High-temperature-resistant and corrosion-resistant cable material for control line and preparation method thereof

Abstract

The invention provides a high-temperature-resistant corrosion-resistant cable material for a control line and a preparation method of the high-temperature-resistant corrosion-resistant cable material, and belongs to the field of metallocene polyolefin materials. The cable material is prepared from the following chemical raw materials: 45 to 65 parts of maleic anhydride grafted metallocene polyolefin, 5 to 10 parts of maleic anhydride grafted polyolefin elastomer, 3 to 6 parts of epoxy group modified polyhedral oligomeric silsesquioxane, 2 to 5 parts of polyether amine, 5 to 10 parts of ion response type core-shell structure sustained release microspheres, 8 to 15 parts of multi-dimensional reinforcement, 15 to 25 parts of halogen-free flame retardant, 0.5 to 1.5 parts of antioxidant and 0.5 to 1.5 parts of processing aid. The chemical raw materials with specific functions are accurately selected, a synergistic effect system is constructed, and meanwhile, the high temperature resistance and corrosion resistance of the cable material for the control line are improved.

Description

Technical Field

[0001] This application relates to the field of metallocene polyolefin materials technology, and in particular to a high-temperature and corrosion-resistant cable material for control lines and its preparation method. Background Technology

[0002] In fields such as industrial automation, petrochemicals, and marine engineering, control lines need to operate in harsh environments such as high temperature (e.g., above 150℃), high humidity, salt spray, and acid and alkali corrosion for extended periods. Traditional cable materials are difficult to meet the requirements for weather resistance and stability.

[0003] Existing technologies primarily improve high-temperature and corrosion resistance through the following methods: using high-temperature resistant polymers such as silicone rubber and polytetrafluoroethylene (PTFE) as insulation layers, but these methods are costly and difficult to process; or improving compatibility with inorganic fillers by grafting maleic anhydride onto polyolefins, but the risk of molecular chain degradation remains under long-term high temperatures; adding metal shielding layers, armor layers, or multi-layer composite sheaths (such as nested PTFE and PVC) can improve mechanical strength and barrier properties, but sacrifices material flexibility and cannot solve the problem of corrosive media penetration; introducing nano-silica, boron nitride, etc., to enhance thermal conductivity, or loading corrosion inhibitors to achieve passive corrosion protection, but uneven filler dispersion can easily lead to local performance defects, and the release of corrosion inhibitors is uncontrollable. In summary, existing technologies have not yet achieved synergistic optimization of high-temperature and corrosion resistance, especially lacking molecular-level active protection mechanisms and efficient heat dissipation networks, making it difficult to meet the long-term use requirements in complex environments. Summary of the Invention

[0004] This application provides a high-temperature and corrosion-resistant cable material for control lines and its preparation method to solve the following technical problem: how to simultaneously improve the high-temperature resistance and corrosion resistance of cable materials for control lines.

[0005] In a first aspect, this application provides a high-temperature and corrosion-resistant cable material for control lines. By weight, the cable material is composed of the following chemical raw materials: maleic anhydride-grafted metallocene polyolefin: 45-65 parts; maleic anhydride-grafted polyolefin elastomer: 5-10 parts; epoxy group-modified cage-type silsesquioxane: 3-6 parts; polyetheramine: 2-5 parts; ion-responsive core-shell structured slow-release microspheres: 5-10 parts; multidimensional reinforcement: 8-15 parts; halogen-free flame retardant: 15-25 parts; antioxidant: 0.5-1.5 parts; and processing aid: 0.5-1.5 parts. The ion-responsive core-shell structure slow-release microspheres are hollow mesoporous silica nanospheres loaded with Schiff base corrosion inhibitors and rare earth ions, and formed by grafting crown ether molecular gates at the pore openings through coordination bonds. The multidimensional reinforcer is a hybrid structure formed by boron nitride nanosheets and triazine-based covalent organic framework nanosheets bridged by a silane coupling agent.

[0006] Optionally, the grafting rate of the maleic anhydride-grafted metallocene polyolefin is 0.8% to 1.5%; The grafting rate of the maleic anhydride-grafted polyolefin elastomer is 1.5% to 2.5%.

[0007] Optionally, the preparation method of the epoxy group-modified cage-like silsesquioxane includes the following steps: Under an inert atmosphere, aminopropylheptyl-cage polysilsesquioxane and γ-(2,3-epoxypropoxy)propyltrimethoxysilane were dissolved in anhydrous toluene and refluxed at 75–85 °C for 20–28 h. After post-treatment, the epoxy group-modified cage silsesquioxane was obtained.

[0008] Optionally, the preparation method of the ion-responsive core-shell structured sustained-release microspheres includes the following steps: S101. Hollow mesoporous silica nanospheres are dispersed in a solvent, and then a mixed solution of Schiff base corrosion inhibitor and rare earth salt is added. The mixture is subjected to ultrasonic impregnation and vacuum rotary evaporation to simultaneously load the corrosion inhibitor and rare earth ions into the cavity of the hollow mesoporous silica nanospheres, thereby obtaining loaded nanospheres. S102. The loaded nanospheres are dispersed in a solvent, and then crown ether and zinc salt are added. The mixture is stirred at 45-55°C for 10-14 hours to graft crown ether molecular gates onto the mesoporous channels through coordination bonds. After post-processing, the ion-responsive core-shell structured sustained-release microspheres are obtained.

[0009] Optionally, the mass ratio of the hollow mesoporous silica nanospheres, the Schiff base corrosion inhibitor, and the rare earth salt is 1:(0.2-0.4):(0.1-0.2). The mass ratio of the hollow mesoporous silica nanospheres, the crown ether, and the zinc salt is 1:(0.1-0.2):(0.05-0.1).

[0010] Optionally, the Schiff base corrosion inhibitor is salicylaldehyde ethylenediamine; The rare earth salt is cerium nitrate hexahydrate; The crown ether is benzo-15-crown ether-5.

[0011] Optionally, the method for preparing the multidimensional reinforcer includes the following steps: S201. Boron nitride nanosheets are dispersed in a solvent, and then γ-aminopropyltriethoxysilane is added. The mixture is reacted at 70-85℃ for 4-6 hours to obtain amino-modified boron nitride nanosheets. S202. The aminated boron nitride nanosheets are redispersed in a solvent, and then a triazine covalent organic framework monomer is added. The mixture is reacted at 75-85°C for 65-75 h to synthesize the multidimensional reinforcer by in-situ interface growth.

[0012] Optionally, the mass ratio of the γ-aminopropyltriethoxysilane to the boron nitride nanosheets is 1:(3-4); The triazine-based covalent organic framework monomer is composed of cyanuric chloride and p-phenylenediamine, wherein the mass ratio of cyanuric chloride to p-phenylenediamine is (1.3-1.5):1; The mass ratio of the triazine-based covalent organic framework monomer to the amino-modified boron nitride nanosheets is (1.5–2):1.

[0013] Optionally, the halogen-free flame retardant is aluminum hydroxide; The antioxidant is a hindered phenolic antioxidant; The processing aid is polyethylene wax.

[0014] Secondly, this application provides a method for preparing a high-temperature and corrosion-resistant cable material for control lines as described in any one of the first aspects, the method comprising the following steps: S301. Maleic anhydride-grafted metallocene polyolefin, maleic anhydride-grafted polyolefin elastomer, epoxy group-modified cage-type silsesquioxane and antioxidant are premixed for 5-15 minutes to obtain a premix. S302. The premix is ​​melt-blended and extruded into granules at 150-180°C using a twin-screw extruder, so that the epoxy groups in the epoxy group-modified cage-type silsesquioxane and the anhydride groups in the maleic anhydride graft polymer undergo a ring-opening reaction under heating conditions to obtain reactive masterbatch. S303. The reactive masterbatch is added to a mixer and plasticized and melted at 160-180°C for 3-8 minutes to obtain a melt. S304. Polyetheramine, ion-responsive core-shell structured slow-release microspheres, multidimensional reinforcement, halogen-free flame retardant and processing aid are added sequentially to the melt, and the mixture is stirred at 170-190°C and 40-80 rpm for 8-15 minutes to allow the polyetheramine to undergo an in-situ amidation reaction with the maleic anhydride groups in the masterbatch to obtain the cable material.

[0015] The technical solutions provided in this application have the following advantages compared with the prior art: This application provides a high-temperature and corrosion-resistant cable material for control lines. By precisely selecting chemical raw materials with specific functions and constructing a synergistic system, the high-temperature resistance and corrosion resistance of the cable material for control lines are improved simultaneously. The specific approach is as follows: In terms of improving high-temperature resistance, the core relies on the structural characteristics and functional complementarity of multiple components: maleic anhydride-grafted metallocene polyolefins, with their linear and regular polyethylene backbone and ordered molecular arrangement, can provide basic heat resistance and structural stability for the material, serving as a matrix to support the overall heat-resistant framework; epoxy-modified cage-like silsesquioxanes contain rigid and thermally stable inorganic silicon-oxygen cages (SiO2). 1.5 )8, can be dispersed in the material as a "molecular-level heat resistance enhancement point", significantly improving the thermal decomposition temperature and high-temperature deformation resistance of the material; in the multidimensional reinforcement, boron nitride nanosheets have extremely high in-plane thermal conductivity, which can build efficient heat conduction pathways inside the material, quickly disperse the local heat generated during cable operation, and avoid high temperature accumulation leading to material degradation, while the rigid aromatic structure of triazine-based covalent organic framework nanosheets itself has excellent thermal stability, which can further enhance the overall high temperature resistance of the material. The three work together to improve the high temperature resistance level from three aspects: "basic heat resistance - enhanced heat resistance - heat dissipation protection".

[0016] In terms of improving corrosion resistance, a dual mechanism of "passive barrier + active protection" is employed: On the one hand, the multidimensional reinforcement consists of boron nitride nanosheets and triazine-based covalent organic framework nanosheets bridged by a silane coupling agent to form a hybrid structure. This structure can construct tortuous nanoscale "maze channels" within the material, significantly extending the passage of water, oxygen, and corrosive ions (such as Cl-). - The penetration path of the corrosive medium is reduced, thus slowing its penetration into the internal metal conductor of the cable and forming a passive corrosion barrier. On the other hand, the ion-responsive core-shell structure slow-release microspheres use hollow mesoporous silica nanospheres as a carrier, loaded with Schiff base corrosion inhibitors and rare earth ions. The pore openings are grafted with crown ether molecular gates through coordination bonds. When a small amount of corrosive medium breaks through the passive barrier, it will trigger the ion recognition function of the crown ether or destroy Zn. 2+ Coordination balance opens the "gate," releasing Schiff base corrosion inhibitors that chelate with metal ions on the surface of the metal conductor to form an organic protective film, while rare earth ions oxidize to form an inorganic passivation film, achieving active corrosion protection at the molecular level. This dual mechanism works together to resist corrosion.

