WO2019105413A1 - 一种聚酯复合材料及其制备方法 - Google Patents

一种聚酯复合材料及其制备方法 Download PDF

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WO2019105413A1
WO2019105413A1 PCT/CN2018/118179 CN2018118179W WO2019105413A1 WO 2019105413 A1 WO2019105413 A1 WO 2019105413A1 CN 2018118179 W CN2018118179 W CN 2018118179W WO 2019105413 A1 WO2019105413 A1 WO 2019105413A1
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parts
vinyl acetate
melt
chain extender
weight
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PCT/CN2018/118179
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English (en)
French (fr)
Inventor
马丕明
吴保钩
操莹
东为富
钮德宇
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江南大学
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Priority claimed from CN201711251368.5A external-priority patent/CN109867917B/zh
Priority claimed from CN201711252299.XA external-priority patent/CN109867918B/zh
Priority claimed from CN201811344797.1A external-priority patent/CN111004476B/zh
Priority claimed from CN201811345231.0A external-priority patent/CN111004478B/zh
Priority claimed from CN201811345199.6A external-priority patent/CN111004477B/zh
Application filed by 江南大学 filed Critical 江南大学
Publication of WO2019105413A1 publication Critical patent/WO2019105413A1/zh
Priority to US16/886,869 priority Critical patent/US11591465B2/en

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    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G63/00—Macromolecular compounds obtained by reactions forming a carboxylic ester link in the main chain of the macromolecule
    • C08G63/02—Polyesters derived from hydroxycarboxylic acids or from polycarboxylic acids and polyhydroxy compounds
    • C08G63/12—Polyesters derived from hydroxycarboxylic acids or from polycarboxylic acids and polyhydroxy compounds derived from polycarboxylic acids and polyhydroxy compounds
    • C08G63/16—Dicarboxylic acids and dihydroxy compounds
    • C08G63/18—Dicarboxylic acids and dihydroxy compounds the acids or hydroxy compounds containing carbocyclic rings
    • C08G63/181—Acids containing aromatic rings
    • C08G63/183—Terephthalic acids
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J3/00—Processes of treating or compounding macromolecular substances
    • C08J3/20—Compounding polymers with additives, e.g. colouring
    • C08J3/201—Pre-melted polymers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J3/00—Processes of treating or compounding macromolecular substances
    • C08J3/20—Compounding polymers with additives, e.g. colouring
    • C08J3/203—Solid polymers with solid and/or liquid additives
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
    • C08K3/00—Use of inorganic substances as compounding ingredients
    • C08K3/18—Oxygen-containing compounds, e.g. metal carbonyls
    • C08K3/20—Oxides; Hydroxides
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
    • C08K5/00—Use of organic ingredients
    • C08K5/04—Oxygen-containing compounds
    • C08K5/15—Heterocyclic compounds having oxygen in the ring
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L23/00—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers
    • C08L23/02—Compositions of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Compositions of derivatives of such polymers not modified by chemical after-treatment
    • C08L23/04—Homopolymers or copolymers of ethene
    • C08L23/08—Copolymers of ethene
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L51/00—Compositions of graft polymers in which the grafted component is obtained by reactions only involving carbon-to-carbon unsaturated bonds; Compositions of derivatives of such polymers
    • C08L51/06—Compositions of graft polymers in which the grafted component is obtained by reactions only involving carbon-to-carbon unsaturated bonds; Compositions of derivatives of such polymers grafted on to homopolymers or copolymers of aliphatic hydrocarbons containing only one carbon-to-carbon double bond
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L67/00—Compositions of polyesters obtained by reactions forming a carboxylic ester link in the main chain; Compositions of derivatives of such polymers
    • C08L67/02—Polyesters derived from dicarboxylic acids and dihydroxy compounds
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J2367/00—Characterised by the use of polyesters obtained by reactions forming a carboxylic ester link in the main chain; Derivatives of such polymers
    • C08J2367/02—Polyesters derived from dicarboxylic acids and dihydroxy compounds
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J2423/00—Characterised by the use of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Derivatives of such polymers
    • C08J2423/02—Characterised by the use of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Derivatives of such polymers not modified by chemical after treatment
    • C08J2423/04—Homopolymers or copolymers of ethene
    • C08J2423/08—Copolymers of ethene
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2203/00—Applications
    • C08L2203/12—Applications used for fibers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2203/00—Applications
    • C08L2203/20—Applications use in electrical or conductive gadgets
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2205/00—Polymer mixtures characterised by other features
    • C08L2205/02—Polymer mixtures characterised by other features containing two or more polymers of the same C08L -group
    • C08L2205/025—Polymer mixtures characterised by other features containing two or more polymers of the same C08L -group containing two or more polymers of the same hierarchy C08L, and differing only in parameters such as density, comonomer content, molecular weight, structure
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2205/00—Polymer mixtures characterised by other features
    • C08L2205/03—Polymer mixtures characterised by other features containing three or more polymers in a blend
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
    • C08L2207/00—Properties characterising the ingredient of the composition
    • C08L2207/20—Recycled plastic

Definitions

  • the invention relates to a polyester composite material and a preparation method thereof, and belongs to the technical field of polymer processing and modification.
  • Polybutylene terephthalate (PBT) and polyethylene terephthalate (PET) plastics are two commonly used polyester materials. Because of its high strength, fatigue resistance, dimensional stability, creep, heat aging, and good processing performance, it is widely used in automotive, electronic appliances, industrial machinery and other fields.
