[0205] The electro-output performance of H-PSS films, H-PSS / I films, and H-PSS / Fe films sandwiched between MnO2 and MoS2 electrodes, respectively, was compared. Figure 46 and Figure 47 It can be seen that the voltage and current in Comparative Example 2 are both less than those in Example 1 during continuous output. In quasi-continuous output, the accumulated charge in 12 hours is also significantly less than that in Example 1, which illustrates the necessity of the coexistence of H-PSS / I film, H-PSS film and H-PSS / Fe film.

[0206] Comparative Example 3

[0207] The main difference between Comparative Example 3 and Example 1 is that the direction of the moisture field is different.

[0208] The electrical output performance of forward-moving, reverse-moving, and uniform-moving (i.e., liquid phase) moisture fields was compared. Figure 48 It can be seen that the voltage of the forward humidification field is greater than that of the uniform humidification field, and also greater than that of the reverse humidification field. This indicates that directional ion migration can induce voltage generation, and when it is aligned with the voltage induced by the asymmetric double layer, it can promote voltage generation. The 12-hour accumulated charge of the forward humidification field is also significantly higher than that of the reverse and uniform humidification fields. This is because the lower voltage weakens the electron transfer reaction at the electrode interface between the redox couple and the open circuit.

[0209] Comparative Example 4

[0210] The main difference between Comparative Example 4 and Example 1 is that the redox couple is added in a different way during the preparation of the functional layer.

[0211] The preparation of the membrane solution was compared with that of Example 1, where the same amount of I was used. 3- / I - Solution and [Fe(CN)6] 3- / 4- The solution was mixed with H-PSS solution to prepare a uniform layer containing I3 with a thickness of 1480 μm. - / I - and [Fe(CN)6] 3- / 4- A thin film was prepared and assembled with MnO2 and MoS2 electrodes to form a device, and its electrical output performance was studied. Figure 49 It can be seen that the voltage, current, output charge, and energy are all lower than those in Example 1, indicating that the H-PSS film in Example 1 can effectively block I3 in H-PSS / I. - / I - [Fe(CN)6] in H-PSS / Fe 3- / 4- The direct reaction between them.

[0212] Comparative Example 5

[0213] The main difference between Comparative Example 5 and Example 1 is that the redox couple in the functional layer is replaced with an electro-active substance (KCl).

[0214] Comparative Example 5 uses [Fe(CN)6] from Example 1. 3- / 4- Replace the solution with a 5mM KCl aqueous solution, and add I3 - / I - The solution was replaced with a 5 mM KCl aqueous solution, and then the same steps were followed to assemble the device. Figure 50 It can be seen that the current, cumulative charge and energy output in Comparative Example 5 are all less than those in Example 1, indicating that the good performance of the device in Example 1 is not caused by the reduction of membrane resistance due to the addition of redox couple.

[0215] In summary, this application successfully developed a moisture-powered device with enhanced interfacial ion-electron conversion. By designing the device's structure and composition, the number of ion storage sites on the electrode surface was increased, improving the ion-electron conversion capability and efficiency at the interface. Furthermore, a new ion-electron conversion pathway was introduced at the interface, and a redox couple was introduced. Electron transfer reactions between the redox couple and the electrode were driven by the electrode potential change induced by the moisture field. On the one hand, charge can be stored in the functional layer in this way and released to the external circuit during electrical output. On the other hand, the built-in electric field can be weakened, promoting directional ion migration within the membrane and achieving the storage of more ions. By improving the interfacial ion-electron conversion efficiency and weakening the built-in electric field, the electrical output performance of the moisture-powered device is improved (Examples 1-7). This device also possesses good flexibility and series-parallel integration capabilities, enabling it to charge commercial energy storage devices and providing broad prospects for the development of green hydropower.

[0216] In the description of this specification, the references to terms such as "one embodiment," "some embodiments," "example," "specific example," or "some examples," etc., indicate that a specific feature, structure, material, or characteristic described in connection with that embodiment or example is included in at least one embodiment or example of the present invention. In this specification, the illustrative expressions of the above terms do not necessarily refer to the same embodiment or example. Furthermore, the specific features, structures, materials, or characteristics described may be combined in any suitable manner in one or more embodiments or examples. Moreover, without contradiction, those skilled in the art can combine and integrate the different embodiments or examples described in this specification, as well as the features of different embodiments or examples.

[0217] Although embodiments of the present invention have been shown and described above, it is understood that the above embodiments are exemplary and should not be construed as limiting the present invention. Those skilled in the art can make changes, modifications, substitutions and variations to the above embodiments within the scope of the present invention.

Claims

1. An interface ion-electron conversion enhanced wet gas power generator device, characterized by, include: First electrode layer; A first interface layer is stacked on one side of the first electrode layer, and the first interface layer includes a first electrochemical active material. A second interface layer is stacked on the side of the first interface layer away from the first electrode layer, and the second interface layer includes a first redox couple. A moisture-generating layer is stacked on the side of the second interface layer away from the first interface layer; A third interface layer is stacked on the side of the moisture-generating layer away from the second interface layer, and the third interface layer includes a second redox couple. A fourth interface layer is stacked on the side of the third interface layer away from the moisture-generating layer, and the fourth interface layer includes a second electrochemically active material. The second electrode layer is stacked on the side of the fourth interface layer away from the third interface layer, and the second electrode layer has through holes.