[0017] Meanwhile, some components have the dual function of improving high temperature resistance and corrosion resistance (such as multidimensional reinforcement). The components are compatible with each other at the molecular level, which not only avoids functional conflicts, but also strengthens the overall performance through structural complementarity, ultimately achieving a synergistic improvement of the two core properties. Attached Figure Description

[0018] The accompanying drawings, which are incorporated in and form part of this specification, illustrate embodiments consistent with this application and, together with the description, serve to explain the principles of this application.

[0019] To more clearly illustrate the technical solutions in the embodiments of this application or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, for those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0020] Figure 1 This is a schematic flowchart illustrating the preparation method of the high-temperature and corrosion-resistant cable material for control lines provided in this application embodiment. Detailed Implementation

[0021] To make the objectives, technical solutions, and advantages of the embodiments of this application clearer, the technical solutions of the embodiments of this application will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of this application, not all embodiments. Based on the embodiments of this application, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of this application.

[0022] Unless otherwise specified, all raw materials, reagents, instruments and equipment used in this application can be purchased from the market or prepared by existing methods.

[0023] This application provides a high-temperature and corrosion-resistant cable material for control lines. By weight, the cable material is composed of the following chemical raw materials: maleic anhydride-grafted metallocene polyolefin: 45-65 parts; maleic anhydride-grafted polyolefin elastomer: 5-10 parts; epoxy group-modified cage-type silsesquioxane: 3-6 parts; polyetheramine: 2-5 parts; ion-responsive core-shell structured slow-release microspheres: 5-10 parts; multidimensional reinforcement: 8-15 parts; halogen-free flame retardant: 15-25 parts; antioxidant: 0.5-1.5 parts; and processing aid: 0.5-1.5 parts. The ion-responsive core-shell structure slow-release microspheres are hollow mesoporous silica nanospheres loaded with Schiff base corrosion inhibitors and rare earth ions, and formed by grafting crown ether molecular gates at the pore openings through coordination bonds. The multidimensional reinforcer is a hybrid structure formed by boron nitride nanosheets and triazine-based covalent organic framework nanosheets bridged by a silane coupling agent.

[0024] It should be noted that this application improves both the high-temperature resistance and corrosion resistance of control cable materials by rationally designing the chemical raw materials. Specifically, the functions of each chemical raw material are as follows: Maleic anhydride-grafted metallocene polyolefins: From a molecular structure perspective, they consist of a linear, well-ordered polyethylene backbone formed by a metallocene catalyst, with polar maleic anhydride rings suspended on the sides of the backbone. This well-ordered polyethylene backbone, with its highly ordered molecular arrangement, provides the cable material with fundamental mechanical strength, structural rigidity, and heat resistance, ensuring the material maintains a stable form under normal operating conditions. The maleic anhydride rings on the side chains act as crucial "chemical handles," containing active groups that provide necessary active sites for subsequent chemical reactions with other components, forming an important foundation for constructing the overall molecular network of the material.

[0025] Maleic anhydride-grafted polyolefin elastomers: Their molecular structure is primarily composed of amorphous elastomer segments, on which maleic anhydride groups are grafted. This amorphous segmental structure allows for significant segmental movement under external forces. This movement effectively absorbs and dissipates energy transferred from the outside, thus endowing the cable material with excellent flexibility and impact resistance, preventing direct breakage upon impact. Simultaneously, similar to maleic anhydride-grafted metallocene polyolefins, the grafted maleic anhydride groups can also serve as reaction sites, participating in subsequent cross-linking reactions and promoting the formation of the material's molecular network.

[0026] Polyetheramines, in terms of molecular structure, possess a long-chain polyether backbone. This backbone exhibits good flexibility, providing sufficient space for molecular movement. At both ends of the polyether backbone are highly reactive primary amine groups (-NH2). These primary amine groups can undergo amidation reactions with maleic anhydride-grafted metallocene polyolefins and maleic anhydride-grafted polyolefin elastomers, forming a stable covalent cross-linked network within the material through this chemical reaction. The long-chain polyether backbone acts as a "flexible bridge," firmly connecting the rigid maleic anhydride-grafted metallocene polyolefin segments with the flexible maleic anhydride-grafted polyolefin elastomer segments. This achieves a synergistic improvement in both rigidity and toughness at the molecular level, giving the material sufficient strength while maintaining good flexibility.

[0027] Epoxy group-modified cage-like silsesquioxanes: The molecular structure exhibits a unique core-shell morphology, with the interior composed of (SiO2) groups. 1.5The inorganic silicon dioxide (SiO2) is composed of a rigid, thermally stable cage, which endows the molecule with excellent high-temperature resistance and deformation resistance. The exterior is modified with organic epoxy groups, which have high reactivity and can chemically react with maleic anhydride groups in the matrix material (such as maleic anhydride-grafted metallocene polyolefins and maleic anhydride-grafted polyolefin elastomers) or amino groups in polyetheramines. Through this chemical reaction, this "molecular-level silica" can be firmly anchored to the polymer network through covalent bonds, allowing it to be uniformly dispersed within the material and become nanoscale reinforcing points. These reinforcing points can significantly improve the material's elastic modulus and hardness, while further enhancing its thermal stability and flame retardant properties, providing protection for the cable material in complex environments.

[0028] Multidimensional Reinforcement: This is a hybrid structure formed by silane coupling agents, composed of boron nitride nanosheets and triazine-based covalent organic framework nanosheets. From a molecular structure perspective, the boron nitride nanosheets exhibit a two-dimensional honeycomb structure, composed of alternating boron and nitrogen atoms, similar to graphene, but possessing excellent insulation properties and extremely high in-plane thermal conductivity. The triazine-based covalent organic framework nanosheets are two-dimensional or three-dimensional ordered porous crystalline structures formed by the reversible covalent bonding (such as borate ester bonds and imine bonds) of rigid organic monomers. Their molecules are regularly arranged and possess a large specific surface area and good rigidity. After covalent bridging of the two through silane coupling agents, the boron nitride nanosheets, with their two-dimensional structure and high thermal conductivity, can construct a dominant heat conduction pathway within the material, rapidly transferring heat. The triazine-based covalent organic framework nanosheets, relying on their porous structure and large specific surface area, generate strong physical adsorption and entanglement with the polymer molecular chains, while their rigid framework provides mechanical reinforcement to the material. More importantly, triazine-based covalent organic framework nanosheets can also act as "molecular connecting plates," bridging adjacent boron nitride nanosheets and repairing defects in the heat conduction path caused by uneven dispersion or local breakage of the nanosheets. Ultimately, this forms an efficient and adaptive three-dimensional heat conduction network within the material, while also taking into account the material's insulation and mechanical properties.

[0029] Ion-responsive core-shell structured slow-release microspheres: These microspheres have a relatively complex molecular structure, using hollow mesoporous silica nanospheres as a carrier. Schiff base corrosion inhibitors and rare earth ions are loaded inside the hollow mesopores of the nanospheres; Zn is introduced at the pore openings of the hollow mesoporous silica nanospheres. 2+ Coordination bonds are grafted with crown ether molecules, forming a "molecular gate" structure. The crown ether molecule is a macrocyclic molecule with a specific cavity size, which is crucial for K... + Na + Certain metal ions possess extremely strong host-guest recognition and coordination abilities; Zn 2+Coordination bonds act like "hinges," stably connecting crown ether molecules to the surface of hollow mesoporous silica nanospheres, together forming a delicate "molecular switch." When corrosive ions (such as Cl-) are present in the environment where the cable material is located... - When these corrosive ions react with Zn, 2+ Competition occurs, or when K in the environment + Na + When the concentration increases and the ions coordinate with crown ether molecules, the originally stable coordination equilibrium is disrupted, causing the "molecular gate" at the pore opening to release the internally loaded Schiff base corrosion inhibitors and rare earth ions (such as Ce). 3+ From the perspective of the molecular effects of the released components, Schiff base corrosion inhibitors contain -C=N- groups, which can undergo a strong chelation reaction with metal ions on the surface of metal conductors, forming a dense monomolecular protective film on the metal surface; while Ce... 3+ It will then migrate to the surface of the metal conductor and be oxidized in the air to form CeO2. CeO2 can form a dense passivation film on the metal surface, thus achieving dual active protection of "organic protective film + inorganic passivation film" at the molecular level, effectively preventing the metal conductor from being corroded.

[0030] Meanwhile, the synergistic effects at the molecular level among the components are as follows: (1) Synergistic toughening of “flexible bridges and rigid islands”: This synergistic effect mainly involves maleic anhydride-grafted metallocene polyolefins (rigid segments), maleic anhydride-grafted polyolefin elastomers (flexible segments), polyetheramines (flexible bridges), epoxy-modified cage-like silsesquioxanes (rigid nano-reinforcing points), and multidimensional reinforcements (rigid nano-reinforcing points). When the cable material is subjected to external impact, the impact stress will be uniformly transmitted within the material through the flexible cross-linking bonds formed by the polyetheramine. First, the amorphous segments in the maleic anhydride-grafted polyolefin elastomer will absorb and dissipate some of the impact energy through large-amplitude molecular chain movement, initially mitigating the damage to the material from the impact; when the impact energy causes microcracks to form inside the material and attempt to propagate, the microcracks will encounter the rigid “nano-islands” such as epoxy-modified cage-like silsesquioxanes and multidimensional reinforcements. Because of the strong resistance to deformation of these rigid components, they hinder the propagation of microcracks, forcing them to change their propagation direction, deflect, and branch, thereby increasing the energy required for microcrack propagation. Simultaneously, the long-chain polyether backbone of polyetheramine acts like a "safety rope," undergoing tensile deformation during microcrack propagation to further absorb energy and effectively prevent microcracks from connecting and merging into macroscopic fracture. This molecular design of "flexible chain segment energy dissipation - rigid component crack inhibition - flexible bridge energy absorption" achieves a perfect balance between material strength and toughness, allowing cable materials to possess sufficient load-bearing capacity while also resisting external impacts.