  • PBT and PET also have obvious shortcomings, such as being very sensitive to the notch and low notched impact strength. This is their main disadvantage as engineering plastics, and the lack of toughness has become a major obstacle to the promotion and application. Therefore, research on toughening modification of PBT and PET has always been an important part of PBT and PET high performance. Melt blending with functionalized elastomers is a simple, economical, and effective method to improve the toughness of polyesters.
  • polyester material obtained by the above preparation method still cannot satisfy some products requiring high application, and the addition of the elastomer can significantly reduce the tensile strength of the polyester material.
  • polyester materials such as PBT are often not resistant to hydrolysis due to the presence of terminal carboxyl groups, terminal hydroxyl groups, and a large number of ester bonds, and thus are difficult to apply in environments with high humidity.
  • Elastomers are usually dispersed in a polyester matrix with spherical particles to form a common island structure, and the toughening efficiency is often inferior to the "double continuous” or “double continuous” phase morphology. Therefore, the transformation of the phase morphology of the polyester/elastomer blend material from the island structure to the bicontinuous phase structure is the key to further improving the toughening efficiency.
  • the patent CN 102838852 A adds a composite antibacterial agent containing zinc oxide to the PBT material to impart antibacterial properties to the material, but in the process of melt processing, The addition of zinc oxide catalyzes the thermal degradation of PBT, which significantly reduces the toughness of the material and limits the application of PBT materials.
  • Patent CN 102675836 A invents a conductive/antistatic polyester PET composite material, but the addition amount of carbon nanotubes is large, and the preparation process is cumbersome, which is not conducive to industrial production. Therefore, it is highly desirable to invent a composite material that is stable in toughness and has a good additional function.
  • the present invention provides a polyester composite material, which ensures the phase morphology of the blended material changes from a common island structure to a bi-continuous structure while ensuring in-situ reaction with the elastomer.
  • a super tough polyester composite is obtained and still maintains high tensile strength.
  • the composition of the present invention has excellent hydrolysis resistance and can be widely used in the fields of plastic structural members, plastic packaging or automotive interior parts.
  • the polyester composite material provided by the invention first melt-blends the polyester and the elastomer to ensure that the functional groups on the elastomer fully react with the terminal groups (carboxyl groups or hydroxyl groups) of the polyester to achieve in-situ reaction compatibilization;
  • the chain extender continues to melt blend, expand the molecular weight of the polyester, thereby increasing the viscosity of the polyester matrix, and transforming the elastomer from the original dispersed phase to the continuous phase to form a bicontinuous structure, thereby further enhancing the elastomer to the polyester. Toughening effect.
  • the tensile strength of the blend is also significantly improved. Since the functionalized elastomer and the chain extender react with the end groups of the polyester, a large amount of terminal carboxyl groups and terminal hydroxyl groups are consumed, thereby also significantly improving the hydrolysis resistance of the composition.
  • a first object of the present invention is to provide a polyester material or an engineering plastic composition, the formulation of which is formulated in parts by weight, including: 65 to 90 parts of polyester, and 5 to 35 parts of an elastomer. , chain extender 0.05 ⁇ 3 parts, functional additives 0.01 ⁇ 5 parts;
  • a method of preparing the material or composition comprising:
  • the polyester, the elastomer and the functional auxiliary are mixed according to the parts by weight, and then melt-extruded, and the chain extender is added according to the weight ratio, and then melt-extruded to obtain a material;
  • the polyester, the elastomer and the functional auxiliary are mixed according to the parts by weight, and then melt blended, and the chain extender is added according to the weight ratio, and then melt blended to obtain a material;
  • the elastomer is an elastomer containing an epoxy group or an acid anhydride group
  • the elastomer contains structural units of vinyl acetate.
  • the polyester comprises at least at least polyethylene terephthalate (PET), polybutylene terephthalate (PBT), and polycarbonate (PC).
  • PET polyethylene terephthalate
  • PBT polybutylene terephthalate
  • PC polycarbonate
  • the polyester has an intrinsic viscosity of from 0.3 to 1.5 dL/g.
  • the chain extender includes at least one of a compound containing a plurality of epoxy groups, a compound containing a plurality of isocyanate groups, and an acid anhydride compound.
  • the functional adjuvant includes at least one of an antioxidant, a lubricant, a nucleating agent, an anti-hydrolysis agent, and a transesterification inhibitor.
  • the antioxidant comprises tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propanoate]pentaerythritol ester, three [2,4-di-tertiary At least one of butylphenyl]phosphite and n-octadecanol of ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionate.
  • the lubricant comprises solid paraffin, liquid paraffin, polyethylene wax, stearic acid amide, methyl bis stearic acid amide, N, N-ethylene bis stearic acid amide, and At least one of pentaerythritol stearate.
  • the nucleating agent comprises at least one of talc, magnesium stearate, sodium benzoate, and Surlyn8920.
  • the anti-hydrolysis agent comprises N,N'-bis(2,6-diisopropylphenyl)carbodiimide; the transesterification inhibitor is sodium dihydrogen phosphate At least one of triphenyl phosphite and disodium dihydrogen pyrophosphate.
  • the preparation method of the composition specifically includes:
  • the polyester, the elastomer and the functional auxiliary are pre-mixed according to the weight ratio, and then the premix is fed from the main feeding port to the conveying section of the twin-screw extruder, and the chain extender is added by weight according to the side feeding.
