Fluorocarbon modified polymer insulating material and insulating joint

Abstract

The present application relates to the technical field of high polymer special electrical insulation material manufacturing, in particular to a fluorocarbon modified high polymer insulation material and an insulation joint, and a preparation method of the fluorocarbon modified high polymer insulation joint insulation material, which comprises the following steps: preparing a homogeneous resin base liquid by vacuum devolatilization of aromatic rigid skeleton epoxy resin and multi-function fluorinated epoxy resin; adding two-dimensional modified fluorinated graphene powder and zero-dimensional surface fluorinated nano dielectric filler for high-strength dispersion and ultrasonic defoaming; sequentially injecting aromatic fluorinated diamine curing agent, perfluoropolyether modified polysiloxane leveling agent and silane coupling agent in a light-proof and low-humidity environment, and performing a flexible kneading mixing operation; pouring the multi-phase homogeneous mixture into a mold, and then performing a step-by-step thermodynamic curing program including a gel crosslinking stage, a high-temperature curing stage and a conformation rearrangement stage. The present application improves the multi-field coupling resistance and size stability of the insulation joint insulation material.

Description

Technical Field

[0001] This invention relates to the field of manufacturing technology of special polymer electrical insulation materials, specifically to a fluorocarbon modified polymer insulation material and an insulation connector. Background Technology

[0002] In modern energy transmission systems, insulating joints in inter-regional ultra-high voltage direct current transmission systems, cathodic protection systems for deep-sea oil and gas pipelines, and traction power distribution networks for heavy-duty rail transit serve multiple functions, including electrical isolation, pipeline mechanical connection, and high-pressure fluid sealing. Their applications are continuously expanding to conditions involving high-concentration corrosive salt spray, high absolute humidity, wide-range thermal shock, and strong electric field coupling.

[0003] Existing high-voltage insulation joints mostly use single-component aromatic bisphenol A type epoxy resin as the load-bearing body. This resin macromolecular chain contains residual polar hydroxyl groups and incompletely reacted active end groups. Under the long-term action of an ultra-high voltage alternating electric field, the polar dipoles undergo high-frequency orientation reversal polarization in accordance with the electric field direction, accompanied by intramolecular micro-friction effects, inducing dielectric loss and heat accumulation. The accumulation of heat, combined with external mechanical loads, forces the resin matrix to cross the glass transition temperature, macroscopically manifesting as irreversible high-temperature creep deformation. Creep deformation causes relaxation of the normal compression stress at the internal sealing interface of the insulation joint, leading to moisture penetration and electrochemical partial discharge.

[0004] In existing technologies, modification methods employ physical blending of low surface energy materials. Polytetrafluoroethylene (PTFE) micropowder is directly physical blended with a polar epoxy resin matrix, utilizing its low polarity to enhance corrosion resistance and hydrophobicity. However, this system lacks covalent bonding between the PTFE micropowder and the polar epoxy resin matrix, and interfacial thermodynamic incompatibility leads to macroscopic phase separation. During vacuum casting of thick-walled, irregularly shaped insulating joints, the phase separation interface forms a microporous leakage network penetrating the wall thickness. When conventional inorganic nano-silica fillers are introduced to enhance mechanical modulus, fillers with mismatched surface dielectric parameters undergo electrostatic agglomeration in high-viscosity resin bases. According to the Maxwell-Wagner interfacial polarization theory, the dielectric constant difference between the filler agglomerates and the resin matrix causes local electric field distortion when the electric field penetrates the phase interface, leading to space charge accumulation at the interface and accelerating the initiation and penetration of high-voltage electrical trees. Surface-based formulation improvements fail to address the electric field distortion and thermal creep failure from the physical nature of the polymer chain segment thermal motion energy levels and space charge transport channels. Summary of the Invention

[0005] The purpose of this invention is to provide a fluorocarbon modified polymer insulating material and an insulating joint, which solves the technical problems of insufficient creep resistance and poor interfacial compatibility of existing high-voltage insulating joint materials under extreme coupling conditions due to electric field distortion at the phase separation interface, thermal creep dimensional instability, and insulation microcracks induced by environmental stress.

[0006] To solve the above-mentioned technical problems, the technical solution adopted by the present invention is as follows: A fluorocarbon-modified polymer insulating material, wherein the insulating material is prepared by the following steps: Step 1: Aromatic rigid skeleton epoxy resin and multifunctional fluorinated epoxy resin are put into a reaction device and vacuum devolatilization reaction is performed under constant temperature and negative pressure conditions to prepare a homogeneous resin base liquid. The homogeneous resin base liquid is uniform to the naked eye. Step 2: Add two-dimensional modified fluorinated graphene powder and zero-dimensional surface fluorinated nano-dielectric filler to the homogeneous resin base liquid, apply a high energy density physical cross shear stress field for high-intensity dispersion, and apply ultrasonic degassing treatment to the fluid slurry after high-intensity dispersion. Step 3: Control the working environment to be in a light-proof state and maintain the upper limit of relative humidity not exceeding 40%. Inject aromatic fluorinated diamine curing agent, perfluoropolyether modified polysiloxane leveling agent and silane coupling agent into the fluid slurry that has undergone ultrasonic degassing treatment in sequence. Perform flexible kneading and mixing operation under constant low temperature conditions to obtain a multiphase uniform mixture. Step 4: The multiphase homogeneous mixture is poured into the preheated inner cavity of the insulating joint metal mold and a multi-stage stepped thermodynamic curing process is executed. The multi-stage stepped thermodynamic curing process includes a gel crosslinking stage, a high-temperature curing stage, and a conformational rearrangement stage in sequence. After the multi-stage stepped thermodynamic curing process is completed, a demolding process is performed to obtain the molded fluorocarbon modified polymer insulating joint insulating material.

[0007] Furthermore, the raw materials for preparation include: 60 to 80 parts of aromatic rigid skeleton epoxy resin; 20 to 40 parts of multifunctional fluorinated epoxy resin; 0.5 to 2.5 parts of two-dimensional modified fluorinated graphene powder; 5 to 15 parts of zero-dimensional surface fluorinated nano-dielectric filler; 35 to 50 parts of aromatic fluorinated diamine curing agent; 0.2 to 0.8 parts of perfluoropolyether modified polysiloxane leveling agent; 1.0 to 2.0 parts of silane coupling agent.

[0008] Furthermore, the aromatic rigid skeleton epoxy resin is a bisphenol A type epoxy resin, a bisphenol F type epoxy resin, or a biphenyl type epoxy resin. The aromatic rigid skeleton epoxy resin has an epoxy equivalent index of 180 g / eq to 210 g / eq, and the absolute dynamic viscosity of the aromatic rigid skeleton epoxy resin at 25°C is between 10000 mPa·s and 15000 mPa·s.