[0031] (2) Synergistic heat resistance of "thermal conductivity highway and thermal stability cornerstone": This synergistic effect is centered on the multidimensional reinforcement (thermal conductivity network builder), epoxy group-modified cage-type silsesquioxane (thermal stability enhancer), and triazine-based covalent organic framework nanosheets (thermal stability aid). During the use of cable materials, the current passing through generates heat, which may lead to local hot spots in the material. Boron nitride nanosheets in the multidimensional reinforcement, with their extremely high in-plane thermal conductivity, construct an efficient "thermal conductivity highway" inside the material, which can quickly conduct the heat generated by local hot spots to various parts of the material and dissipate it, avoiding heat accumulation in local areas. The rapid dissipation of heat can effectively reduce degradation phenomena such as intensified thermal motion of polymer molecular chains and chain segment breakage caused by high temperature. This is to achieve heat resistance protection of the material from a physical level. At the same time, the inorganic silicon-oxygen cage (SiO2) inside the epoxy group-modified cage-type silsesquioxane... 1.5 8 exhibits extremely high thermal stability, resisting decomposition at high temperatures and providing a stable molecular framework for the material. The rigid aromatic structure (containing triazine rings) of the triazine-based covalent organic framework nanosheets also possesses excellent thermal stability, with high intermolecular covalent bond energies that prevent bond breakage at high temperatures. These two components, at the molecular level, increase the thermal decomposition temperature of the entire material system, reducing the damage to the material's molecular structure caused by high temperatures, thus providing chemical-level heat resistance protection. The synergistic effect of physical heat dissipation and chemical heat resistance significantly improves the long-term temperature resistance of the cable material, enabling it to operate stably for extended periods in high-temperature environments.

[0032] (3) Synergistic corrosion protection of "intelligent microcapsules and dense networks": This synergistic mechanism involves ion-responsive core-shell structured slow-release microspheres (intelligent protection implementers), multidimensional reinforcing bodies (dense network builders), and epoxy-modified cage-like silsesquioxanes (dense network facilitators). In the service environment of cable materials, water, oxygen, and corrosive ions (such as Cl-) are present. - Corrosive media such as boron nitride nanosheets and triazine-based covalent organic framework nanosheets, covalently bridged in the multidimensional reinforcement, along with the dispersion of epoxy-modified cage-like silsesquioxanes within the material, collectively construct a tortuous nanoscale "maze-like channel." These channels prolong the penetration path of corrosive media within the material, increasing the resistance to penetration and thus significantly slowing the rate of penetration of water, oxygen, and corrosive media into the metal conductor—a passive corrosion protection for the metal conductor. However, when a few "escaped" corrosive media breach this passive protection and penetrate deep into the material, approaching the metal conductor, corrosive ions in the medium (such as Cl-) can cause corrosion. - or high concentrations of K + Na +This triggers a "molecular switch" mechanism in the ion-responsive core-shell structured slow-release microspheres, opening the crown ether molecular gates at the microsphere pore openings and releasing the internal Schiff base corrosion inhibitor and rare earth ions (Ce). 3+ The released corrosion inhibitors and rare earth ions react rapidly with the surface of the metal conductor at the forefront of the corrosive medium, forming a protective and passivating film. This prevents the corrosive medium from further reacting with the metal, achieving active corrosion protection for the metal conductor. The passive protection of "delayed penetration" and the active protection of "targeted removal" work together to form multiple lines of defense against corrosion, achieving ultimate protection for the metal conductor and extending the service life of the cable.

[0033] (4) Synergistic enhancement of “covalent anchoring and interface maximization”: This synergistic effect encompasses all nanocomponents (epoxy-modified cage-like silsesquioxanes, multidimensional reinforcing agents, and ion-responsive core-shell structured sustained-release microspheres) and matrix components (maleic anhydride-grafted metallocene polyolefins, maleic anhydride-grafted polyolefin elastomers), as well as polyetheramines. Epoxy-modified cage-like silsesquioxanes achieve covalent anchoring with the matrix through covalent reactions between external epoxy groups and maleic anhydride groups or amino groups in the matrix or polyetheramines; multidimensional reinforcing agents achieve covalent bonding with the matrix through bridging by silane coupling agents, forming covalent bonds at one end with boron nitride nanosheets and triazine-based covalent organic framework nanosheets, and reacting with the matrix molecular chains at the other end; active groups (such as hydroxyl groups) that may exist on the surface of ion-responsive core-shell structured sustained-release microspheres can also form coordination or covalent bonds with maleic anhydride groups or amino groups in the matrix or polyetheramines, achieving a strong bond with the matrix. This comprehensive covalent anchoring method ensures a robust molecular interface between the nanocomponents and the matrix, avoiding problems such as nanocomponent aggregation and interface slippage that can occur with simple physical blending. The robust molecular interface allows stress to be efficiently transferred to the nano-reinforcing components when the material is subjected to external forces, fully leveraging their reinforcing effect. Simultaneously, heat can be rapidly transferred between the matrix and the nano-thermal conductive components through the interface, improving the material's thermal conductivity. During corrosion protection, ionic signals can also promptly trigger the response mechanism of the slow-release microspheres through the interface. This "interface maximization" effect brought about by "covalent anchoring" maximizes the nano-effect, allowing the functions of each nanocomponent to be fully utilized, comprehensively improving the overall performance of the cable material.

[0034] (5) Optimized synergy of ion-responsive core-shell structured slow-release microspheres (pH / ion dual response): In this synergistic system, the support is still hollow mesoporous silica nanospheres, and the gating system is the crown ether molecules grafted onto the pore openings of the hollow mesoporous silica nanospheres via coordination bonds. The interior is loaded with Schiff base corrosion inhibitors and rare earth ions (such as Ce). 3+ From the perspective of synergistic molecular interactions, crown ether molecules act on specific ions (such as K+). + Na+ It has a high degree of selective recognition capability, while cable materials are exposed to common corrosive environments such as oceans and salt spray, where K... + Na + The concentration is relatively high. When these corrosive media penetrate into the material, the ion concentration in the environment increases, and crown ether molecules will coordinate with these ions, or Cl in the corrosive media... - With Zn 2+ Competitive coordination occurs, leading to the breakage of the coordination bonds between the crown ether molecular gate and the surface of the hollow mesoporous silica nanospheres. This "gate" opens, releasing the inhibitor. This ionic strength-responsive mechanism precisely adapts to the common corrosive environments of polyolefin cables, ensuring timely release of protective components when needed. Simultaneously, the released Schiff base corrosion inhibitor not only forms a protective film by chelating with metal ions on the surface of the metal conductor through its -C=N- groups, but its molecular structure also exhibits pH-responsive characteristics. When H+ is generated in the environment due to corrosion reactions... + When the pH decreases, Schiff base molecules will capture H+. + It also undergoes a color change, which can serve as a visual indicator of early corrosion, facilitating the timely detection of potential corrosion within the cable; while rare earth ions Ce... 3+ The corrosion virus then migrates to the surface of the metal conductor, where it is oxidized to form a dense CeO2 passivation film, further preventing corrosion. These three elements work synergistically to achieve triple protection: corrosion inhibition, surface passivation, and corrosion indication, making cable corrosion protection more comprehensive and precise.

[0035] (6) Synergistic “Face-to-Face” Covalent Hybridization of Multidimensional Reinforcement: In the multidimensional reinforcement, boron nitride nanosheets and triazine-based covalent organic framework nanosheets achieve “face-to-face” covalent hybridization through a silane coupling agent, forming a “sandwich”-like heterostructure. From the perspective of molecular synergistic effects, in terms of thermal conductivity and insulation performance, the two-dimensional honeycomb structure of boron nitride nanosheets gives them extremely high in-plane thermal conductivity, enabling the construction of efficient in-plane thermal conduction pathways within the material; triazine-based covalent organic framework nanosheets can act as “molecular connecting plates,” bridging adjacent boron nitride nanosheets through covalent bonds, filling the gaps between boron nitride nanosheets, and forming a continuous three-dimensional thermally conductive network. At the same time, the triazine-based covalent organic framework nanosheets and the polyolefin matrix can be tightly bonded through the weak interactions (such as van der Waals forces and hydrogen bonds) between the triazine rings and polymer molecular chains, reducing interfacial thermal resistance and improving heat transfer efficiency. This synergistic effect can quickly dissipate the heat generated during cable operation, preventing heat accumulation that leads to material aging, thereby improving the long-term temperature resistance of polyolefin cables. Meanwhile, both boron nitride nanosheets and triazine-based covalent organic framework nanosheets are materials with excellent insulating properties. Their synergistic effect ensures that the cable material maintains good insulation performance while improving thermal conductivity, meeting the insulation requirements of the cable. In terms of mechanical and barrier properties, the "sandwich"-like heterogeneous structure has excellent rigidity, which can significantly improve the tensile strength and elastic modulus of the material. At the same time, this multi-level structure forms a dense barrier network inside the material, increasing the penetration resistance of water, oxygen, and corrosive media, delaying the penetration of corrosive media into the metal conductor, and further enhancing the corrosion resistance of the cable material, achieving a multi-synergistic improvement in thermal conductivity, insulation, mechanical properties, and barrier properties.

[0036] In some embodiments, the grafting rate of the maleic anhydride-grafted metallocene polyolefin is 0.8% to 1.5%; The grafting rate of the maleic anhydride-grafted polyolefin elastomer is 1.5% to 2.5%.

[0037] For the matrix and toughening phase, the grafting rate of maleic anhydride-grafted metallocene polyolefins is set at 0.8%–1.5%. This range balances the material's rigidity and reactivity: too low a grafting rate leads to insufficient crosslinking sites, affecting the material's strength and compatibility with other components; too high a rate restricts molecular chain movement, reducing the material's toughness. Preparation involves grafting maleic anhydride onto the polyolefin backbone using melt or solution grafting methods, introducing polar groups to provide "anchor points" for subsequent reactions. Maleic anhydride-grafted polyolefin elastomers have a higher grafting rate of 1.5%–2.5%, designed to ensure sufficiently strong chemical bonds between the elastomer and the rigid matrix, effectively transferring stress and preventing interfacial separation to maximize the toughening effect. The preparation principle is similar to the former, except that grafting occurs on the elastomer backbone to improve its compatibility with polar fillers and crosslinking agents.

[0038] In some embodiments, the method for preparing the epoxy-modified cage-like silsesquioxane includes the following steps: Under an inert atmosphere, aminopropylheptyl-cage polysilsesquioxane and γ-(2,3-epoxypropoxy)propyltrimethoxysilane were dissolved in anhydrous toluene and refluxed at 75–85 °C for 20–28 h. After post-treatment, the epoxy group-modified cage silsesquioxane was obtained.

[0039] In the preparation of epoxy-modified cage-like silsesquioxanes, the reaction principle is the ring-opening addition of amino and epoxy groups under an inert atmosphere: the amino group (-NH2) of aminopropylheptyl-cage-like polysilsesquioxane attacks the epoxy ring of γ-(2,3-epoxypropoxy)propyltrimethoxysilane, forming a stable CN bond to achieve epoxy group modification. In this process, the inert atmosphere and anhydrous toluene eliminate interference from water and oxygen, avoiding side reactions such as amino oxidation and epoxy hydrolysis; the reflux reaction at 75–85℃ for 20–28 h ensures a complete reaction and enhances the functionalization degree of POSS; the post-treatment is used to purify the product.