  • the ratio is added to the middle of the meshing section of the twin-screw extruder, and the composite material is obtained by continuous melt extrusion, wherein the melt extrusion temperature is 1 to 30 ° C above the melting point of the polyester, and the screw rotation speed is 100 to 350 rpm;
  • the polyester, the elastomer and the functional auxiliary are added to the internal mixer according to the weight ratio to melt blend for 2 to 5 minutes, and then the chain extender is added to continue blending for 1 to 5 minutes to obtain an engineering.
  • a plastic composition wherein the melt blending temperature is from 1 to 30 ° C above the melting point of the polyester.
  • the material when the polyester is selected from PBT, the material further comprises 0.1 to 4 parts of an antibacterial agent, and the antibacterial agent comprises one or more of zinc oxide, silver oxide, titanium oxide, and antimony oxide.
  • the antibacterial agent comprises one or more of zinc oxide, silver oxide, titanium oxide, and antimony oxide.
  • the method for preparing the material comprises:
  • the elastomer and the antibacterial agent are mixed according to the weight ratio, and then extruded, the chain extender is added according to the weight ratio, and then the material is obtained by continuous melt extrusion;
  • the PBT, the elastomer, and the antibacterial agent are mixed according to the parts by weight, melt-blended, and then blended by adding a chain extender in a weight ratio to obtain a material.
  • the melt blending temperature is from 1 to 30 ° C above the melting point of the polyester.
  • a second object of the present invention is to provide a PBT composite material, which has a formulation ratio of 65 to 90 parts of PBT, 5 to 35 parts of a vinyl acetate-based copolymer, and an antibacterial agent. ⁇ 4 parts, 0 to 3 parts of the chain extender; the antibacterial agent includes one or more of zinc oxide, silver oxide, titanium dioxide, and cerium oxide.
  • the formulation of the composite material comprises 65 to 90 parts of PBT, 5 to 35 parts of a vinyl acetate-based copolymer, and 0.1 to 4 parts of an antibacterial agent according to a weight ratio.
  • the chain agent is 0.05 to 3 parts, and the functional auxiliary agent is 0.01 to 5 parts.
  • the method for preparing the composite material comprises: mixing PBT, a vinyl acetate-based copolymer, and an antibacterial agent according to a weight ratio, and then extruding, adding according to a weight ratio.
  • the chain extender is then subjected to continuous melt extrusion to obtain a material;
  • the PBT, the vinyl acetate-based copolymer, and the antibacterial agent are mixed according to the parts by weight, melt-blended, and then blended by adding a chain extender in a weight ratio to obtain a material.
  • the method for preparing the composite material specifically includes:
  • PBT vinyl acetate-based copolymer and antibacterial agent are pre-mixed uniformly according to the weight ratio at room temperature, and then the premix is added from the main feed port to the conveying section of the twin-screw extruder, and the chain is extended by the side feed.
  • the agent is added to the middle of the meshing section of the twin-screw extruder, and the material is obtained by continuous melt extrusion;
  • the PBT, the vinyl acetate-based copolymer and the antibacterial agent are pre-mixed uniformly at room temperature according to the weight ratio, and the premix is melt blended in an internal mixer for 2 to 5 minutes, and then the chain extender is added to continue.
  • the material is obtained by blending for 1 to 5 minutes.
  • the temperature of the melt blending is 1 to 30 ° C above the melting point of the PBT, and the screw rotation speed is 100 to 350 rpm.
  • the formulation of the composite material comprises 65 to 90 parts of PBT, 5 to 35 parts of vinyl acetate-based copolymer, and 0.1 to 5 parts of carbon epoxide according to parts by weight.
  • the preparation method of the composite material comprises: mixing PBT, epoxidized carbon-based particles and functional auxiliary agents according to the parts by weight, and then extruding and extruding according to the parts by weight. Adding a vinyl acetate-based copolymer to the mixture, and then performing melt extrusion, finally adding a chain extender according to the proportion by weight, and continuing melt extrusion to obtain a material;
  • the PBT, the epoxidized carbon-based particles and the functional auxiliary are mixed according to the parts by weight, and then melt-blended, and the vinyl acetate-based copolymer is added in a weight ratio, and then melt blended, and finally The chain extender is added in proportions by weight, and further melt blending is carried out to obtain a material.
  • the method for preparing the composite material specifically includes:
  • PBT, epoxidized carbon-based particles and functional additives are pre-mixed according to the weight ratio, and then the premix is fed from the main feed port to the conveying section of the twin-screw extruder, and the acetic acid is fed through the first side feed.
  • the vinyl ester-based copolymer is melt-blended by adding to a twin-screw extruder according to the proportion by weight, and then the chain extender is added to the twin-screw extruder by continuous melt extrusion through the ratio of the weight ratio of the second side feed.
  • a material wherein the melt extrusion temperature is 1 to 30 ° C above the melting point of PBT, and the screw rotation speed is 100 to 350 rpm;
  • the PBT, the epoxidized carbon-based particles and the functional auxiliary are added to the internal mixer for melt blending according to the parts by weight for 1 to 3 minutes, and then the vinyl acetate-based copolymer is added in proportion to the weight ratio. After mixing for 1 to 4 minutes, finally adding the chain extender according to the weight ratio to continue blending for 1 to 3 minutes to obtain a material, wherein the melt blending temperature is 1 to 30 ° C above the melting point of PBT.