[0009] Furthermore, the multifunctional fluorinated epoxy resin is prepared by a nucleophilic substitution reaction between perfluorononenoxyphenyl glycidyl ether and a polyphenol compound; after curing and crosslinking, the multifunctional fluorinated epoxy resin can form a highly branched three-dimensional topological network structure; the absolute mass percentage of fluorine in the multifunctional fluorinated epoxy resin system is in the range of 15% to 25%; and the epoxy equivalent of the multifunctional fluorinated epoxy resin is measured to be 240 g / eq to 280 g / eq.

[0010] Furthermore, the thickness of the micro-sheets of the two-dimensional modified fluorinated graphene powder is distributed between 3 and 8 layers; the two-dimensional layered surface of the two-dimensional modified fluorinated graphene powder is covalently modified by fluorinated alkyl silanes containing terminal amino groups, and the two-dimensional layered surface of the two-dimensional modified fluorinated graphene powder is grafted with fluorinated alkyl segments with a carbon atom number between 8 and 12.

[0011] Furthermore, the zero-dimensional surface fluorinated nano-dielectric filler comprises an inorganic dielectric matrix and a low-polarity halogenated conformal hydrocarbon film coated on the outside of the inorganic dielectric matrix; the inorganic dielectric matrix is ​​selected from amorphous silicon dioxide, aluminum oxide or boron nitride, and the original particle size range of the inorganic dielectric matrix is ​​20 nm to 50 nm.

[0012] Furthermore, the low polarizability halogenated conformal hydrocarbon film is a polytetrafluoroethylene continuous film grown in situ using plasma-enhanced chemical vapor deposition; the absolute thickness tolerance of the low polarizability halogenated conformal hydrocarbon film is controlled between 2 nm and 5 nm.

[0013] Furthermore, the aromatic fluorinated diamine curing agent has the chemical molecular structure of 2,2-bis[4-(4-aminophenoxy)phenyl]hexafluoropropane; the number average molecular weight of the perfluoropolyether modified polysiloxane leveling agent is limited to the range of 3000 g / mol to 5000 g / mol.

[0014] Furthermore, in step 1, the constant temperature and negative pressure conditions are specifically defined as follows: the absolute temperature inside the reaction equipment is maintained in the range of 60°C to 80°C, the absolute vacuum inside the reaction equipment is extracted and limited to below -0.09 MPa, and the continuous execution time of the vacuum devolatilization reaction is 30 min to 50 min.

[0015] Furthermore, in step 2, the high-energy-density physical cross-shear stress field's rotational high-shear speed is set to a threshold of 2000 rpm to 3000 rpm, and the high-intensity dispersion execution cycle is not less than 120 min; the mechanical longitudinal wave frequency applied in the ultrasonic degassing treatment is set to 40 kHz, and the duration of the ultrasonic degassing treatment is 30 min.

[0016] Furthermore, in step 3, the constant low temperature condition is specifically set to 40°C to 50°C, and the duration of the flexible kneading and mixing operation is 20 minutes.

[0017] Furthermore, in step 4, the multi-stage stepped thermodynamic curing process is as follows: baking in a constant temperature air field at 80℃ for 2 hours to perform the gel crosslinking stage; switching to a temperature plateau at 120℃ at a constant heating rate of 1.5℃ / min and staying for 3 hours to perform the high-temperature curing stage; continuing to climb to the extreme plateau at 160℃ at a constant heating rate of 1.5℃ / min and staying for 4 hours to perform the conformational rearrangement stage.

[0018] Furthermore, the two-dimensional layered edges of the two-dimensional modified fluorinated graphene powder are covalently grafted with cage-like octa(trifluoropropyl)silsesquioxane; the rigid cage-like siloxane core of the cage-like octa(trifluoropropyl)silsesquioxane forms a topological anchoring structure with the carboxyl defect sites at the edge of the two-dimensional modified fluorinated graphene powder through amide bonds, and the absolute mass percentage of the cage-like octa(trifluoropropyl)silsesquioxane in the two-dimensional modified fluorinated graphene powder is 8% to 15%.

[0019] Furthermore, after being formed through the multi-stage stepped thermodynamic curing process, the average radius of the microscopic free volume pores inside the insulating material of the fluorocarbon modified polymer insulating joint was determined by positron annihilation lifetime spectroscopy and limited to the range of 0.22 nm to 0.28 nm; the average radius of the microscopic free volume pores... Long-lived components annihilated by positrons It conforms to the following semi-empirical mathematical relation of quantum mechanics: In the mathematical relation, Defined as the annihilation lifetime of positrons formed by positrons in the free volume of a polymer, measured in nanoseconds; Defined as the average radius of a hypothetical spherical free volume cavity, in nm; Defined as an empirical constant for the electron layer thickness of the pore wall, with a value of 0.1656 nm; the relative fraction of free volume inside the insulating material of the molded fluorocarbon modified polymer insulating joint. Strictly below 3.5%.

[0020] In addition, the present invention also discloses a fluorocarbon modified polymer insulating joint, including an insulating joint body, wherein the insulating joint body is made of the above-mentioned fluorocarbon modified polymer insulating material.

[0021] Compared with the prior art, the present invention has the following beneficial effects: This invention fundamentally suppresses the micropore leakage defects induced by phase separation interfaces in traditional physical blending systems by vacuum devolatilizing aromatic rigid-skeletal epoxy resin and multifunctional fluorinated epoxy resin under negative pressure and constant temperature conditions to form a homogeneous resin matrix. Two-dimensional modified fluorinated graphene powder and zero-dimensional surface fluorinated nano-dielectric fillers are introduced into the homogeneous resin matrix, and a high-energy-density physical cross-shear stress field is applied for high-intensity dispersion. Combined with ultrasonic degassing treatment, uniform dispersion and dielectric parameter matching of the nano-reinforced phase in the fluorinated resin matrix are achieved, eliminating local electric field distortion and space charge accumulation channels caused by filler agglomeration.

[0022] This invention employs an aromatic fluorinated diamine curing agent to perform a flexible kneading and mixing process under constant low-temperature conditions, effectively delaying the crosslinking reaction process and ensuring the low initial dynamic viscosity and pouring flowability of the multiphase homogeneous mixture. The multi-stage, step-by-step thermodynamic curing process sequentially undergoes a gel crosslinking stage, a high-temperature curing stage, and a conformational rearrangement stage, resulting in a highly branched three-dimensional topological crosslinking network and a dense free-volume structure within the molded fluorocarbon modified polymer insulating joint insulation material. This significantly improves the material's creep resistance and dielectric stability under high-temperature, high-humidity, and strong electric field coupling conditions.