[0040] In some embodiments, the preparation method of the ion-responsive core-shell structured sustained-release microspheres includes the following steps: S101. Hollow mesoporous silica nanospheres are dispersed in a solvent, and then a mixed solution of Schiff base corrosion inhibitor and rare earth salt is added. The mixture is subjected to ultrasonic impregnation and vacuum rotary evaporation to simultaneously load the corrosion inhibitor and rare earth ions into the cavity of the hollow mesoporous silica nanospheres, thereby obtaining loaded nanospheres. S102. The loaded nanospheres are dispersed in a solvent, and then crown ether and zinc salt are added. The mixture is stirred at 45-55°C for 10-14 hours to graft crown ether molecular gates onto the mesoporous channels through coordination bonds. After post-processing, the ion-responsive core-shell structured sustained-release microspheres are obtained.

[0041] In some embodiments, the mass ratio of the hollow mesoporous silica nanospheres, the Schiff base corrosion inhibitor, and the rare earth salt is 1:(0.2-0.4):(0.1-0.2). The mass ratio of the hollow mesoporous silica nanospheres, the crown ether, and the zinc salt is 1:(0.1-0.2):(0.05-0.1).

[0042] In some embodiments, the Schiff base corrosion inhibitor is salicylaldehyde ethylenediamine; The rare earth salt is cerium nitrate hexahydrate; The crown ether is benzo-15-crown ether-5.

[0043] The preparation of ion-responsive core-shell structured sustained-release microspheres involves two steps: S101 utilizes capillary action and hydrogen bonding / electrostatic adsorption to ultrasonically impregnate salicylaldehyde ethylenediamine (a Schiff base corrosion inhibitor) and cerium nitrate hexahydrate (a rare earth salt) into the cavities and mesoporous channels of hollow mesoporous silica nanospheres. Then, high-efficiency loading is achieved by desolvating the solvent through vacuum rotary evaporation. The mass ratio of hollow mesoporous silica nanospheres, Schiff base, and rare earth salt is 1:(0.2~0.4):(0.1~0.2), which can optimize the amount of both and avoid excessive amounts that may cause blockage or agglomeration, ultimately yielding loaded nanospheres. S102 utilizes coordination bonds, with zinc ions acting as a "bridge," coordinating with hydroxyl groups or loadings on the surface of nanospheres at one end and with oxygen atoms within the benzo-15-crown ether-5 (crown ether) molecule at the other end, thus "locking" the crown ether at the pore opening to form a molecular gate. The mass ratio of hollow mesoporous silica nanospheres, crown ether, and zinc salt is 1:(0.1~0.2):(0.05~0.1), which ensures the stability and responsiveness of the "gate." Stirring the reaction at 45~55℃ for 10~14h promotes complete coordination reaction under mild conditions. Post-processing and purification yield the target microspheres.

[0044] In some embodiments, the method for preparing the multidimensional reinforcer includes the following steps: S201. Boron nitride nanosheets are dispersed in a solvent, and then γ-aminopropyltriethoxysilane is added. The mixture is reacted at 70-85℃ for 4-6 hours to obtain amino-modified boron nitride nanosheets. S202. The aminated boron nitride nanosheets are redispersed in a solvent, and then a triazine covalent organic framework monomer is added. The mixture is reacted at 75-85°C for 65-75 h to synthesize the multidimensional reinforcer by in-situ interface growth.

[0045] In some embodiments, the mass ratio of the γ-aminopropyltriethoxysilane to the boron nitride nanosheets is 1:(3-4); The triazine-based covalent organic framework monomer is composed of cyanuric chloride and p-phenylenediamine, wherein the mass ratio of cyanuric chloride to p-phenylenediamine is (1.3-1.5):1; The mass ratio of the triazine-based covalent organic framework monomer to the amino-modified boron nitride nanosheets is (1.5–2):1.

[0046] The preparation of the multidimensional reinforcer also involves two steps: S101 utilizes a silane coupling agent hydrolysis-condensation reaction, where the ethoxy group (-OEt) of γ-aminopropyltriethoxysilane hydrolyzes to generate silanol groups (-SiOH), which then dehydrate and condense with the hydroxyl groups on the surface of boron nitride nanosheets to form stable Si-OB bonds, achieving amination modification. The mass ratio of γ-aminopropyltriethoxysilane to boron nitride nanosheets is 1:(3-4), allowing control of the coupling agent dosage to achieve uniform amination and provide sufficient active sites for subsequent reactions. The reaction is carried out at 70-85℃ for 4-6 hours to ensure complete amination, resulting in amination-reinforced boron nitride. Boron nanosheets; S102, through Schiff base condensation reaction (iminolation reaction), allows triazine-based covalent organic framework monomers composed of cyanuric chloride and p-phenylenediamine (mass ratio 1.3-1.5:1) to be in situ polymerized on the surface of aminated boron nitride nanosheets. The mass ratio of monomer to aminated boron nitride nanosheets is 1.5-2:1, which can control the growth thickness and coverage of COF. The reaction is carried out at 75-85℃ for 65-75h, and the reversible reaction reaches equilibrium through long-term high temperature, forming a COF layer with high crystallinity and stable structure. Finally, a multidimensional reinforcement is obtained through in-situ interface growth method.

[0047] In some embodiments, the halogen-free flame retardant is aluminum hydroxide; The antioxidant is a hindered phenolic antioxidant; The processing aid is polyethylene wax.

[0048] Among the additives, the halogen-free flame retardant aluminum hydroxide absorbs heat when it decomposes under heat, and at the same time releases water of crystallization to dilute flammable gases. The generated alumina also forms a physical barrier on the material surface, isolating oxygen and heat to achieve flame retardancy. Hindered phenolic antioxidants, as free radical scavengers, can preferentially react with active free radicals generated by material aging, interrupting the chain oxidation reaction and delaying material degradation. In the processing aid polyethylene wax, during the processing, the low molecular weight part reduces the melt viscosity to improve fluidity, while the long chain part forms a lubricating film on the material surface, reducing friction and adhesion and improving processing performance.

[0049] Figure 1 This is a schematic flowchart illustrating the preparation method of the high-temperature and corrosion-resistant cable material for control lines provided in this application embodiment.

[0050] Based on a general inventive concept, such as Figure 1 As shown, this application provides a method for preparing a high-temperature and corrosion-resistant cable material for control lines as described in any one of the above claims, the method comprising the following steps: S301. Maleic anhydride-grafted metallocene polyolefin, maleic anhydride-grafted polyolefin elastomer, epoxy group-modified cage-type silsesquioxane and antioxidant are premixed for 5-15 minutes to obtain a premix. S302. The premix is ​​melt-blended and extruded into granules at 150-180°C using a twin-screw extruder, so that the epoxy groups in the epoxy group-modified cage-type silsesquioxane and the anhydride groups in the maleic anhydride graft polymer undergo a ring-opening reaction under heating conditions to obtain reactive masterbatch. S303. The reactive masterbatch is added to a mixer and plasticized and melted at 160-180°C for 3-8 minutes to obtain a melt. S304. Polyetheramine, ion-responsive core-shell structured slow-release microspheres, multidimensional reinforcement, halogen-free flame retardant and processing aid are added sequentially to the melt, and the mixture is stirred at 170-190°C and 40-80 rpm for 8-15 minutes to allow the polyetheramine to undergo an in-situ amidation reaction with the maleic anhydride groups in the masterbatch to obtain the cable material.

[0051] It should be noted that step S301 is the premixing stage, in which maleic anhydride-grafted metallocene polyolefin, maleic anhydride-grafted polyolefin elastomer, epoxy group-modified cage-type silsesquioxane, and antioxidant are premixed for 5 to 15 minutes. Its core function is to achieve preliminary uniform dispersion of the four solid raw materials in an unheated state, so as to avoid local component enrichment or voids during subsequent melt blending. At the same time, adding antioxidants in advance can provide preliminary antioxidant protection for the raw materials before the subsequent heating process, reducing the early oxidative degradation of the raw materials due to contact with air.

[0052] Step S302 is the melt blending and granulation stage. The premix is ​​melt-blended and extruded into granules in a twin-screw extruder at 150-180°C. The purpose is to transform the solid premix into a homogeneous melt through heating, creating conditions for chemical reactions. At the same time, the reactive masterbatch formed by extrusion granulation facilitates rapid plasticization in the subsequent internal mixing process. The key reaction in this step is the ring-opening reaction between the epoxy groups in the epoxy-modified cage-like silsesquioxane and the anhydride groups in the maleic anhydride-grafted metallocene polyolefin and the maleic anhydride-grafted polyolefin elastomer under heating conditions. Through this reaction, the cage-like silsesquioxane is initially covalently grafted onto the polyolefin molecular chain, laying the foundation for the subsequent formation of a stable cross-linked network and improved high-temperature resistance of the material.

[0053] Step S303 is the masterbatch plasticizing and melting stage. The reactive masterbatch is plasticized and melted in a mixer at 160-180°C for 3-8 minutes to obtain a melt. Its main function is to reheat and melt the granular reactive masterbatch into a homogeneous melt with good flowability. This provides a uniform mixing matrix for the subsequent addition of other functional components such as polyetheramine and ion-responsive core-shell structured slow-release microspheres, ensuring that the subsequent components can be dispersed quickly and uniformly.

[0054] Step S304 is the functional component blending and crosslinking stage. Polyetheramine, ion-responsive core-shell structured slow-release microspheres, multidimensional reinforcement, halogen-free flame retardant, and processing aid are added sequentially to the melt. The mixture is blended at 170–190°C and 40–80 rpm for 8–15 minutes. This process serves two purposes: firstly, it ensures that the ion-responsive core-shell structured slow-release microspheres (providing corrosion resistance), multidimensional reinforcement (enhancing high-temperature resistance and mechanical properties), halogen-free flame retardant (enhancing flame retardancy), and processing aid (improving processing flowability) are uniformly dispersed in the melt through appropriate temperature and speed. Secondly, it promotes the key in-situ amidation reaction, where the primary amino groups at both ends of the polyetheramine molecule react with the unreacted maleic anhydride groups in the reactive masterbatch to form stable amide bonds, constructing a covalent crosslinking network of "rigid polyolefin chain-flexible polyether chain". This further enhances the rigidity, toughness, and high-temperature stability of the material, ultimately yielding a cable material with both high-temperature resistance and corrosion resistance.