  • the formulation of the composite material comprises 65 to 90 parts of PBT, 5 to 35 parts of a vinyl acetate based copolymer, and 0.1 to epoxidized nano zinc oxide according to a weight ratio. 4 parts.
  • the vinyl acetate-based copolymer further contains at least glycidyl methacrylate and an ethylene structural unit.
  • the vinyl acetate-based copolymer has a vinyl acetate content of 45 to 75% by mass and a glycidyl methacrylate content of 0.5 to 10% by mass.
  • the vinyl acetate based copolymer may further comprise an ethylene vinyl acetate binary copolymer.
  • the ethylene-vinyl acetate binary copolymer has a vinyl acetate content of 45 to 75% by mass.
  • the polyester has an intrinsic viscosity of from 0.3 to 1.5 dL/g.
  • the antimicrobial agent oxide has a particle size of from 10 to 3000 nanometers.
  • the particle size of the antibacterial agent oxide is preferably from 10 to 300 nm.
  • the epoxidized carbon-based particles are at least one of epoxidized multi-walled carbon nanotubes, epoxidized graphene, and epoxidized carbon black.
  • the epoxidized carbon-based particles have a diameter of 10 to 300 nm.
  • the functional adjuvant includes at least one of an antioxidant, a lubricant, a nucleating agent, an anti-hydrolysis agent, and a transesterification inhibitor.
  • the chain extender is at least one of a compound containing a plurality of epoxy groups, a compound containing a plurality of isocyanate groups, and an acid anhydride compound.
  • the antioxidant is tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propanoic acid]pentaerythritol ester, three [2,4-di-tertiary At least one of butylphenyl]phosphite and n-octadecanol of ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionate.
  • the lubricant is solid paraffin, liquid paraffin, polyethylene wax, stearic acid amide, methyl bis stearic acid amide, N, N-ethylene bis stearic acid amide, and At least one of pentaerythritol stearate.
  • the nucleating agent is at least one of talc, magnesium stearate, sodium benzoate, and Surlyn8920.
  • the temperature of the melt blending is 1 to 30 ° C above the melting point of the PBT.
  • a third object of the present invention is to provide a PET composite material, wherein the formulation of the material is formulated in parts by weight, comprising: 70-95 parts of recycled PET, 5-30 parts of vinyl acetate copolymer,
  • the recovered PET has an intrinsic viscosity of 0.3 to 1.0 dL/g, and the vinyl acetate-based copolymer has a vinyl acetate content of 45 to 75% by mass.
  • the material further comprises 0.1 to 4 parts of epoxidized nano zinc oxide or 0.1 to 4 parts of nano zinc oxide.
  • the material further comprises 0.05-3 parts of a chain extender.
  • the preparation method of the material comprises:
  • the PET, the vinyl acetate-based copolymer, and the epoxidized nano-zinc oxide are pre-mixed uniformly according to the weight ratio at room temperature, and then melt-extruded through a twin-screw extruder to obtain a composite material, wherein the melt extrusion temperature is PET melting point above 1 ⁇ 30 ° C, screw speed is 100 ⁇ 350 rpm;
  • the PET, the vinyl acetate-based copolymer, and the epoxidized nano-zinc oxide are melt-blended in a mixer for 3 to 10 minutes according to the parts by weight to obtain a composite material, wherein the melt blending temperature is PET. Above the melting point of 1 to 30 ° C.
  • the surface of the epoxidized nano zinc oxide contains at least one epoxy group, and the preparation method thereof comprises:
  • the epoxy nano zinc oxide, the solvent and the epoxy compound are mixed in a ratio by weight of 5 to 15:65 to 85:2 to 30, and reacted at 30 to 70 ° C for 1 to 24 hours to obtain an epoxidized nanometer after purification.
  • the epoxy nano-zinc oxide, the solvent and the epoxy compound are stirred at a high speed of 80 to 99:0.5 to 20:0.5 to 5 at a high speed for 2 to 10 minutes to obtain an epoxidized nano zinc oxide;
  • the solvent is at least one of water, methanol, and ethanol.
  • the epoxy compound contains at least one -Si-O- group, and the nano zinc oxide has a particle diameter of 10 to 300 nm.
  • the preparation method of the material comprises:
  • the PET, vinyl acetate-based copolymer and nano-zinc oxide are pre-mixed uniformly according to the weight ratio at room temperature, and then the premix is added from the main feed port to the conveying section of the twin-screw extruder, and the side feed is expanded.
  • the chain agent is added to the middle of the meshing section of the twin-screw extruder according to the weight ratio, and a tough PET antibacterial composite material is obtained by continuous melt extrusion, wherein the melt extrusion temperature is 1 to 30 ° C above the melting point of the PET, and the screw rotation speed is 100 to 350 rpm;
  • the PET, the vinyl acetate-based copolymer, and the nano-zinc oxide are added to the internal mixer for melt blending for 2 to 5 minutes according to the weight ratio, and then the chain extender is added to continue blending for 1 to 5 minutes to obtain a A tough PET antibacterial composite material in which the melt blending temperature is 1 to 30 ° C above the melting point of PET.
  • the material further comprises 0.1 to 5 parts of the epoxidized carbon-based particles, 0.01 to 5 parts of the functional auxiliary agent, and 0.05 to 3 parts of the chain extender.