[0023] Furthermore, the surface of the two-dimensional modified fluorinated graphene powder is covalently grafted with fluorinated alkyl segments and an octa(trifluoropropyl)silsesquioxane edge anchoring structure is introduced, constructing a stacked compressive array and a deep charge trap at the submicron scale. This endows the material with excellent resistance to external mechanical crack propagation and radiation-induced conductivity suppression. Zero-dimensional surface fluorinated nano-dielectric fillers, grown in situ using plasma-enhanced chemical vapor deposition (PECVD) to form low-polarity halogenated conformal hydrocarbon films, smooth out the dielectric constant difference between the inorganic filler and the resin matrix, reducing the power frequency dielectric constant and dielectric loss heating factor. The addition of perfluoropolyether-modified polysiloxane leveling agents forms a surface-enriched physical isolation protective film during the curing stage, enhancing the hydrophobic and salt-repellent properties and volume resistivity retention of the insulating joint insulation material in deep-sea salt spray environments. Attached Figure Description

[0024] To more clearly illustrate the technical solutions of the embodiments of the present invention, the accompanying drawings used in the embodiments will be briefly introduced below. It should be understood that the following drawings only show some embodiments of the present invention and should not be regarded as a limitation of the scope. For those skilled in the art, other related drawings can be obtained from these drawings without creative effort.

[0025] Figure 1 This is a process flow diagram for preparing the fluorocarbon modified polymer insulating material of the present invention.

[0026] Figure 2This is a table of physical and electrical comparison test data for embodiments and comparative examples of the present invention. Detailed Implementation

[0027] In the following description, only certain exemplary embodiments are briefly described. As those skilled in the art will recognize, the described embodiments can be modified in various ways without departing from the spirit or scope of the embodiments of the invention. Therefore, the drawings and description are considered to be exemplary in nature and not restrictive.

[0028] The following is in conjunction with the appendix Figure 1 and Figure 2 The embodiments of the present invention will be described in detail below.

[0029] This invention provides an alternative to the traditional wet chemical coupling modification method for polymers. This method utilizes a long-chain fluoroalkyl silane reagent (e.g., heptadecafluorodecyltrimethoxysilane) to undergo a heated reflux hydrolysis condensation grafting reaction with the active hydroxyl groups on the surface of nano-silica in an anhydrous ethanol system. This method is limited by the steric hindrance effect of the long-chain fluoroalkyl group, making it difficult to form a dense, continuous, and microporous monomolecular fluorinated layer on the surface of nano-silica. Grafting defects result in micro-polarization leaks and sharp electric field distortion points in zero-dimensional nanoparticles under ultra-high voltage electric fields.

[0030] This invention establishes plasma-enhanced chemical vapor deposition (PECVD) as the core implementation path. A high-energy radio frequency electromagnetic field is used to bombard and decompose the octafluorocyclobutane precursor gas into highly reactive free fluorocarbon radicals. These highly reactive free fluorocarbon radicals undergo uniform in-situ polymerization and recombination on the outer surface of an inorganic dielectric substrate, generating a dense and continuous polytetrafluoroethylene-based low-polarity halogenated conformal hydrocarbon film. This process enables uniform thickness growth with absolute thickness control within a tolerance range of 2 nm to 5 nm, fundamentally eliminating grafting porosity defects caused by steric hindrance.

[0031] The analysis of the internal electric field polarization suppression and control model of the insulating material system is as follows. Eliminating the Maxwell-Wagner electromagnetic interface polarization effect at the interface between the inorganic dielectric filler agglomerates and the polymer resin matrix requires achieving precise and consistent dielectric parameters between the inorganic reinforcing dispersed phase and the continuous polymer phase. This invention introduces a mathematical model derived from the Maxwell-Garnett mixing law, clarifying that the effective dielectric constant of the cured insulating material follows the mathematical relationship described above.

[0032] The key input adjustment data for deriving the mathematical model is the thickness parameter of the low-polarity halide conformal hydrocarbon film, precisely controlled by the plasma-enhanced chemical vapor deposition process. Fine-tuning this film thickness parameter can directly influence the equivalent dielectric constant. The final physical output value. The core engineering control objective of the model is to force the input variables... The absolute value approaches the dielectric constant of the resin matrix. The absolute value. Values ​​approaching each other lead to differences in the numerator. The value approaches zero. The model output is directly used to guide the setting of filler volume ratio boundaries and conformal film thickness process tolerances in the industrial manufacturing process of insulating joints.

[0033] Taking the formulation of Example 1 as an example, the dielectric constant of the resin matrix formed after the aromatic rigid skeleton epoxy resin and the multifunctional fluorinated epoxy resin are cross-linked and cured is... The measured value is 2.85. The equivalent dielectric constant of the zero-dimensional surface fluorinated nano-dielectric filler is... The density was adjusted to 2.80 by plasma deposition. When the mass fraction of the zero-dimensional surface fluorinated nano-dielectric filler in the system was 10 parts, the density was based on amorphous silica of 2.2 g / cm³. 3 The density of the resin matrix is ​​1.25 g / cm³. 3 Conversion, geometric fraction of volume It is approximately 0.051. Substituting this into the above mathematical formula, the effective dielectric constant is calculated. Approximately 2.848. This theoretical calculation demonstrates how controlling the coating thickness can achieve... Approaching This makes it feasible to reduce the overall dielectric constant.

[0034] The vacuum casting of large-volume, complex-cavity, irregularly shaped insulating joint components without physical defects relies on the control of fluid rheology and thermodynamic physical models. The dynamic shear viscosity evolution response of the multiphase homogeneous mixture during vacuum casting follows the Arrhenius rheological equation. Perfluoropolyether-modified polysiloxane leveling agent, as a rheological modifier, lowers the lower limit of the rheological pre-exponential factor constant. The multiphase homogeneous mixture exhibits quasi-Newtonian fluid dynamics characteristics within a constant low-temperature range of 40℃ to 50℃. The low-threshold flow activation energy ensures that the high-concentration liquid multiphase homogeneous mixture spontaneously empties and fills the micron-sized latent gas nuclei in the dead corners of the deep-sea insulating joint mold cavity through the weak capillary permeation hydraulic driving force of the hydraulic fluid.

[0035] The insulating joint components continuously withstand axial pipe tensile stress and radial deep-sea water pressure compressive stress throughout their service life. The macroscopic creep resistance assessment model of the molded fluorocarbon modified polymer insulating joint material against microscopic persistent deformation follows the physical formula of high-temperature steady-state creep strain rate. The deep interweaving physical anchoring effect between the microscopic layered intercalation network structure of the two-dimensional modified fluorinated graphene powder and the high-density fluorinated covalent backbone significantly increases the microscopic creep activation energy of the molded insulating material. The constant mechanical stress applied externally is intercepted, dispersed, and converted into elastic deformation potential energy through frictional dissipation by the three-dimensional fluorocarbon topological network.