[0055] In summary, the core advantage of this application lies in the synergistic improvement of the high-temperature resistance and corrosion resistance of cable materials through scientific component design, precise molecular-level synergistic regulation, and reasonable preparation process, while also taking into account mechanical properties, insulation, environmental friendliness, and process practicality. This can be elaborated from four aspects: Firstly, the component design is highly targeted, with comprehensive and precise functional coverage. Raw material selection and proportioning revolve around the core requirements of "high temperature resistance and corrosion resistance": the matrix uses maleic anhydride-grafted metallocene polyolefins and polyolefin elastomers, and the rigidity and reactivity are balanced by optimizing the grafting rate (0.8%–1.5% and 1.5%–2.5%, respectively), laying the foundation for subsequent cross-linking and functional integration; epoxy-modified cage-like silsesquioxanes are anchored to the polymer network as "molecular-level inorganic reinforcing points," simultaneously improving thermal stability and mechanical strength; ion-responsive core-shell structured slow-release microspheres (loaded with salicylic acid)... Ethylenediamine acetal and cerium nitrate hexahydrate (with a benzo-15-crown ether-5 gate at the orifice) achieve intelligent corrosion protection through "corrosion sensing, active release, and dual protection." The pH color change of the Schiff base can also provide early corrosion indication. The multidimensional reinforcement (covalent hybridization of boron nitride nanosheets and triazine COF) balances high thermal conductivity (rapid heat dissipation), high insulation (meeting cable insulation requirements), and barrier properties (delaying the penetration of corrosive media). The functions of each component are complementary and non-conflicting, forming a complete system of "basic performance, core function, and auxiliary protection."

[0056] Secondly, significant molecular-level synergistic effects result in performance improvements far exceeding those of single-component additives. The components are not simply physically mixed, but rather form a synergistic mechanism through chemical bonding or strong interactions: In terms of heat resistance, the "thermal highway" (physical heat dissipation) constructed by the multidimensional reinforcement, combined with the rigid heat-resistant structure (chemical anti-degradation) of the cage-like silsesquioxane and COF, significantly improves long-term temperature resistance; in terms of corrosion resistance, the "nanomaze channel" (passive barrier) formed by the multidimensional reinforcement and cage-like silsesquioxane, combined with the "targeted release protection" (active response) of the intelligent microspheres, constitutes multiple lines of corrosion protection; in terms of mechanics, the "flexible bridge" of polyetheramine connects the rigid matrix and the elastomer, and combined with the "crack-resistant effect" of the nano-reinforcement, achieves a balance between strength and toughness; simultaneously, all nano-components are covalently anchored to the matrix, preventing interfacial slippage, maximizing the nano-effect, and ensuring stable performance of each component.

[0057] Thirdly, the preparation process is reasonable and controllable, taking into account both the sufficiency of the reaction and the stability of the components. A step-by-step process of "premixing-melt granulation-intensive mixing" is adopted: the premixing stage achieves the initial dispersion of raw materials and adds antioxidants in advance to avoid early oxidation; in the melt granulation stage, the cage-like silsesquioxane and the matrix undergo a ring-opening reaction to form a "reactive masterbatch", laying the foundation for subsequent crosslinking; in the intensive mixing stage, polyetheramine (initiating amidation crosslinking) and functional components (microspheres, multidimensional reinforcements, etc.) are added, which not only ensures the full crosslinking reaction (building a stable network) but also avoids the functional components from becoming ineffective due to premature high-temperature treatment (such as damage to the gate structure of microspheres and a decrease in the crystallinity of COF). At the same time, by controlling the temperature (150-190℃) and the rotation speed (40-80rpm), the uniform dispersion of each component is ensured, and the final product has high performance consistency.

[0058] Fourth, it balances environmental protection and practicality, adapting to the application scenarios of control lines. The use of halogen-free aluminum hydroxide flame retardant avoids the release of toxic gases during combustion of traditional halogenated flame retardants, meeting environmental protection requirements; hindered phenolic antioxidants delay material aging and extend cable lifespan; polyethylene wax processing aids improve melt flowability, reduce production difficulty, and are compatible with conventional processing techniques such as cable extrusion; simultaneously, the corrosion indication function of intelligent microspheres and the insulation and thermal conductivity balance of multi-dimensional reinforcements meet the usage requirements of control lines in complex environments (high temperature, high humidity, salt spray) such as industrial and marine environments, satisfying performance indicators while possessing practical application value.

[0059] The present application is further illustrated below with reference to specific embodiments. It should be understood that these embodiments are for illustrative purposes only and are not intended to limit the scope of the application. Experimental methods in the following embodiments that do not specify specific conditions are generally determined according to industry standards. If there is no corresponding industry standard, then common international standards, conventional conditions, or conditions recommended by the manufacturer are followed. Example 1

[0060] This embodiment provides a high-temperature and corrosion-resistant cable material for control lines, which, by weight, comprises the following chemical components: Maleic anhydride-grafted metallocene polyolefin (grafting rate 1.2%): 55 parts; Maleic anhydride-grafted polyolefin elastomer (grafting rate 2.0%): 8 parts; Epoxy group modified cage-like silsesquioxanes: 5 parts; Polyetheramine (model Jeffamine® D230, CAS No. 9046-10-0, purchased from Huntsman Chemicals): 4 parts; Ion-responsive core-shell structured sustained-release microspheres: 8 parts; Multidimensional augmentation: 12 parts; Halogen-free flame retardant (aluminum hydroxide, average particle size 1μm): 20 parts; Antioxidant (hindered phenolic antioxidant 1010, i.e., pentaerythritol tetrakis[β-(3,5-di-tert-butyl-4-hydroxyphenyl)propionate], CAS No. 6683-19-8): 1 part; Processing aid (polyethylene wax, CAS No. 9002-88-4): 1 part.

[0061] The method for preparing the maleic anhydride-grafted metallocene polyolefin includes: 100g of dried metallocene polyethylene (mPE, purchased from ExxonMobil Chemical Company, USA, model 1018CA), 2.0g of maleic anhydride (MAH, CAS No. 108-31-6), 0.2g of dicumyl peroxide (DCP, CAS No. 80-43-3), and 1.5g of styrene (CAS No. 100-42-5) were added to a high-speed mixer and stirred at room temperature for 10-15 minutes until all components were fully contacted and uniformly dispersed to obtain a premix. The premix was then stably fed into a twin-screw extruder via a loss-in-weight feeder for melt grafting reaction. The extruder temperatures were set sequentially as follows: feeding section 150℃, melting section 165℃, reaction section 175℃, homogenization section 170℃, and die head 165℃, with a screw speed of 250 rpm. Under high temperature and strong shear, the material melts and mixes uniformly. DCP decomposes to generate free radicals, which initiate the grafting of MAH onto the mPE molecular chain with the aid of styrene. The molten strip extruded from the die is immediately cooled and shaped in a water bath, and then cut into uniform particles by a pelletizer. Finally, the obtained particles are placed in a vacuum oven at 80°C for 6 hours to completely remove unreacted MAH monomers and volatiles, yielding purified maleic anhydride-grafted metallocene polyethylene (mPE-g-MAH).

[0062] The preparation method of the maleic anhydride-grafted polyolefin elastomer is as follows: 100g of dried polyolefin elastomer (POE, model DowAffinity GA1950, CAS number 26221-73-8), 3.0g of maleic anhydride (MAH), 0.25g of dicumyl peroxide (DCP), and 2.0g of styrene were added to a high-speed mixer and mixed at room temperature for 10-15 minutes until homogeneous to obtain a premix. The premix was fed into a twin-screw extruder through a loss-in-weight feeder, with the following temperatures set: feeding section 140℃, melting section 155℃, reaction section 170℃, homogenization section 165℃, and die head 160℃, and the screw speed 220rpm. Under high temperature and shear, DCP decomposed to generate free radicals, which initiated the grafting of MAH onto the POE molecular chain with the aid of styrene. The molten material was immediately water-cooled and shaped after extrusion through the die, and then pelletized. Finally, the particles were extracted with acetone using a Soxhlet extractor for 8 hours to remove ungrafted monomers, and then vacuum dried at 80°C for 6 hours to obtain maleic anhydride-grafted polyolefin elastomer.

[0063] The method for preparing the epoxy group-modified cage-like silsesquioxane is as follows: Under nitrogen protection, 10 g of aminopropylheptyl-cage-type polysilsesquioxane (CAS No. 444315-15-5, purchased from Shanghai Tengzhun Biotechnology Co., Ltd. AY35817) and 8 g of γ-(2,3-epoxypropoxy)propyltrimethoxysilane (KH-560, CAS No. 2530-83-8) were dissolved in 100 mL of anhydrous toluene and stirred until homogeneous to obtain a mixture. The mixture was placed in an oil bath and refluxed at 80 °C for 24 h. During the reaction, the epoxy group content was monitored every 2 h until the epoxy group content stabilized. After the reaction was completed, the reaction solution was rotary evaporated (temperature 60 °C, vacuum degree -0.09 MPa) to remove the anhydrous toluene. The obtained solid was washed three times with anhydrous ethanol, 50 mL each time, and then dried under vacuum at 80 °C for 8 h to obtain epoxy group-modified cage-type silsesquioxane.

[0064] The preparation method of the ion-responsive core-shell structured sustained-release microspheres is as follows: 10 g of hollow mesoporous silica nanospheres (purchased from Bio-Tech, model CatNo150nm) were dispersed in 150 mL of anhydrous ethanol and sonicated for 30 min (300 W, 40 kHz) to obtain a dispersion. A mixed solution of 3 g of salicylaldehyde ethylenediamine (CAS No. 94-93-9) and 1.5 g of cerium nitrate hexahydrate (solvent: 50 mL anhydrous ethanol) was added to the dispersion. After stirring at room temperature for 2 h, the mixture was heated to 50 °C and sonicated for 4 h (200 W, 40 kHz). The above system was then subjected to rotary evaporation under reduced pressure at 60 °C (vacuum degree -0.09 MPa). After removing anhydrous ethanol, loaded nanospheres were obtained. 10 g of the loaded nanospheres were dispersed in 120 mL of N,N-dimethylformamide, and 1.5 g of benzo-15-crown ether-5 (CAS No. 14098-44-3) and 0.75 g of zinc chloride were added. After stirring evenly, the mixture was placed in an oil bath and the temperature was controlled at 50 °C. The mixture was stirred for 12 h. After the reaction was completed, the mixture was centrifuged (8000 rpm, 15 min) to obtain a solid product. The solid product was washed three times with N,N-dimethylformamide, 50 mL each time, and then vacuum dried at 70 °C for 10 h to obtain ion-responsive core-shell structured sustained-release microspheres.