  • the method for preparing the material comprises:
  • the PET, the epoxidized carbon-based particles and the functional auxiliary are mixed according to the parts by weight, and then melt-extruded, the vinyl acetate-based copolymer is added according to the weight ratio, and then melt-extruded, and finally according to the weight.
  • the proportion of the parts is added to the chain extender, and the melt extrusion is continued to obtain the material;
  • the PET, the epoxidized carbon-based particles and the functional auxiliary are mixed according to the parts by weight, then melt-blended, and the vinyl acetate-based copolymer is added according to the weight ratio, and then melt blended, and finally The chain extender is added in proportions by weight, and further melt blending is carried out to obtain a material.
  • the method for preparing the material specifically includes:
  • the PET, the epoxidized carbon-based particles and the functional auxiliary are pre-mixed according to the weight ratio, and then the premix is fed from the main feed port to the conveying section of the twin-screw extruder, and the acetic acid is fed through the No. 1 side feed.
  • the vinyl ester-based copolymer is melt-blended by adding to a twin-screw extruder according to the proportion by weight, and then the chain extender is added to the twin-screw extruder by continuous melt extrusion through the ratio of the weight ratio of the second side feed.
  • a material wherein the melt extrusion temperature is 1 to 30 ° C above the melting point of PET, and the screw rotation speed is 100 to 350 rpm;
  • the PET, the epoxidized carbon-based particles and the functional auxiliary are added to the internal mixer for melt blending for 1 to 3 minutes according to the weight ratio, and then the vinyl acetate-based copolymer is added in proportion to the weight ratio. After mixing for 1 to 4 minutes, finally adding the chain extender according to the weight ratio to continue blending for 1 to 3 minutes to obtain a material, wherein the melt blending temperature is 1 to 30 ° C above the melting point of PET.
  • the vinyl acetate-based copolymer further contains at least glycidyl methacrylate and an ethylene structural unit, wherein the glycidyl methacrylate has a mass percentage of 0.5 to 10%. .
  • the vinyl acetate based copolymer may further comprise an ethylene vinyl acetate binary copolymer.
  • the epoxidized carbon-based particles are at least one of epoxidized multi-walled carbon nanotubes, epoxidized graphene, and epoxidized carbon black.
  • the epoxidized carbon-based particles have a diameter of 10 to 300 nm.
  • the chain extender includes at least one of a compound containing a plurality of epoxy groups, a compound containing a plurality of isocyanate groups, and an acid anhydride compound.
  • the functional adjuvant includes at least one of an antioxidant, a lubricant, a nucleating agent, an anti-hydrolysis agent, and a transesterification inhibitor.
  • the antioxidant comprises tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propanoate]pentaerythritol ester, three [2,4-di-tertiary At least one of butylphenyl]phosphite and n-octadecanol of ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionate.
  • the lubricant comprises solid paraffin, liquid paraffin, polyethylene wax, stearic acid amide, methyl bis stearic acid amide, N, N-ethylene bis stearic acid amide, and At least one of pentaerythritol stearate.
  • the nucleating agent comprises at least one of talc, magnesium stearate, sodium benzoate, and Surlyn8920.
  • the anti-hydrolysis agent comprises N,N'-bis(2,6-diisopropylphenyl)carbodiimide; the transesterification inhibitor is sodium dihydrogen phosphate At least one of triphenyl phosphite and disodium dihydrogen pyrophosphate.
  • a fourth object of the present invention is to provide a plastic package or plastic structural member comprising the composite material described above.
  • a fifth object of the present invention is to provide an automotive interior trim comprising the composite material described above.
  • a sixth object of the present invention is to provide an electrical enclosure, characterized in that the electrical enclosure comprises the composite material described above.
  • a seventh object of the present invention is to provide an antimicrobial fiber or fabric comprising the composite material described above.
  • polyester composite of the present invention since the vinyl acetate-based copolymer and the chain extender react with the terminal groups of the polyester, a large amount of terminal carboxyl groups and terminal hydroxyl groups are consumed, thereby significantly improving the hydrolysis resistance of the composition. .
  • the polyester material of the present invention first melt-blends the polyester and the elastomer to ensure that the functional groups on the elastomer fully react with the terminal groups (carboxy or hydroxyl groups) of the polyester to achieve in-situ reaction compatibilization. Then adding a chain extender to continue melt blending, expanding the molecular weight of the polyester, thereby increasing the viscosity of the polyester matrix, and transforming the elastomer from the original dispersed phase to the continuous phase to form a bicontinuous structure, thereby further enhancing the elastomer pairing.
  • the toughening effect of the ester In addition, the tensile strength of the composition is also significantly improved due to the expansion of the molecular weight of the polyester matrix.
  • the polyester material of the present invention first melt-blends the polyester and the epoxidized carbon-based particles, and then adds the elastomer blend, so that the carbon-based particles can be selectively distributed in the polyester matrix, and the elasticity is ensured.
  • the body and polyester end groups fully react to achieve in-situ reaction compatibilization; finally add the chain extender to continue melt blending, expand the molecular weight of the polyester, thereby increasing the viscosity of the polyester matrix, and making the particle size and particle spacing of the elastomer Significantly reduce, thereby further improving the toughening effect of the elastomer on the polyester; at the same time, the reduction of the elastomer particle size and the particle spacing makes the carbon-based particles selectively dispersed in the polyester matrix more likely to form a network conductive structure. Therefore, the electrical conductivity of the polyester material can be made to reach an antistatic range, that is, 10 -11 to 10 -4 S/cm, under the condition that the amount of carbon-based particles added is very low.