[0036] In terms of electromagnetic distribution mechanisms, macroscopic phase separation and local dielectric distortion leaks in multiphase resin systems are eliminated. Multifunctional fluorinated epoxy resins and aromatic fluorinated diamine curing agents embed long-chain fluorocarbon components into the center of the epoxy macromolecular backbone through a high-energy covalent bonding reaction. The electron cloud barrier of the carbon-fluorine bond (bond energy approximately 485 kJ / mol) suppresses the high-frequency dipole reversal polarization of the polymer polar chain segments. A low-polarity halogenated conformal hydrocarbon film with dielectric parameters regulated by plasma-enhanced chemical vapor deposition on the surface of zero-dimensional surface fluorinated nano-dielectric fillers achieves equivalent dielectric parameter matching with the surrounding fluorinated resin matrix.

[0037] The effective dielectric constant of the molded insulating material under alternating operating frequencies is reduced to around 2.85, and the power frequency dielectric loss factor is compressed to below 0.005. The deep electron trap structure built inside the material inhibits the transport and accumulation of free space charge, and the average power frequency breakdown voltage remains stable above 35 kV / mm over a long period.

[0038] To elucidate the mechanism of the aforementioned dielectric performance optimization, the overall effective dielectric constant of the molded insulating material can be theoretically estimated using the Maxwell-Garnett mixing rule, and its mathematical relationship is as follows: In the formula, The effective dielectric constant of the overall insulating material of the fluorocarbon modified polymer insulating joint; The dielectric constant of the resin matrix formed after the cross-linking and curing reaction of aromatic rigid skeleton epoxy resin and multifunctional fluorinated epoxy resin; The equivalent dielectric constant of the zero-dimensional surface fluorinated nano-dielectric filler; This represents the volumetric geometric fraction occupied by zero-dimensional surface fluorinated nano-dielectric fillers within a multiphase mixture. The preparation process of these zero-dimensional surface fluorinated nano-dielectric fillers is controlled to achieve their equivalent dielectric constant. With the dielectric constant of the resin matrix By simulating numerical values, the effective dielectric constant of the overall material under an electric field can be effectively reduced. To suppress interface polarization.

[0039] A significant leap has been achieved in thermodynamic dimensional stability and fatigue life. The mechanical locking interface formed between the high-density three-dimensional covalently reconstructed cross-linked network and the two-dimensional modified fluorinated graphene powder enables the two-dimensional fluorinated graphene network architecture to transfer, disperse, and dissipate external mechanical loads. The molded insulating material maintains a long-term steady-state creep strain rate below 0.15% at an ambient temperature of 80°C. The uniform perfluorinated three-dimensional micro-cross-linked structure eliminates the physical density gradient and thermal expansion coefficient mismatch present in traditional insulating joint coating systems. The linear thermal expansion coefficient of the molded insulating material remains within a low threshold range.

[0040] To facilitate a better understanding of the present invention by those skilled in the art, the present invention will be further described below with reference to specific embodiments.

[0041] Example 1: This example discloses the standardized industrial preparation process of insulating materials for fluorocarbon-modified polymer insulating joints used in large-volume rigid insulating support components inside ultra-high voltage direct current (UHVDC) transmission converter stations, as detailed below: Weigh the raw materials for synthesis, and precisely prepare each component according to the absolute weight parts as follows: 70 parts of bisphenol A type epoxy resin (epoxy equivalent measured value is 185 g / eq, absolute dynamic viscosity at 25℃ is 12000 mPa·s); 30 parts of multifunctional fluorinated epoxy resin (fluorine element absolute mass ratio confirmed to be 20%, epoxy equivalent determination value is 260g / eq); 1.5 parts of two-dimensional modified fluorinated graphene powder (microscopic sheet thickness distribution concentrated in the range of 3 to 8 layers); 10 parts of zero-dimensional surface fluorinated nano-dielectric filler (using amorphous silica as the inorganic dielectric matrix, with the original median particle size calibrated to be 30 nm, and the absolute thickness of polytetrafluoroethylene continuous film controlled to be 3 nm). 42 parts of aromatic fluorinated diamine curing agent (2,2-bis[4-(4-aminophenoxy)phenyl]hexafluoropropane powder with a purity higher than 99.5%); 0.5 parts of perfluoropolyether modified polysiloxane leveling agent (number average molecular weight parameter specified as 3500 g / mol); 1.5 parts of silane coupling agent (3-glycidyl etheroxypropyltrimethoxysilane).

[0042] The specific preparation method steps are as follows: Step 1: Vacuum devolatilization and base liquid synthesis.

[0043] Accurately measured bisphenol A epoxy resin and multifunctional fluorinated epoxy resin were introduced into a sealed reaction vessel equipped with a jacketed heat transfer oil circulation heating system. A variable frequency mechanical agitator was activated to steadily raise the absolute temperature of the fluid inside the sealed reaction vessel to 70°C. Simultaneously, a Roots water ring vacuum pump was started to extract and limit the absolute vacuum inside the sealed reaction vessel to -0.095 MPa. Under the dual constraints of constant temperature and negative pressure, the resin mixing system was continuously subjected to high-intensity stirring for 40 minutes. The stirring action, combined with the low-pressure vacuum boiling effect, forcibly desorbed and removed trace amounts of free air and residual polar water molecules dissolved between the polymer resin macromolecular chains, and vented them to the outside of the equipment, resulting in a homogeneous resin base liquid with a visually uniform appearance.

[0044] Step 2: High energy density physical dispersion of multidimensional reinforced powder fillers.

[0045] Pre-weighed two-dimensional modified fluorinated graphene powder and zero-dimensional surface fluorinated nano-dielectric fillers were slowly sieved into a homogeneous resin-based liquid in multiple batches. The initial mixture containing a large amount of powder was transferred to the chamber of an industrial-grade heavy-duty planetary power mixer. The high-shear rotation speed of the heavy-duty planetary power mixer was set to 2500 rpm, and the rotation speed of the frame was set to a stable 40 rpm. The high-energy-density physical cross-shear stress field induced by the high rotation speed forcibly broke the van der Waals adsorption and aggregation bonds between the nano-dielectric particles constructed by electrostatic interactions. The high-intensity dispersion physical operation was carried out continuously for 120 minutes.