[0065] The preparation method of the multidimensional reinforcer is as follows: 10g of boron nitride nanosheets (purchased from Xi'an Qiyue Biotechnology, model XT-0803-4-1) were dispersed in 150mL of anhydrous ethanol and sonicated for 40min (power 300W, frequency 40kHz) to obtain a suspension; 3.5g of γ-aminopropyltriethoxysilane (KH-550) was added to the suspension, stirred evenly, and placed in an oil bath at 75℃ for 5h; after the reaction, the mixture was centrifuged (10000rpm, time 20min) to obtain a solid product, washed three times with 50mL of anhydrous ethanol each time, and vacuum dried at 80℃ for 6h to obtain amino-modified boron nitride nanosheets (γ-aminopropyltriethoxysilane to boron nitride nanosheets mass ratio 1:3.5); 10g Aminated boron nitride nanosheets were redispersed in 200 mL of N,N-dimethylformamide and sonicated for 30 min to obtain a dispersion. 17.5 g of a triazine covalent organic framework monomer (composed of 10 g cyanuric chloride (CAS No. 108-77-0) and 7.14 g p-phenylenediamine, with a mass ratio of cyanuric chloride to p-phenylenediamine of 1.4:1) was added to the dispersion. After stirring, the mixture was placed in an oil bath and reacted at 80 °C for 70 h. After the reaction, the mixture was centrifuged (12000 rpm, 25 min) to obtain a solid product, washed four times with 50 mL of N,N-dimethylformamide each time, and vacuum dried at 90 °C for 12 h to obtain a multidimensional reinforcer (triazine covalent organic framework monomer to aminated boron nitride nanosheet mass ratio of 1.75:1).

[0066] Meanwhile, this embodiment provides a method for preparing the above-mentioned high-temperature and corrosion-resistant cable material for control lines, including the following steps: S301. Add 55 parts of maleic anhydride-grafted metallocene polyolefin, 8 parts of maleic anhydride-grafted polyolefin elastomer, 5 parts of epoxy group-modified cage-type silsesquioxane and 1 part of antioxidant to a high-speed mixer (model SHR-10A, purchased from Zhangjiagang Yili Machinery Co., Ltd.), stir and premix at room temperature for 10 min to obtain a uniform premix. S302. The premix is ​​added to a twin-screw extruder (model TE-35, purchased from Nanjing Keya Chemical Equipment Co., Ltd.). The temperatures of each section of the twin-screw extruder are set as follows: Zone 1 150℃, Zone 2 165℃, Zone 3 180℃, and Die Head 175℃. The screw speed is 150 rpm. During the melt blending process, the epoxy groups in the epoxy-modified cage-like silsesquioxane undergo a ring-opening reaction with the anhydride groups in the maleic anhydride-grafted polymer. The molten material is extruded, water-cooled (water temperature 25℃), and pelletized (particle size 3mm) to obtain reactive masterbatch. S303. Add the reactive masterbatch to the internal mixer (model XSM-500, purchased from Shanghai Kechuang Rubber & Plastic Machinery Equipment Co., Ltd.), set the temperature to 170℃, and plasticize and melt for 5 minutes, stirring once every 1 minute (speed 50 rpm) to obtain a melt with good flowability. S304. While the internal mixer is running continuously (60 rpm), add 4 parts of polyetheramine, 8 parts of ion-responsive core-shell structured slow-release microspheres, 12 parts of multidimensional reinforcement, 20 parts of halogen-free flame retardant and 1 part of processing aid to the melt in sequence. Control the internal mixer temperature at 180℃ and mix for 12 minutes. During this period, the polyetheramine undergoes an in-situ amidation reaction with the unreacted maleic anhydride groups in the masterbatch. After the mixing is completed, remove the material, allow it to cool naturally to room temperature (25℃), and pulverize it (particle size 5 mm) to obtain high-temperature and corrosion-resistant cable material for control lines. Example 2

[0067] This embodiment provides a high-temperature and corrosion-resistant cable material for control lines, which, by weight, comprises the following chemical components: Maleic anhydride-grafted metallocene polyolefins (grafting rate 1.1%): 48 parts; Maleic anhydride-grafted polyolefin elastomer (grafting rate 1.9%): 6 parts; Epoxy group modified cage-like silsesquioxanes: 3 parts; Polyetheramine (model Jeffamine® D230): 3 parts; Ion-responsive core-shell structured sustained-release microspheres: 6 parts; Multidimensional augmentation: 10 units; Halogen-free flame retardant (aluminum hydroxide, average particle size 1μm): 18 parts; Antioxidant (hindered phenolic antioxidant 1010): 0.8 parts; Processing aid (polyethylene wax): 0.8 parts.

[0068] The method for preparing the epoxy group-modified cage-like silsesquioxane is as follows: Under nitrogen protection, 10 g of aminopropylheptyl-cage polysilsesquioxane and 7 g of γ-(2,3-epoxypropoxy)propyltrimethoxysilane were dissolved in 90 mL of anhydrous toluene and stirred until homogeneous to obtain a mixture. The mixture was placed in an oil bath and refluxed at 78 °C for 22 h. During the reaction, the epoxy group content was monitored every 2 h until the epoxy group content stabilized. After the reaction was completed, the reaction solution was rotary evaporated (temperature 58 °C, vacuum degree -0.09 MPa) to remove the anhydrous toluene. The obtained solid was washed three times with anhydrous ethanol, 45 mL each time, and then dried under vacuum at 80 °C for 7.5 h to obtain epoxy group modified cage silsesquioxane.

[0069] The preparation method of the ion-responsive core-shell structured sustained-release microspheres is as follows: 10 g of hollow mesoporous silica nanospheres were dispersed in 140 mL of anhydrous ethanol and sonicated for 28 min (300 W, 40 kHz) to obtain a dispersion. A mixed solution of 2.5 g of salicylaldehyde ethylenediamine and 1.2 g of cerium nitrate hexahydrate (45 mL of anhydrous ethanol) was added to the dispersion. After stirring at room temperature for 2.2 h, the mixture was heated to 48 °C and sonicated for 3.8 h (200 W, 40 kHz). The anhydrous ethanol was removed from the system by rotary evaporation under reduced pressure (0.09 MPa) at 58 °C. Loaded nanospheres were obtained. 10 g of the loaded nanospheres were dispersed in 110 mL of N,N-dimethylformamide, and 1.2 g of benzo-15-crown ether-5 and 0.65 g of zinc chloride were added. After stirring evenly, the mixture was placed in an oil bath and the temperature was controlled at 48 °C. The mixture was stirred for 11 h. After the reaction was completed, the mixture was centrifuged (7500 rpm, 14 min) to obtain a solid product. The solid product was washed three times with N,N-dimethylformamide, 45 mL each time, and then dried under vacuum at 70 °C for 9.5 h to obtain ion-responsive core-shell structured sustained-release microspheres.

[0070] The preparation method of the multidimensional reinforcement is as follows: 10g of boron nitride nanosheets are dispersed in 140mL of anhydrous ethanol and ultrasonically treated for 38min (power 300W, frequency 40kHz) to obtain a suspension; 3.2g of γ-aminopropyltriethoxysilane is added to the suspension, stirred evenly, and then placed in an oil bath at 73℃ for 4.5h; after the reaction, the mixture is centrifuged (9500rpm, time 18min) to obtain a solid product, washed three times with 45mL of anhydrous ethanol each time, and vacuum dried at 80℃ for 5.5h to obtain amino-modified boron nitride nanosheets (γ-aminopropyltriethoxysilane to boron nitride nanosheets mass ratio 1:3.1); 10g of amino-modified boron nitride nanosheets are further processed. The nanosheets were redispersed in 190 mL of N,N-dimethylformamide and sonicated for 28 min to obtain a dispersion. 16 g of triazine covalent organic framework monomer (composed of 9.5 g cyanuric chloride and 6.8 g p-phenylenediamine, with a mass ratio of cyanuric chloride to p-phenylenediamine of 1.4:1) was added to the dispersion. After stirring evenly, the mixture was placed in an oil bath and reacted at 78 °C for 68 h. After the reaction was completed, the mixture was centrifuged (11500 rpm, 23 min) to obtain a solid product. The solid product was washed four times with 45 mL of N,N-dimethylformamide each time and dried under vacuum at 90 °C for 11 h to obtain a multidimensional reinforced body (triazine covalent organic framework monomer to amino boron nitride nanosheets mass ratio of 1.6:1).

[0071] Meanwhile, this embodiment provides a method for preparing the above-mentioned high-temperature and corrosion-resistant cable material for control lines, including the following steps: S301. Add 48 parts of maleic anhydride-grafted metallocene polyolefin, 6 parts of maleic anhydride-grafted polyolefin elastomer, 3 parts of epoxy group-modified cage-type silsesquioxane and 0.8 parts of antioxidant to a high-speed mixer and stir and premix at room temperature for 12 minutes to obtain a uniform premix. S302. Add the premix to a twin-screw extruder and set the temperatures of each section of the twin-screw extruder as follows: Zone 1 148℃, Zone 2 162℃, Zone 3 178℃, and Die Head 173℃. Set the screw speed to 140 rpm. During the melt blending process, the epoxy groups in the epoxy-modified cage-like silsesquioxane undergo a ring-opening reaction with the anhydride groups in the maleic anhydride-grafted polymer. The molten material is then extruded, water-cooled (water temperature 25℃), and pelletized (particle size 3mm) to obtain reactive masterbatch. S303. Add the reactive masterbatch to the internal mixer, set the temperature to 168℃, and plasticize and melt for 6 minutes, stirring once every 1 minute during the process (speed 45 rpm) to obtain a melt with good flowability. S304. While the internal mixer is running continuously (50 rpm), add 3 parts of polyetheramine, 6 parts of ion-responsive core-shell structured slow-release microspheres, 10 parts of multidimensional reinforcement, 18 parts of halogen-free flame retardant and 0.8 parts of processing aid to the melt in sequence. Control the internal mixer temperature at 175℃ and mix for 10 minutes. During this period, the polyetheramine undergoes an in-situ amidation reaction with the unreacted maleic anhydride groups in the masterbatch. After the mixing is completed, remove the material, allow it to cool naturally to room temperature (25℃), and pulverize it (particle size 5 mm) to obtain high-temperature and corrosion-resistant cable material for control lines. Example 3

[0072] This embodiment provides a high-temperature and corrosion-resistant cable material for control lines, which, by weight, comprises the following chemical components: Maleic anhydride-grafted metallocene polyolefin (grafting rate 1.4%): 62 parts; Maleic anhydride-grafted polyolefin elastomer (grafting rate 2.1%): 9 parts; Epoxy group modified cage-like silsesquioxanes: 6 parts; Polyetheramine (model Jeffamine® D230): 5 parts; Ion-responsive core-shell structured sustained-release microspheres: 10 parts; Multidimensional augmentation: 14 copies; Halogen-free flame retardant (aluminum hydroxide, average particle size 1μm): 24 parts; Antioxidant (hindered phenolic antioxidant 1010): 1.4 parts; Processing aid (polyethylene wax): 1.4 parts.