  • the polyester material of the invention is improved by the addition of the metal oxide antibacterial agent and the chain extender, and the antibacterial property of the material is obviously improved, and at the same time, the thermal degradation of the antibacterial agent to the polyester matrix can be compensated, so that the polyester composite material is maintained. High toughness.
  • the polyester composite material of the invention improves the antibacterial property of the material by the addition of the epoxidized nano zinc oxide, and effectively inhibits the migration of zinc oxide in the polyester matrix; and simultaneously oxidizes the nano zinc oxide. It can react in situ with polyester, which weakens the degradation of polyester by zinc oxide, and makes the material have excellent mechanical properties such as impact strength.
  • the preparation method of the polyester composite material of the invention is simple and efficient, and is easy to realize industrial production, and has a broad prospect.
  • PET 80 parts of PET, 20 parts of ethylene-vinyl acetate-glycidyl methacrylate terpolymer, 0.2 parts of tris[2,4-di-tert-butylphenyl]phosphite, and ⁇ -(3,5- 0.2 parts of n-tert-butyl-4-hydroxyphenyl)propanoic acid n-octadecyl alcohol ester was pre-mixed uniformly at room temperature, and then the premix was fed from the main feed port to the conveying section of the twin-screw extruder, and the side was fed.
  • PET 85 parts of PET, 3 parts of ethylene-vinyl acetate-glycidyl methacrylate terpolymer, 12 parts of ethylene-vinyl acetate binary copolymer, and four [ ⁇ -(3,5-di-tert-butyl- 4-hydroxyphenyl)propionic acid]pentaerythritol ester 0.2 parts, polyethylene wax 0.1 parts and sodium benzoate 0.3 parts were melt blended in an internal mixer for 3 minutes, and then 1.3 parts of chain extender, pyromellitic anhydride, was added to continue blending. The composite was obtained in 2 minutes (the blending temperature was 260 ° C).
  • Example 1 On the basis of Example 1, the ethylene-vinyl acetate-glycidyl methacrylate terpolymer was replaced with ethylene-n-butyl acrylate-glycidyl methacrylate terpolymer (ie ethylene-n-butyl) The acrylate-glycidyl methacrylate terpolymer), the other components and conditions are consistent, and a polyester composite is prepared.
  • a composite material was prepared without adding a functionalized elastomer and a chain extender: 100 parts of PBT and tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionic acid] pentaerythritol 0.3
  • the mixture was continuously melt extruded by a twin-screw extruder (extrusion temperature of 240 ° C, screw rotation speed of 150 rpm) to obtain a composite material.
  • a composite material was prepared without adding a chain extender: 80 parts of PBT, 20 parts of ethylene-vinyl acetate-glycidyl methacrylate terpolymer, and four [ ⁇ -(3,5-di-tert-butyl) 0.3 parts of pentaerythritol] pentaerythritol ester was premixed uniformly at room temperature, and then the premix was fed from the main feed port to the conveying section of the twin-screw extruder, and subjected to continuous melt extrusion (extrusion temperature).
  • a composite material was obtained at 240 ° C and a screw speed of 150 rpm.
  • a composite material was prepared using an ethylene-vinyl acetate binary copolymer as an elastomer: 80 parts of PBT, 20 parts of ethylene-vinyl acetate binary copolymer, and four [[beta]-(3,5-di-uncle 0.3 parts of pentaerythritol ester of butyl-4-hydroxyphenyl)propanoate] premixed uniformly at room temperature, then the premix is added from the main feed port to the conveying section of the twin-screw extruder, and 1 part is expanded by the side feed.
  • the chain agent ADR4370 was fed into the middle of the meshing section of the twin-screw extruder and subjected to continuous melt extrusion (extrusion temperature of 240 ° C, screw rotation speed of 150 rpm) to obtain a composite material.
  • a composite material was prepared by one-time mixing: 80 parts of PBT, 20 parts of ethylene-vinyl acetate-glycidyl methacrylate terpolymer, and four [ ⁇ -(3,5-di-tert-butyl- 0.3 parts of 4-hydroxyphenyl)propionic acid] pentaerythritol ester and 1 part of ADR4370 chain extender are pre-mixed uniformly at room temperature, and then the premix is fed from the main feed port to the conveying section of the twin-screw extruder through continuous melt extrusion.
  • the composite material was obtained by extrusion (extrusion temperature of 240 ° C and screw rotation speed of 150 rpm).
  • the composite material was prepared by first extending the chain extender and then adding the elastomer: 80 parts of PBT, 1 part of chain extender ADR4370 and four [ ⁇ -(3,5) -di-tert-butyl-4-hydroxyphenyl)propionic acid] pentaerythritol ester 0.3 parts premixed uniformly at room temperature, then the premix is fed from the main feed port to the twin screw extruder conveying section, and the side feed will be 20 parts of ethylene-vinyl acetate-glycidyl methacrylate terpolymer was placed in the middle of the meshing section of the twin-screw extruder, and subjected to continuous melt extrusion (extrusion temperature of 240 ° C, screw rotation speed of 150 rpm) to obtain a composite material.