[0046] The high-viscosity fluid slurry, after high-intensity dispersion, is pumped into the ultrasonic circulating degassing reaction tank. At an ultrasonic mechanical longitudinal wave frequency of 40 kHz, ultrasonic cavitation and bubble collapse are generated in the fluid inside the tank. The high-speed microjets generated during bubble collapse are used to peel off stubborn micro-gas nuclei hidden and adhered within the micropores of the nano-dielectric filler. The ultrasonic degassing physical treatment process takes 30 minutes.

[0047] Step 3: Low-temperature anti-explosion polymerization process for curing the crosslinking system.

[0048] Implement full UV protection and shading treatment for the mixed operation environment. Activate the industrial dehumidification air conditioning system to force the relative humidity of the working environment to drop below 35%. Slowly and uniformly inject powdered aromatic fluorinated diamine curing agent, liquid perfluoropolyether modified polysiloxane leveling agent, and silane coupling agent sequentially into the ultrasonically degassed fluid slurry. Stabilize the absolute temperature of the mixing reaction equipment at 45°C. Activate the low-shear wide-range propeller agitator and perform a gentle kneading and mixing operation at 150 rpm for 20 minutes.

[0049] The steric hindrance and repulsion effect provided by the hexafluoroisopropyl group within the chemical structure of the aromatic fluorinated diamine curing agent effectively inhibits the premature self-polymerization and crosslinking of highly active crosslinked amino groups in the initial stage of low-temperature mixing. This effect maintains the excellent low initial dynamic viscosity and long-term injection flowability of the multiphase homogeneous mixture from the perspective of molecular dynamics.

[0050] Step 4, stepped thermodynamic curing molding process.

[0051] A multiphase homogeneous mixture is poured into the inner cavity of an ultra-high voltage insulation joint metal mold preheated to 80°C through a sealed vacuum conduit. The filled ultra-high voltage insulation joint metal mold is then automatically conveyed onto a track and pushed into a large hot air circulating oven precisely controlled by a programmable logic controller. A multi-stage, stepped thermodynamic curing temperature control program is then initiated.

[0052] The first stage involves maintaining a constant temperature of 80℃ in a wind field for 2 hours to perform the gel crosslinking stage. The gentle heat induces collisions between polymer reactive groups, causing the reaction chain segments to undergo initial low-speed linear condensation and connection, and gently releasing the exothermic gel crosslinking reaction.

[0053] In the second stage, the oven cavity was switched to a 120℃ medium-temperature platform with a fixed heating rate of 1.5℃ / min, and the oven was forced to remain at this platform for 3 hours to perform a high-temperature curing stage. The medium-temperature energy drove the different polar reactive groups to complete the three-dimensional network crosslinking that evolved into a high-conversion morphology.

[0054] In the third stage, the temperature continues to rise at the same slope of 1.5℃ / min to the ultimate plateau of 160℃, and is held at this plateau for 4 hours to perform a conformational rearrangement stage. The intense thermal motion activates energy to excite violent internal conformational rearrangement of the large macromolecular fluorocarbon chains, releasing and eliminating the residual internal stress caused by the volume shrinkage during the curing of the thick-walled ultra-high voltage component.

[0055] After the curing process is completed, the heating power is automatically cut off. The UHV insulating joint metal mold is cooled slowly to room temperature (25°C) in a hot air circulating oven. The demolding process is then carried out with the assistance of large hydraulic equipment to obtain a final, smooth-surfaced solid sample of the UHV fluorocarbon modified polymer insulating joint insulation material.

[0056] Example 2: Based on the formulation of Example 1, Example 2 is designed to enhance the corrosion resistance of the aforementioned insulating components used in oil and gas energy pipelines laid on the deep seabed, which are subjected to ultra-high deep-sea water pressure forced penetration and long-life-cycle high-concentration salt spray electrochemical corrosion. The formulation ratio of multi-dimensional reinforcing phase and the physical interface isolation control strategy are customized.

[0057] In this embodiment: The weight proportions of the synthetic raw materials are changed as follows: 60 parts of bisphenol A type epoxy resin; 40 parts of multifunctional fluorinated epoxy resin; 0.5 parts of two-dimensional modified fluorinated graphene powder; 15 parts of zero-dimensional surface fluorinated nano-dielectric filler (the thickness of the polytetrafluoroethylene continuous film is controlled at 5 nm); 35 parts of aromatic fluorinated diamine curing agent; 0.8 parts of perfluoropolyether modified polysiloxane leveling agent (the number average molecular weight is adjusted upward to 4500 g / mol); and 2.0 parts of silane coupling agent.

[0058] The preparation method steps of Example 2 are completely consistent with those of Example 1.

[0059] Based on the design objective of maximizing the anti-corrosion and shielding performance in deep-sea applications, Example 2 increased the proportion of multifunctional fluorinated epoxy resin to the upper limit of 40 parts, while simultaneously increasing the amount of zero-dimensional surface fluorinated nano-dielectric filler to 15 parts. This formulation adjustment created a dense, tightly interwoven, physically hydrophobic repulsive labyrinth network structure within the insulating material of the deep-sea insulating joint.

[0060] To mitigate the risk of a surge in viscosity of the homogeneous resin-based liquid caused by ultra-high nanoparticle filler loading, Example 2 utilizes the low surface energy suppression effect imparted by 0.8 parts of a high-dose perfluoropolyether-modified polysiloxane leveling agent to reduce the dynamic surface tension of the high-viscosity multiphase fluid slurry to a lower rheological level. This rheological parameter modification enables the multiphase homogeneous mixture to spontaneously fill the narrow and complex stress-relieving grooves and labyrinthine water-stop sealing tooth gaps inside the metal mold of the deep-sea insulating joint, driven by the capillary permeation force induced by the liquid surface tension.

[0061] During the high-temperature final stage of the multi-stage, stepwise thermodynamic curing process, the free, uncrosslinked perfluoropolyether flexible segments, due to their low surface energy, spontaneously tend to float upwards and migrate towards the external space of the insulating material sample. These segments then undergo in-situ crosslinking and curing at the gas-solid interface of the insulating material sample, forming a physical protective film with water-repellent and chloride ion-blocking properties.

[0062] Example 3: Example 3 is a further optimization based on Example 1. In this example, it is dedicated to addressing the mechanical application scenarios in which key mechanical insulation equipment in heavy-duty rail transit traction substations needs to frequently withstand huge instantaneous mechanical impacts, high-frequency vibration mechanical fatigue, and severe high and low temperature cyclic thermal shocks.

[0063] The following raw materials were weighed for synthesis: 80 parts of bisphenol F type epoxy resin with higher physical rigidity were used to replace bisphenol A type epoxy resin; 20 parts of multifunctional fluorinated epoxy resin; 2.5 parts of two-dimensional modified fluorinated graphene powder; 5 parts of zero-dimensional surface fluorinated nano dielectric filler; 50 parts of aromatic fluorinated diamine curing agent; 0.2 parts of perfluoropolyether modified polysiloxane leveling agent; and 1.0 part of silane coupling agent.