[0073] The method for preparing the epoxy group-modified cage-like silsesquioxane is as follows: Under nitrogen protection, 10 g of aminopropylheptyl-cage polysilsesquioxane and 9 g of γ-(2,3-epoxypropoxy)propyltrimethoxysilane were dissolved in 110 mL of anhydrous toluene and stirred until homogeneous to obtain a mixture. The mixture was placed in an oil bath and refluxed at 82 °C for 26 h. During the reaction, the epoxy group content was monitored every 2 h until the epoxy group content stabilized. After the reaction was completed, the reaction solution was rotary evaporated (temperature 62 °C, vacuum degree -0.09 MPa) to remove the anhydrous toluene. The obtained solid was washed three times with anhydrous ethanol, 55 mL each time, and then dried under vacuum at 80 °C for 8.5 h to obtain epoxy group modified cage polysilsesquioxane.

[0074] The preparation method of the ion-responsive core-shell structured sustained-release microspheres is as follows: 10g of hollow mesoporous silica nanospheres are dispersed in 160mL of anhydrous ethanol and ultrasonically treated for 32min (power 300W, frequency 40kHz) to obtain a dispersion; a mixed solution of 3.5g of salicylaldehyde ethylenediamine and 1.8g of cerium nitrate hexahydrate (solvent: 55mL anhydrous ethanol) is added to the dispersion, stirred at room temperature for 1.8h, and then ultrasonically impregnated at 52℃ for 4.2h (power 200W, frequency 40kHz); the above system is then subjected to rotary evaporation under reduced pressure at 62℃ (vacuum degree -0.0). Anhydrous ethanol was removed at 9 MPa to obtain supported nanospheres. 10 g of the supported nanospheres were dispersed in 130 mL of N,N-dimethylformamide, and 1.8 g of benzo-15-crown ether-5 and 0.95 g of zinc chloride were added. After stirring evenly, the mixture was placed in an oil bath and the temperature was controlled at 52 °C. The mixture was stirred for 13 h. After the reaction was completed, the mixture was centrifuged (8500 rpm, 16 min) to obtain a solid product. The solid product was washed three times with 55 mL of N,N-dimethylformamide each time, and then dried under vacuum at 70 °C for 10.5 h to obtain ion-responsive core-shell structured sustained-release microspheres.

[0075] The preparation method of the multidimensional reinforcement is as follows: 10g of boron nitride nanosheets are dispersed in 160mL of anhydrous ethanol and ultrasonically treated for 42min (power 300W, frequency 40kHz) to obtain a suspension; 3.3g of γ-aminopropyltriethoxysilane is added to the suspension, stirred evenly, and then placed in an oil bath at 77℃ for 5.5h; after the reaction, the mixture is centrifuged (10500rpm, time 22min) to obtain a solid product, washed three times with 55mL of anhydrous ethanol each time, and vacuum dried at 80℃ for 6.5h to obtain amino-modified boron nitride nanosheets (γ-aminopropyltriethoxysilane to boron nitride nanosheets mass ratio 1:3); 10g of amino-modified boron nitride nanosheets The product was redispersed in 210 mL of N,N-dimethylformamide and sonicated for 32 min to obtain a dispersion. 19 g of triazine covalent organic framework monomer (composed of 10.5 g cyanuric chloride and 7.5 g p-phenylenediamine, with a mass ratio of cyanuric chloride to p-phenylenediamine of 1.4:1) was added to the dispersion. After stirring evenly, the mixture was placed in an oil bath and reacted at 82 °C for 72 h. After the reaction was completed, the product was centrifuged (12500 rpm, 27 min) to obtain a solid product. The solid product was washed four times with 55 mL of N,N-dimethylformamide each time and dried under vacuum at 90 °C for 13 h to obtain a multidimensional reinforced body (triazine covalent organic framework monomer to amino boron nitride nanosheets in a mass ratio of 1.9:1).

[0076] Meanwhile, this embodiment provides a method for preparing the above-mentioned high-temperature and corrosion-resistant cable material for control lines, including the following steps: S301. Add 62 parts of maleic anhydride-grafted metallocene polyolefin, 9 parts of maleic anhydride-grafted polyolefin elastomer, 6 parts of epoxy group-modified cage-type silsesquioxane and 1.4 parts of antioxidant to a high-speed mixer and stir and premix at room temperature for 15 minutes to obtain a uniform premix. S302. Add the premix to a twin-screw extruder and set the temperatures of each section of the twin-screw extruder as follows: Zone 1 152℃, Zone 2 168℃, Zone 3 182℃, and Die Head 177℃. Set the screw speed to 160 rpm. During the melt blending process, the epoxy groups in the epoxy-modified cage-like silsesquioxane undergo a ring-opening reaction with the anhydride groups in the maleic anhydride-grafted polymer. The molten material is then extruded, water-cooled (water temperature 25℃), and pelletized (particle size 3mm) to obtain reactive masterbatch. S303. Add the reactive masterbatch to the internal mixer, set the temperature to 172℃, and plasticize and melt for 8 minutes, stirring once every 1 minute during the process (speed 55 rpm) to obtain a melt with good flowability. S304. While the internal mixer is running continuously (70 rpm), 5 parts of polyetheramine, 10 parts of ion-responsive core-shell structured slow-release microspheres, 14 parts of multidimensional reinforcement, 24 parts of halogen-free flame retardant, and 1.4 parts of processing aid are added to the melt in sequence. The internal mixer temperature is controlled at 185℃, and the mixture is mixed for 14 minutes. During this period, the polyetheramine undergoes an in-situ amidation reaction with the unreacted maleic anhydride groups in the masterbatch. After the mixing is completed, the material is taken out, naturally cooled to room temperature (25℃), and pulverized (particle size 5 mm) to obtain high-temperature and corrosion-resistant cable material for control lines.

[0077] Comparative Example 1 This comparative example is modified from the one disclosed in Example 1 as follows: The chemical composition of the cable material does not contain epoxy group-modified cage-type silsesquioxanes.

[0078] Comparative Example 2 This comparative example is modified from the one disclosed in Example 1 as follows: The chemical composition of the cable material does not contain polyetheramine.

[0079] Comparative Example 3 This comparative example is modified from the one disclosed in Example 1 as follows: The chemical composition of the cable material does not contain ion-responsive core-shell structured slow-release microspheres.

[0080] Comparative Example 4 This comparative example is modified from the one disclosed in Example 1 as follows: The chemical composition of the cable material does not contain multidimensional reinforcements.

[0081] Comparative Example 5 This comparative example is modified from the one disclosed in Example 1 as follows: Replace the maleic anhydride-grafted metallocene polyolefins and maleic anhydride-grafted polyolefin elastomers with the same number of ungrafted ordinary metallocene polyethylenes and ordinary polyolefin elastomers.

[0082] The cable materials obtained in Examples 1-3 and Comparative Examples 1-5 were subjected to performance testing, and the results are shown in Tables 1-4. The specific performance testing methods are as follows: (1) Mechanical properties: Tensile strength and elongation at break: determined by a universal tensile testing machine according to standard ASTM D 638. Impact strength: determined by a cantilever beam impact testing machine according to standard ASTM D 256.

[0083] (2) Thermal properties: Heat distortion temperature (HDT): determined according to standard ASTM D 648 (load 1.82 MPa). Thermal stability: using a thermogravimetric analyzer (TGA) under nitrogen atmosphere, the temperature was increased from 50 °C to 800 °C at a rate of 10 °C / min, and the 5% thermogravimetric temperature (T5%) was recorded.

[0084] (3) Flame retardant properties: Limiting oxygen index (LOI): determined according to standard ASTM D 2863. Vertical burning (UL-94): tested and rated according to standard ASTM D 3801.

[0085] (4) Corrosion resistance: Salt spray test: According to standard ASTMB 117, place the copper conductor coated with this material in a 5% NaCl salt spray chamber and record the time when the conductor surface shows corrosion.

[0086] Table 1 Mechanical properties of cable materials in Examples 1-3 and Comparative Examples 1-5

[0087] Table 2 Thermal properties of cable materials in Examples 1-3 and Comparative Examples 1-5

[0088] Table 3 Flame retardant properties of cable materials in Examples 1-3 and Comparative Examples 1-5

[0089] Table 4. Corrosion resistance of cable materials in Examples 1-3 and Comparative Examples 1-5

[0090] As shown in Tables 1-4, the cable materials of Examples 1-3 exhibit excellent comprehensive performance. In terms of mechanical properties, the initial tensile strength is 23.4-26.5 MPa, the elongation at break is 403-424%, and the impact strength is 58.3-66.1 kJ / m. 2 It possesses both high strength and good toughness; in terms of thermal properties, the heat distortion temperature (HDT) is 108-112℃, and the 5% thermal weight loss temperature (T5%) is 398-413℃, exhibiting good heat resistance and thermal stability; in terms of flame retardancy, the limiting oxygen index (LOI) is 32.2-34.1%, and the UL-94 rating reaches V-0, demonstrating excellent flame retardant effect; in terms of corrosion resistance, the salt spray resistance time exceeds 1800h, with Example 3 exceeding 2200h, demonstrating excellent long-term corrosion resistance.

[0091] Test results show that the cable materials provided in Examples 1-3 of this application, based on maleic anhydride-grafted metallocene polyolefins and polyolefin elastomers as the matrix, with epoxy group-modified cage-type silsesquioxanes providing molecular-level reinforcement and flame retardant synergy, polyetheramine constructing a flexible covalent cross-linked network, ion-responsive core-shell structure slow-release microspheres achieving active corrosion protection, and multidimensional reinforcement forming a highly efficient thermal conductivity and barrier network, achieve a good balance in mechanical, heat resistance, flame retardant and corrosion resistance properties through the synergistic effect of each component, and can better meet the requirements of control line cable sheath materials in high temperature, humid and highly corrosive environments.

[0092] Comparative Example 1 (ion-deficient responsive core-shell structured sustained-release microspheres) showed significantly inferior performance compared to the Example. In terms of mechanical properties, the tensile strength decreased to 20.5 MPa, the elongation at break decreased to 384%, and the impact strength decreased to 49.3 kJ / m². 2 In terms of thermal performance, HDT decreased to 98℃ and T5% decreased to 385℃; in terms of flame retardancy, LOI decreased to 30.5% and UL-94 rating decreased to V-1; in terms of corrosion resistance, salt spray resistance time decreased to below 1800h. This is because the ion-responsive core-shell structure slow-release microspheres were missing, resulting in the loss of the intelligent release and synergistic passivation effect of Schiff base and cerium ions. The system now relies solely on the passive barrier of the multidimensional reinforcement, leading to accelerated penetration of corrosive media and a significant shortening of corrosion protection life. Simultaneously, the nano-reinforcement and flame-retardant synergistic effect of the microspheres in the matrix disappeared, causing varying degrees of decline in mechanical properties, thermal stability, and flame retardancy.