  • elastomer 80 parts of PBT, 1 part of chain extender ADR4370 and four [ ⁇ -(3,5) -di-tert-butyl-4-hydroxyphen
  • the composite materials obtained by extruding the above Examples 1-3 and Comparative Examples 1-5 were injected into a standard spline on an injection molding machine for tensile and impact property tests, and the test results are shown in Table 1 (aging 0 h).
  • the composite materials obtained in Examples 4-6 were hot-pressed by a flat vulcanizer, and cut into standard splines according to relevant standards for tensile and impact property tests.
  • the test results are shown in Table 1 (aging 0 h).
  • the splines of the examples and the comparative examples were placed in an environmental aging chamber to perform constant temperature and humidity aging experiments under the conditions of 70 ° C / 80% RH, and a batch of samples were taken at regular intervals (24h, 48h, 72h, 96h).
  • the tensile properties and impact properties were measured to evaluate the hydrolysis resistance of the composite.
  • the test results are shown in Table 1.
  • Example 3 34,375,95 33,340,93 31,295,88 19,102,42 11,23,9
  • Example 4 41,320,75 39,280,72 36,234,65 35,200,54 21,97,32
  • Example 5 35,430,88 34,413,84 32,384,72 28,280,65 16,113,28
  • Comparative example 4 36,51,12 36,44,11 34,38,9 23,18,5 11,8,2 Comparative example 5 36,26,7 35,21,6 34,18,4 21,10,2 11,5,1
  • the three numbers in each grid in the table indicate the values of tensile strength, elongation at break and notched impact strength from left to right, respectively, in units of MPa, % and kJ/m 2 .
  • the tensile properties (tensile strength and elongation at break) of the composites obtained in the examples and the comparative examples were tested according to the GB/T 1040-1992 standard, and the tensile rate was 50 mm/min; the notched impact strength was according to GB/T 1043-1993. Standard test, the depth of the gap is 2mm. All mechanical properties were measured after 24 hours in a 23 ° C environment.
  • the ethylene-vinyl acetate-glycidyl methacrylate terpolymer used was supplied by LANXESS Chemical Company, and the remaining chemicals were common commercial products.
  • the preparation method of the present invention firstly reacts the polyester matrix with the functionalized elastomer to achieve the original reaction compatibilization, and then adds an appropriate amount of chain extender to increase the molecular weight of the polyester, thereby increasing the viscosity of the matrix and making the blend.
  • the phase morphology changes from the original island structure to the bi-continuous structure, thereby further enhancing the toughening effect of the elastomer on the polyester matrix.
  • the tensile strength of the resulting composite was also significantly higher than that of the composite of Comparative Example 2.
  • the chain extender with a smaller molecular weight and more functional groups will preferentially react with the polyester, increasing the steric hindrance of the reaction, making the elastomer difficult to re- Reacts with polyester and does not achieve good compatibilization.
  • the toughness of the composite material obtained by first adding a chain extender and then adding an elastomer was also poor. It can be seen that the in-situ compatibilization effect of the fully functionalized elastomer and the polyester and the chain extension of the chain extender have a synergistic effect on the toughening of the polyester.
  • Example 1 and Example 6 it is also a functionalized elastomer, ethylene-vinyl acetate-glycidyl methacrylate terpolymer than ethylene-n-butyl acrylate-glycidyl methacrylate The toughening effect of the terpolymer is better.
  • the pure PBT (Comparative Example 1) and the composite material obtained by adding only the ethylene-vinyl acetate-glycidyl methacrylate terpolymer (Comparative Example 2) have poor hydrolysis resistance.
  • the mechanical properties decreased significantly after aging for 24 h, while the composite of the present invention was excellent in hydrolysis resistance, and the mechanical properties were significantly decreased after aging for 72 h or 96 h.
  • the presence of terminal carboxyl groups and terminal hydroxyl groups promotes the hydrolysis of the polyester, and the present invention utilizes the reaction of the functionalized elastomer and the chain extender with the polyester end groups, consuming a large amount of terminal carboxyl groups and terminal hydroxyl groups, so that the composite material can be significantly improved. Hydrolysis resistance.
  • the polyester composite obtained by the invention not only has excellent toughness, but also maintains high tensile strength and excellent hydrolysis resistance, and can be widely used in the fields of plastic structural parts, plastic packaging, automobile interior parts and the like. .
  • PET 85 parts of PET, 0.5 parts of epoxidized multi-walled carbon nanotubes, 0.2 parts of tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionic acid] pentaerythritol ester, 0.1 parts of polyethylene wax and 0.3 parts of sodium benzoate was added to the internal mixer for melt blending for 2 minutes, then 15 parts of ethylene-vinyl acetate-glycidyl methacrylate terpolymer was added to continue blending for 3 minutes, and finally 1.3 parts of chain extender were added. The benzenetetracarboxylic anhydride was further blended for 2 minutes (the blending temperature was 260 ° C) to obtain a polyester material.
  • PET 70 parts of PET, 0.6 parts of epoxidized multi-walled carbon nanotubes, 0.2 parts of tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propanoic acid] pentaerythritol ester, three [2,4- 0.2 parts of di-tert-butylphenyl]phosphite and 0.2 parts of sodium dihydrogen phosphate were melt blended in an internal mixer for 1 minute, and then ethylene-vinyl acetate-glycidyl methacrylate terpolymer 10 was added.