[0064] The preparation method of Example 3 continues the macroscopic logical structure of vacuum devolatilization, slurry mixing, and step-by-step solidification as in Example 1. However, to address the problem of physical agglomeration and dispersion at the phase interface caused by the ultra-high proportion of two-dimensional modified fluorinated graphene powder (reaching the upper limit of 2.5 parts), the physical dispersion stage of step 2 is upgraded as follows: After the initial cross-shearing and agglomeration action of the heavy-duty planetary power mixing equipment and before the ultrasonic degassing process, an additional secondary forced hydraulic dispersion process using an industrial three-roll cryogenic mill is added.

[0065] A viscous fluid slurry containing two-dimensional modified fluorinated graphene sheets is continuously and stably pumped through a three-roll cryogenic mill fluid system, with the mechanical interlocking gap between the three hard cryogenic alloy rollers set at 5 μm. Within this physical channel, the fluid slurry is subjected to mechanical roller pressing and grinding stress as well as fluid flow dynamic shear force. The rolling shear force breaks down the van der Waals adsorption between the two-dimensional nanosheets of the two-dimensional modified fluorinated graphene powder, promoting interlayer parallel sliding and microscopic dissociation of the two-dimensional modified fluorinated graphene nanosheets.

[0066] The fluid-oriented accelerated shear force field generated by the three-roll system forces the exfoliated two-dimensional modified fluorinated graphene nanosheets to conform to the rheological extrusion direction of the resin mixture, forming a microscopic layered array arrangement. This arrangement simulates the compressive strength of staggered laminated blocks at the submicron scale, endowing the molded special fluorocarbon modified polymer insulating joint insulation material samples with resistance to external damage crack propagation and bending mechanical fatigue.

[0067] Example 4: This example mainly addresses the insulation structure of special motors in nuclear power plants and the high-voltage through-wall terminals of deep space probes, dealing with the severe multi-field coupling conditions of high-energy radiation, continuous high temperature, and ultra-high voltage electric fields. High-energy radiation easily breaks the covalent bonds of conventional polymer skeletons, inducing a nonlinear surge in radiation-induced conductivity (RIC), leading to overall thermal breakdown of the material under rated operating voltage.

[0068] To block such physical evolution paths, this embodiment modifies the two-dimensional polarized defense phase into a "zero-dimensional to two-dimensional" multi-level heterogeneous structure.

[0069] The preparation process and formulation parameters are as follows.

[0070] Example 4 introduces cage-like octa(trifluoropropyl)silsesquioxane (F-POSS) into the microstructure of two-dimensional modified fluorinated graphene powder.

[0071] Original graphene oxide with a microsheet thickness of 3 to 5 layers was ultrasonically dispersed in anhydrous... In a dimethylformamide solvent, excess thionyl chloride is added to perform a carboxyl chlorination reaction.

[0072] After removing residual reagents, cage-like octa(trifluoropropyl)silsesquioxane powder with amino-terminated groups was injected into the reaction system, and the mixture was refluxed at 85°C under inert argon atmosphere for 24 h. The amino groups of F-POSS collided with the acyl chloride groups at the edges of graphene at high frequency and formed amide covalent bonds.

[0073] After the reaction, the graphene two-dimensional plane was modified by secondary covalent bonding using fluorinated alkyl silanes containing terminal amino groups after centrifugation and washing. The resulting two-dimensional modified fluorinated graphene powder had densely anchored nanoscale inorganic siloxane rigid cage-like cores at its edges. The absolute mass percentage of F-POSS in the powder was confirmed to be 12% by thermogravimetric analysis.

[0074] The components are as follows, in absolute weight parts: 60 parts of biphenyl-type epoxy resin (epoxy equivalent measured value is 192 g / eq, absolute dynamic viscosity at 25℃ is 13500 mPa·s); 40 parts of a multifunctional fluorinated epoxy resin (epoxy equivalent value of 250 g / eq) synthesized from perfluorononenoxyphenyl glycidyl ether. 2.0 parts of two-dimensional modified fluorinated graphene powder with F-POSS edge grafting; 15 parts of zero-dimensional surface fluorinated nano-dielectric filler (using high thermal conductivity boron nitride as an inorganic dielectric matrix, with an original particle size of 40 nm, and the thickness of a low polarizability halogenated conformal hydrocarbon film grown in situ by plasma-enhanced chemical vapor deposition of octafluorocyclobutane was precisely calibrated to 4 nm). 48 parts of aromatic fluorinated diamine curing agent (2,2-bis[4-(4-aminophenoxy)phenyl]hexafluoropropane); 0.6 parts of perfluoropolyether modified polysiloxane leveling agent with a number average molecular weight of 4500 g / mol; 1.8 parts of silane coupling agent.

[0075] Biphenyl-type epoxy resin and multifunctional fluorinated epoxy resin were placed inside a reaction apparatus. A vacuum devolatilization reaction was continuously performed for 45 min under a vacuum constraint of 80°C and -0.098 MPa. Quantitative amounts of edge-grafted F-POSS-modified fluorinated graphene powder and zero-dimensional surface-fluorinated nano-dielectric fillers were sieved into a homogeneous resin matrix in multiple batches. A heavy-duty planetary mixer was set to a high-shear rotation speed of 2800 rpm, and continuous high-intensity dispersion was achieved for 150 min. The high shear stress field allowed the rigid cage-like structure of F-POSS to fully expand within the liquid resin matrix. The fluid slurry was pumped into an ultrasonic reaction tank and degassed for 30 min at a mechanical longitudinal wave frequency of 40 kHz.

[0076] Maintain the relative humidity of the working environment below 30%. Under constant temperature conditions of 45℃, sequentially inject powdered aromatic fluorinated diamine curing agent, liquid perfluoropolyether modified polysiloxane leveling agent, and silane coupling agent into the ultrasonically degassed fluid slurry. Perform a flexible kneading and mixing operation at 120 rpm for 20 minutes using a wide-width propeller agitator.

[0077] The multiphase homogeneous mixture is vacuum-injected into the inner cavity of an ultra-high voltage insulation component mold preheated to 80°C through a closed pipeline.