2. The power generating device of claim 1, wherein The first electrochemically active material and the second electrochemically active material each independently include at least one of the following: carbon material with double-layer capacitance behavior, metal oxide with pseudocapacitive behavior, conductive polymer with pseudocapacitive behavior, metal oxide with intercalation behavior, metal chalcogenide with intercalation behavior, metal-organic framework and covalent organic framework. And / or, the moisture-generating layer comprises at least one of carbon materials, polyelectrolytes, metal oxides, metal sulfides, two-dimensional transition metal carbides, zeolites, metal-organic frameworks, covalent organic frameworks, plants, and microorganisms.

3. The power generating device of claim 2, wherein, The carbon material with double-layer capacitance behavior includes at least one of porous activated carbon material, ordered mesoporous carbon, carbide-derived carbon, ordered hierarchical mesoporous / microporous carbon, ordered mesoporous carbon nanofiber bundles, and heteroatom-doped carbon material. And / or, the metal oxide having pseudocapacitive behavior includes at least one of ruthenium-based materials, manganese-based materials, nickel-based materials, and cobalt-based materials; And / or, the conductive polymer having pseudocapacitive behavior includes at least one of polyacetylene, polypyrrole, polyaniline, and poly(3,4-ethylenedioxythiophene); And / or, at least one of the orthorhombic metal oxides Nb2O5 (T-Nb2O5) and Ni(OH)2 having intercalation behavior; And / or, the metal chalcogenides with intercalation behavior include at least one of MoS2, MoTe2 and ReS2; And / or, the metal-organic framework comprises at least one of ZIF-8, ZIF-67, MOF-74, MOF-808, and Prussian blue-like materials; And / or, the covalent organic framework includes at least one of COF-1, COF-5, ZnP-COF, CuP-COF, Py-Azine COF, and HPB-COF.

4. The power generating device of claim 1, wherein, The first redox couple and the second redox couple each independently comprise at least one of a metal compound, a halide, and an aromatic compound.

5. The power generating device of claim 4, wherein The metal compound includes Fe. 2+ / 3+ Cr 2+ / 3+ [Fe(CN)6] 3- / 4- [IrCl4] 2- / [IrCl4] 3- [Ru(bpy)3] 2+ / 3+ At least one of cobalt tri / dipyridine and metal locene; and / or the halide comprises I3 - / I - and Br2 / Br - at least one of And / or, the aromatic compound includes at least one of thiaanthracene, thiaanthracene derivatives, phenazine, phenazine derivatives, phenthia, phenthia derivatives, quinoline, quinoline derivatives, phenol, phenol derivatives, 2,2,6,6-tetramethylpiperidin-1-yloxy derivatives, anthraquinone derivatives, anisole, and bi(bi)anisole.

6. The power generating device of claim 1, wherein, The method for preparing the first interface layer includes: mixing the first electrochemical active material, the first conductive agent, the first binder and the first solvent and applying them to one side of the first electrode layer to obtain a non-self-supporting first interface layer; And / or, the method for preparing the fourth interface layer includes: mixing the second electrochemical active material, the second conductive agent, the second binder, and the second solvent and applying the mixture to one side of the second electrode layer to obtain the non-self-supporting fourth interface layer; And / or, the method for preparing the second interface layer includes: drying a solution containing a first host material and a first redox couple to obtain a self-supporting second interface layer; And / or, the method for preparing the third interface layer includes: drying a solution containing a second host material and a second redox couple to obtain the self-supporting third interface layer; And / or, the method for preparing the second interface layer includes: scraping or electrochemically depositing a first redox couple on the side of the first interface layer away from the first electrode layer to form a non-self-supporting second interface layer; And / or, the method for preparing the third interface layer includes: coating or electrochemically depositing a second redox couple on the side of the fourth interface layer away from the second electrode layer to form the non-self-supporting third interface layer.

7. The power generating device of claim 6, wherein, The mass ratio of the first electrochemically active material, the first conductive agent, and the first binder is (7~9):(2~0.5):(1~0.5). And / or, the mass ratio of the second electrochemically active material, the second conductive agent, and the second binder is (7~9):(2~0.5):(1~0.5); And / or, based on the total mass of the self-supporting second interface layer, the mass percentage of the first redox couple is 0.005wt%~0.3wt%; And / or, based on the total mass of the self-supporting third interface layer, the mass percentage of the second redox couple is 0.005wt%~0.3wt%; And / or, the first host material and the second host material each independently include at least one of carbon materials, polyelectrolytes, metal oxides, metal sulfides, two-dimensional transition metal carbides, zeolites, metal-organic frameworks, covalent organic frameworks, plants, and microorganisms.

8. The power generating device according to any one of claims 1 to 7, wherein The porosity of the through-holes on the second electrode layer is 30%~80%; And / or, the thickness of the first interface layer is 5μm~100μm; And / or, the thickness of the fourth interface layer is 5μm~100μm; And / or, the thickness of the moisture-generating layer is 100μm~800μm; And / or, the thickness of the second interface layer is 50 μm to 400 μm; And / or, the thickness of the third interface layer is 50μm~400μm; And / or, the thickness ratio of the second interface layer, the moisture power generation layer and the third interface layer is 1: (1~2):

1.

9. A power generation device characterized by comprising: The moisture power generation device comprising the interface ion-electron conversion enhanced according to any one of claims 1-8.

Images