[0093] Comparative Example 2 (lacking multidimensional reinforcement) showed a significant performance decline. In terms of mechanical properties, tensile strength decreased to 17.2 MPa, elongation at break decreased to 323%, and impact strength decreased to 38.5 kJ / m. 2In terms of thermal performance, the HDT dropped to 95°C; in terms of flame retardancy, the LOI dropped to 32.4%, although it still maintained the V-0 rating, it was lower than in the previous example; in terms of corrosion resistance, the salt spray resistance time dropped to below 1700 hours. This is because the multidimensional reinforcement was missing, making it impossible to construct an efficient three-dimensional thermal conductivity and barrier network. Heat transfer was difficult, increasing the risk of localized overheating and increasing the penetration pathways of corrosive media. Furthermore, the nano-reinforcing effect of the reinforcement itself disappeared, leading to a significant deterioration in mechanical properties, especially a severe loss of toughness.

[0094] The performance of Comparative Example 3 (a cage-like silsesquioxane lacking epoxy group modification) declined significantly. In terms of mechanical properties, the tensile strength decreased to 24.1 MPa, and the impact strength decreased to 60.4 kJ / m². 2 In terms of thermal properties, HDT drops to 110℃ and T5% drops to 402℃; in terms of corrosion resistance, the salt spray resistance time drops sharply to below 1000h. This is because the epoxy POSS is missing, losing its molecular-level rigidity enhancement and flame-retardant synergistic effect, resulting in decreased material rigidity and thermal stability. Simultaneously, the ring-opening reaction between epoxy groups and anhydride groups decreases, the matrix crosslinking density decreases, and the interfacial bonding force weakens, adversely affecting both mechanical and corrosion resistance properties.

[0095] Comparative Example 4 (lacking polyetheramine) showed significantly worse performance. In terms of mechanical properties, tensile strength decreased to 21.5 MPa, elongation at break decreased to 395%, and impact strength decreased to 52.3 kJ / m. 2 In terms of thermal properties, HDT decreased to 102℃ and T5% decreased to 395℃; in terms of flame retardancy, LOI decreased to 32.8%; and in terms of corrosion resistance, salt spray resistance time decreased to below 1900 hours. This is because the absence of polyetheramine prevents the formation of a covalently cross-linked network of "rigid chains-flexible chains," resulting in a significant decrease in material toughness and a weakening of stress transmission and dissipation capabilities. Simultaneously, reduced interfacial compatibility between components leads to a decline in mechanical properties, thermal stability, and corrosion resistance.

[0096] Comparative Example 5 (using ungrafted polymer) exhibited the worst performance across all categories. In terms of mechanical properties, its tensile strength was only 14.9 MPa, elongation at break was only 281%, and impact strength was only 30.1 kJ / m². 2In terms of thermal properties, the HDT is only 88℃, and the T5% is only 377℃; in terms of flame retardancy, the LOI is only 27.5%, failing to pass the UL-94 rating; in terms of corrosion resistance, the salt spray resistance time is only about 1200 hours. The reason lies in the use of ungrafted ordinary polymers, resulting in a system that degenerates into a simple physical blend. The components lack chemical bonds, have extremely poor interfacial compatibility, and suffer from severe stress concentration, leading to a collapse in mechanical properties. Simultaneously, the nanofillers agglomerate because they cannot effectively bind to the matrix, failing to provide reinforcement and instead becoming defects, further deteriorating the material's overall performance.

[0097] Various embodiments of this application may exist in the form of a range; it should be understood that the description in the form of a range is merely for convenience and brevity and should not be construed as a hard limitation on the scope of this application; therefore, it should be considered that the range description has specifically disclosed all possible sub-ranges and single numerical values ​​within that range. For example, it should be considered that the range description from 1 to 6 has specifically disclosed sub-ranges such as from 1 to 3, from 1 to 4, from 1 to 5, from 2 to 4, from 2 to 6, from 3 to 6, etc., and single numbers within the range, such as 1, 2, 3, 4, 5, and 6, regardless of the range. Furthermore, whenever a numerical range is referred to herein, it means including any referenced number (fraction or integer) within the referred range.

[0098] The above description is merely a specific embodiment of this application, enabling those skilled in the art to understand or implement this application. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the general principles defined herein may be implemented in other embodiments without departing from the spirit or scope of this application. Therefore, this application is not to be limited to the embodiments shown herein, but is to be accorded the widest scope consistent with the principles and novel features claimed herein.

Claims

1. A high-temperature and corrosion-resistant cable material for control lines, characterized in that, By weight, the cable material is composed of the following chemical raw materials: maleic anhydride-grafted metallocene polyolefin: 45-65 parts; maleic anhydride-grafted polyolefin elastomer: 5-10 parts; epoxy group-modified cage-type silsesquioxane: 3-6 parts; polyetheramine: 2-5 parts; ion-responsive core-shell structured slow-release microspheres: 5-10 parts; multidimensional reinforcement: 8-15 parts; halogen-free flame retardant: 15-25 parts; antioxidant: 0.5-1.5 parts; processing aid: 0.5-1.5 parts. The ion-responsive core-shell structure slow-release microspheres are hollow mesoporous silica nanospheres loaded with Schiff base corrosion inhibitors and rare earth ions, and formed by grafting crown ether molecular gates at the pore openings through coordination bonds. The multidimensional reinforcer is a hybrid structure formed by boron nitride nanosheets and triazine-based covalent organic framework nanosheets bridged by a silane coupling agent.

2. The high-temperature and corrosion-resistant cable material for control lines according to claim 1, characterized in that, The grafting rate of the maleic anhydride-grafted metallocene polyolefin is 0.8% to 1.5%. The grafting rate of the maleic anhydride-grafted polyolefin elastomer is 1.5% to 2.5%.

3. The high-temperature and corrosion-resistant cable material for control lines according to claim 1, characterized in that, The preparation method of the epoxy group-modified cage-type silsesquioxane includes the following steps: Under an inert atmosphere, aminopropylheptyl-cage polysilsesquioxane and γ-(2,3-epoxypropoxy)propyltrimethoxysilane were dissolved in anhydrous toluene and refluxed at 75–85 °C for 20–28 h. After post-treatment, the epoxy group-modified cage silsesquioxane was obtained.

4. The high-temperature and corrosion-resistant cable material for control lines according to claim 1, characterized in that, The preparation method of the ion-responsive core-shell structured sustained-release microspheres includes the following steps: S101. Hollow mesoporous silica nanospheres are dispersed in a solvent, and then a mixed solution of Schiff base corrosion inhibitor and rare earth salt is added. The mixture is subjected to ultrasonic impregnation and vacuum rotary evaporation to simultaneously load the corrosion inhibitor and rare earth ions into the cavity of the hollow mesoporous silica nanospheres, thereby obtaining loaded nanospheres. S102. The loaded nanospheres are dispersed in a solvent, and then crown ether and zinc salt are added. The mixture is stirred at 45-55°C for 10-14 hours to graft crown ether molecular gates onto the mesoporous channels through coordination bonds. After post-processing, the ion-responsive core-shell structured sustained-release microspheres are obtained.

5. The high-temperature and corrosion-resistant cable material for control lines according to claim 4, characterized in that, The mass ratio of the hollow mesoporous silica nanospheres, the Schiff base corrosion inhibitor, and the rare earth salt is 1:(0.2-0.4):(0.1-0.2). The mass ratio of the hollow mesoporous silica nanospheres, the crown ether, and the zinc salt is 1:(0.1-0.2):(0.05-0.1).

6. The high-temperature and corrosion-resistant cable material for control lines according to claim 5, characterized in that, The Schiff base corrosion inhibitor is salicylaldehyde ethylenediamine; The rare earth salt is cerium nitrate hexahydrate; The crown ether is benzo-15-crown ether-5.

7. The high-temperature and corrosion-resistant cable material for control lines according to claim 1, characterized in that, The method for preparing the multidimensional reinforcer includes the following steps: S201. Boron nitride nanosheets are dispersed in a solvent, and then γ-aminopropyltriethoxysilane is added. The mixture is reacted at 70-85℃ for 4-6 hours to obtain amino-modified boron nitride nanosheets. S202. The aminated boron nitride nanosheets are redispersed in a solvent, and then a triazine covalent organic framework monomer is added. The mixture is reacted at 75-85°C for 65-75 h to synthesize the multidimensional reinforcer by in-situ interface growth.

8. The high-temperature and corrosion-resistant cable material for control lines according to claim 7, characterized in that, The mass ratio of the γ-aminopropyltriethoxysilane to the boron nitride nanosheets is 1:(3-4); The triazine-based covalent organic framework monomer is composed of cyanuric chloride and p-phenylenediamine, wherein the mass ratio of cyanuric chloride to p-phenylenediamine is (1.3-1.5):1; The mass ratio of the triazine-based covalent organic framework monomer to the amino-modified boron nitride nanosheets is (1.5–2):

1.

9. The high-temperature and corrosion-resistant cable material for control lines according to claim 1, characterized in that, The halogen-free flame retardant is aluminum hydroxide; The antioxidant is a hindered phenolic antioxidant; The processing aid is polyethylene wax.

10. A method for preparing a high-temperature and corrosion-resistant cable material for control lines according to any one of claims 1 to 9, characterized in that, The method includes the following steps: S301. Maleic anhydride-grafted metallocene polyolefin, maleic anhydride-grafted polyolefin elastomer, epoxy group-modified cage-type silsesquioxane and antioxidant are premixed for 5-15 minutes to obtain a premix. S302. The premix is ​​melt-blended and extruded into granules at 150-180°C using a twin-screw extruder, so that the epoxy groups in the epoxy group-modified cage-type silsesquioxane and the anhydride groups in the maleic anhydride graft polymer undergo a ring-opening reaction under heating conditions to obtain reactive masterbatch. S303. The reactive masterbatch is added to a mixer and plasticized and melted at 160-180°C for 3-8 minutes to obtain a melt. S304. Polyetheramine, ion-responsive core-shell structured slow-release microspheres, multidimensional reinforcement, halogen-free flame retardant and processing aid are added sequentially to the melt, and the mixture is stirred at 170-190°C and 40-80 rpm for 8-15 minutes to allow the polyetheramine to undergo an in-situ amidation reaction with the maleic anhydride groups in the masterbatch to obtain the cable material.

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