[0078] The curing and molding process follows a three-stage stepped thermodynamic procedure: The gel crosslinking stage was performed by maintaining a constant temperature of 80℃ for 2 hours. The temperature was increased to 130℃ at a slope of 1.2℃ / min and held at the platform for 4 hours to perform the high-temperature curing stage; The conformational rearrangement stage was performed by climbing to the 180℃ limit plateau at an extremely low heating rate of 1.0℃ / min and remaining there for 5 hours. The extremely low-slope high-temperature rearrangement provided the fluorocarbon segments and F-POSS rigid cages with sufficient relaxation time to form a thermodynamic cross-linked topology in the lowest energy state.

[0079] Nanoscale free volume probing was performed on molded insulating solid samples using positron annihilation lifetime spectroscopy (PALS). Lifetime data from positron trapped states within the samples revealed long-lifetime components of the positrons. It is extremely compressed to 1.72 ns. Substituting this value into the semi-empirical mathematical relations of quantum mechanics: In the formula, The annihilation lifetime of positrons formed by positrons in the free volume of the polymer is expressed in nanoseconds (ns). The average radius of the assumed spherical free volume cavity is expressed in nm. is an empirical constant for the electron layer thickness of the hole wall, with a value of 0.1656 nm.

[0080] Inverse calculations revealed that the average radius of the microscopic free volume pores inside the material is only 0.24 nm, and the relative free volume fraction... As low as 2.8%. The highly contracted microscopic free volume completely seals off the space for slippage and creep of macromolecular chain segments under the impact of high temperature and high energy radiation.

[0081] A total absorbed dose of 1000 kGy was applied to the sample. Forced irradiation aging with high-energy gamma rays.

[0082] In the measured data after irradiation, the volume resistivity of the material remained stable. Above the insulation safety threshold, the electromagnetic limit of the power frequency insulation breakdown voltage only slightly decreases to 41.2 kV / mm.

[0083] In this embodiment, the leap in radiation resistance and electrical conductivity stems from the F-POSS core structure, an inorganic siloxane rigid cage ( This material exhibits high radiometric transparency and structural rigidity. Its high-density trifluoropropyl segments and highly electronegative carbon-fluorine bonds on the periphery construct a high-density charge trapping network reaching a depth of 1.35 eV within the material. High-energy Compton secondary electrons excited by radiation are instantly and densely trapped and firmly pinned by the microscopic deep traps woven together by F-POSS and two-dimensional graphene during short-range transitions. This mechanism blocks the macroscopic long-range transport avalanche effect of radiation-induced charge at its source.

[0084] Comparative Example 1: Comparative Example 1 provides a traditional general-purpose polymer insulation material formulation system without underlying fluorocarbon physical reconstruction modification.

[0085] The raw material components of Comparative Example 1 were set as follows: 100 parts of bisphenol A type epoxy resin; 80 parts of liquid conventional polar methyltetrahydrophthalic anhydride curing agent; 10 parts of ordinary hydrophilic fumed silica nanoparticles without dielectric matching and surface hydrophobic treatment; and 0.5 parts of conventional industrial dimethyl silicone oil leveling agent. The chemical crosslinking system of Comparative Example 1 lacked multifunctional fluorinated epoxy resin, two-dimensional modified fluorinated graphene powder, and aromatic fluorinated diamine curing agent. The preparation process of Comparative Example 1 excluded the three-stage step-by-step high-temperature post-curing conformational rearrangement process.

[0086] Comparative Example 2: Comparative Example 2 provides an alternative solution for achieving the goal of low polarization modification by using macroscopic physical blending.

[0087] Under the same formulation weight ratio structure and process execution steps as Example 1, Comparative Example 2 replaced the multifunctional fluorinated epoxy resin with covalent chemical reaction capability in Example 1 with an equal weight of ordinary bisphenol A type epoxy resin, and replaced the two-dimensional modified fluorinated graphene powder containing amino-fluorinated alkyl grafted long chains in Example 1 with ordinary hydrophilic graphene nanoparticles without any surface chemical modification. The remaining leveling and coupling components remained completely consistent with those in Example 1.

[0088] A comprehensive ultimate test was conducted on the physical standard test blocks of the insulating materials prepared using the above embodiments and comparative examples. Detailed physical and electrical comparative test data are shown below. Figure 2 .

[0089] Figure 2In the static mechanical load evaluation system, Examples 1 to 3 exhibited advantages in tensile fracture physical strength and three-point bending rigidity physical modulus. Example 3, relying on a high-density physically oriented two-dimensional modified fluorinated graphene array, pushed the tensile fracture physical strength limit to 110.5 MPa and the three-point bending rigidity physical modulus to 6.2 GPa. Comparative Example 1 lacked multi-dimensional rigid three-dimensional network support, resulting in a lower three-point bending rigidity physical modulus and a tendency to yield deformation under gravity-suspended physical loads. Comparative Example 2 employed a physical blending principle, where a physical interface thermodynamic repulsion effect existed between the polar bisphenol A type epoxy resin matrix and the non-polar ordinary hydrophilic graphene. During the volume shrinkage process of resin cross-linking and curing, this effect tore apart the micro-bonding interface, creating physical micro-pore stress concentration defects. After the application of external mechanical load, micro-cracks propagated along the pore network, and the tensile fracture physical strength dropped to 82.3 MPa.

[0090] In the dimension of insulation dielectric electromagnetic properties, under test conditions of 25℃ and alternating frequency of 1 kHz, Comparative Example 1, due to the presence of polar dipoles in the polymer main chain segment, experienced high-frequency reversal, resulting in an effective dielectric constant of 4.15 at power frequency and a power frequency dielectric loss heating factor of 0.0120. Example 2, which introduced a multifunctional fluorinated epoxy resin chemical reconstruction system, anchored polar groups using electronegative electron clouds, reducing the effective dielectric constant at power frequency to 2.85 and compressing the power frequency dielectric loss heating factor to 0.0028. The high-frequency triboelectric heating power under alternating electric fields was reduced. The insulation breakdown voltage electromagnetic limits of Examples 1 to 3 ranged from 38.6 kV / mm to 45.2 kV / mm. Surface-coated fluorinated nano-silica, coated by vapor deposition, filled local microscopic electric field distortion traps, blocking avalanche-type electron avalanche penetration caused by space charge.

[0091] In a creep resistance evaluation conducted under a constant mechanical tensile load of 20 MPa at 80°C for 1000 h, the steady-state creep strain rates of Examples 1 to 3 remained within the range of 0.09% to 0.15%. The steady-state creep strain rate of Comparative Example 1 increased to 0.48%. After a 3000-h high-concentration standard salt spray erosion test, the hydrophobic contact angle of the static deionized water surface of Example 2 remained at 125°, and the volume resistivity retention rate was 98.2%. This corrosion resistance effect is attributed to the low surface energy physical protective isolation layer formed by the surface migration and cross-linking of the perfluoropolyether modified polysiloxane leveling agent during the curing stage. In Comparative Example 1, the microstructure was penetrated by moisture and underwent electrochemical degradation, resulting in a volume resistivity retention rate decrease to 62.4%.

[0092] Test results show that the electromagnetic interaction between the aromatic dual-source fluorinated reconstructed network and the surface-stealth nano-dielectric filler demonstrates the multi-field coupling resistance advantage of the microscopic reconstructed polymer network shaped by the method of this invention. The dielectric stealth physical interface blocks the Maxwell-Wagner charge accumulation electromagnetic channels. The multidimensional mechanical locking physical network blocks macroscopic creep slip dislocation anchor points.

[0093] Although preferred embodiments of the invention have been described, those skilled in the art, upon learning the basic inventive concept, can make other changes and modifications to these embodiments. Therefore, the appended claims are intended to be interpreted as including both the preferred embodiments and all changes and modifications falling within the scope of the invention.

[0094] The above description is merely a preferred embodiment of the present invention and is not intended to limit the present invention. It should be noted that any modifications, equivalent substitutions, and improvements made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A fluorocarbon-modified polymer insulating material, characterized in that, The insulating material is prepared using the following steps: Step 1: Aromatic rigid skeleton epoxy resin and multifunctional fluorinated epoxy resin are put into a reaction device and vacuum devolatilization reaction is performed under constant temperature and negative pressure conditions to prepare a homogeneous resin base liquid. The homogeneous resin base liquid is uniform to the naked eye. Step 2: Add two-dimensional modified fluorinated graphene powder and zero-dimensional surface fluorinated nano-dielectric filler to the homogeneous resin base liquid, apply a high energy density physical cross shear stress field for high-intensity dispersion, and apply ultrasonic degassing treatment to the fluid slurry after high-intensity dispersion. Step 3: Control the working environment to be in a light-proof state and maintain the upper limit of relative humidity not exceeding 40%. Inject aromatic fluorinated diamine curing agent, perfluoropolyether modified polysiloxane leveling agent and silane coupling agent into the fluid slurry that has undergone ultrasonic degassing treatment in sequence. Perform flexible kneading and mixing operation under constant low temperature conditions to obtain a multiphase uniform mixture. Step 4: The multiphase homogeneous mixture is poured into the preheated inner cavity of the insulating joint metal mold and a multi-stage stepped thermodynamic curing process is executed. The multi-stage stepped thermodynamic curing process includes a gel crosslinking stage, a high-temperature curing stage, and a conformational rearrangement stage in sequence. After the multi-stage stepped thermodynamic curing process is completed, a demolding process is performed to obtain the molded fluorocarbon modified polymer insulating joint insulating material.

2. The fluorocarbon modified polymer insulating material according to claim 1, characterized in that, The raw materials for preparation, by absolute weight, include: 60 to 80 parts of aromatic rigid skeleton epoxy resin; 20 to 40 parts of multifunctional fluorinated epoxy resin; 0.5 to 2.5 parts of two-dimensional modified fluorinated graphene powder; 5 to 15 parts of zero-dimensional surface fluorinated nano-dielectric filler; 35 to 50 parts of aromatic fluorinated diamine curing agent; 0.2 to 0.8 parts of perfluoropolyether modified polysiloxane leveling agent; 1.0 to 2.0 parts of silane coupling agent.

3. The fluorocarbon-modified polymer insulating material according to claim 2, characterized in that, The aromatic rigid skeleton epoxy resin is a bisphenol A type epoxy resin, a bisphenol F type epoxy resin, or a biphenyl type epoxy resin. The aromatic rigid skeleton epoxy resin has an epoxy equivalent index of 180 g / eq to 210 g / eq, and the absolute dynamic viscosity of the aromatic rigid skeleton epoxy resin at 25°C is between 10000 mPa·s and 15000 mPa·s.

4. The fluorocarbon modified polymer insulating material according to claim 2, characterized in that, The multifunctional fluorinated epoxy resin is prepared by a nucleophilic substitution reaction between perfluorononenoxyphenyl glycidyl ether and a polyphenol compound; after curing and crosslinking, the multifunctional fluorinated epoxy resin can form a highly branched three-dimensional topological network structure; the absolute mass percentage of fluorine in the multifunctional fluorinated epoxy resin system is in the range of 15% to 25%; and the epoxy equivalent of the multifunctional fluorinated epoxy resin is measured to be 240 g / eq to 280 g / eq.

5. The fluorocarbon modified polymer insulating material according to claim 2, characterized in that, The thickness of the microsheets of the two-dimensional modified fluorinated graphene powder is distributed between 3 and 8 layers; the two-dimensional layered surface of the two-dimensional modified fluorinated graphene powder is covalently modified by fluorinated alkyl silanes containing terminal amino groups, and the two-dimensional layered surface of the two-dimensional modified fluorinated graphene powder is grafted with fluorinated alkyl segments with a carbon atom number between 8 and 12.

6. The fluorocarbon modified polymer insulating material according to claim 2, characterized in that, The zero-dimensional surface fluorinated nano-dielectric filler comprises an inorganic dielectric matrix and a low-polarity halogenated conformal hydrocarbon film coated on the outside of the inorganic dielectric matrix; the inorganic dielectric matrix is ​​selected from amorphous silicon dioxide, aluminum oxide or boron nitride, and the original particle size range of the inorganic dielectric matrix is ​​20 nm to 50 nm.

7. The fluorocarbon modified polymer insulating material according to claim 6, characterized in that, The low polarizability halogenated conformal hydrocarbon film is a polytetrafluoroethylene continuous film grown in situ using plasma-enhanced chemical vapor deposition; the absolute thickness tolerance of the low polarizability halogenated conformal hydrocarbon film is controlled between 2 nm and 5 nm.

8. The fluorocarbon modified polymer insulating material according to claim 2, characterized in that, The aromatic fluorinated diamine curing agent has the chemical molecular structure of 2,2-bis[4-(4-aminophenoxy)phenyl]hexafluoropropane; the number average molecular weight of the perfluoropolyether modified polysiloxane leveling agent is limited to the range of 3000 g / mol to 5000 g / mol.

9. The fluorocarbon modified polymer insulating material according to claim 1, characterized in that, In step 1, the constant temperature and negative pressure conditions are specifically defined as follows: the absolute temperature inside the reaction equipment is maintained in the range of 60°C to 80°C, the absolute vacuum inside the reaction equipment is extracted and limited to below -0.09 MPa, and the continuous execution time of the vacuum devolatilization reaction is 30 min to 50 min.

10. A fluorocarbon-modified polymer insulating joint, characterized in that: It includes an insulating joint body, which is made of a fluorocarbon modified polymer insulating material as described in any one of claims 1-9.

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