  • the portion and the ethylene-vinyl acetate binary copolymer 20 parts were further blended for 4 minutes, and finally 0.8 parts of the chain extender ADR4370 was added and the blending was continued for 2 minutes (the blending temperature was 250 ° C) to obtain a polyester material.
  • a polyester material was prepared using an ethylene-vinyl acetate binary copolymer as an elastomer: 80 parts of PBT, 0.4 parts of epoxidized multi-walled carbon nanotubes, and four [[beta]-(3,5-di-uncle 0.3 parts of pentaerythritol ester of butyl-4-hydroxyphenyl)propanoate] premixed uniformly at room temperature, then the premix was fed from the main feed port to the conveying section of the twin-screw extruder, and ethylene was fed through the No. 1 side feed.
  • a polyester material was prepared without adding epoxidized carbon-based particles: 80 parts of PBT and 0.3 parts of tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propanoic acid] pentaerythritol ester Premixed uniformly at room temperature, then the premix was fed from the main feed port to the twin-screw extruder transfer section, and the ethylene-vinyl acetate-glycidyl methacrylate terpolymer 20 was fed through the No. 1 side feed.
  • the mixture was melt blended by adding a twin-screw extruder, and then 1 part of the chain extender ADR4370 was fed into the twin-screw extruder through the second side feed through continuous melt extrusion (extrusion temperature was 240 ° C, screw speed was 150 rpm).
  • a polyester material is available.
  • a polyester material was prepared without adding a chain extender: 80 parts of PBT, 0.4 parts of epoxidized multi-walled carbon nanotubes, and tetra[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl) ) propionate] pentaerythritol ester 0.3 parts premixed uniformly at room temperature, then the premix is fed from the main feed port to the twin-screw extruder transfer section, and the ethylene-vinyl acetate-methacrylic acid is fed through the No. 1 side feed.
  • a part of the glycidyl ester terpolymer was added to a twin-screw extruder through continuous melt extrusion (extrusion temperature of 240 ° C, screw rotation speed of 150 rpm) to obtain a polyester material.
  • a polyester material was prepared by simultaneously adding epoxidized carbon-based particles and an elastomer: 80 parts of PBT, 0.4 parts of epoxidized multi-walled carbon nanotubes, and ethylene-vinyl acetate-glycidyl methacrylate 20 parts of the meta-copolymer and 0.3 parts of tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionic acid] pentaerythritol ester were uniformly mixed at room temperature, and then the premix was supplied from the main feed port.
  • the polyester materials obtained by extruding the above Examples 7-9 and Comparative Examples 6-9 were injected into a standard spline on an injection molding machine for tensile, impact and electrical conductivity tests, and the test results are shown in Table 2.
  • the composite materials obtained in Examples 10-12 were hot pressed by a flat vulcanizer, and cut into standard splines according to relevant standards for tensile, impact and electrical conductivity tests. The test results are shown in Table 2.
  • the splines of the examples and the comparative examples were placed in an environmental aging chamber at 70 ° C / 80% RH for constant temperature and humidity aging experiments. After 48 h, the splines were taken out, and the tensile properties and impact properties were measured and evaluated.
  • the hydrolysis resistance of the polyester material is shown in Table 2.
  • the tensile properties (tensile strength and elongation at break) of the polyester materials obtained in the examples and the comparative examples were tested according to the GB/T 1040-1992 standard, and the tensile rate was 50 mm/min; the notched impact strength was according to GB/T1043-
  • the 1993 standard test has a notch depth of 2 mm. All mechanical properties were measured after 24 hours in a 23 ° C environment.
  • the conductivity of the polyester material was measured using a four-probe conductivity meter.
  • the ethylene-vinyl acetate-glycidyl methacrylate terpolymer used was supplied by LANXESS Chemical Company, and the remaining chemicals were common commercial products.
  • the polyester material of Comparative Example 8 If no chain extender is added to the polyester material (Comparative Example 8), the viscosity of the matrix during melt blending is not high, and the particle size and particle spacing of the elastomer particles cannot be further reduced. Therefore, the polyester material of Comparative Example 8 The mechanical properties and electrical conductivity are also significantly inferior to the present invention.
  • the polyester material obtained by blending the epoxidized carbon-based particles and the elastomer simultaneously into the polyester (Comparative Example 9) is difficult to form a conductive network because the carbon-based particles cannot be selectively distributed in the polyester matrix.
  • the electrical conductivity of the polyester material of the ratio 9 is also far less than that of the present invention.
  • the elongation at break and the notched impact strength of the present invention (such as Example 7) were increased by 62.8 times and 29.7 times, respectively, and the electrical conductivity was improved by 8 orders of magnitude from the original insulating material. Change to antistatic materials. Further, the polyester material of the present invention can maintain a high tensile strength due to the significant increase in the molecular weight of the polyester matrix by the chain extender and the reinforcing effect of the carbon-based particles.
  • the polyester material obtained by the invention not only has excellent mechanical properties, but also obtains antistatic property under the condition that the amount of conductive carbon-based particles is very low, and has excellent hydrolysis resistance, and can be widely applied to plastic structural parts, Electrical enclosures and other fields.
  • the PBT composite materials obtained by extruding the above Examples 13-14 and Comparative Examples 10-11 were sufficiently dried to be subjected to a melt index test, and standard splines were injected on the injection molding machine for tensile and impact property tests, and the test results were as follows. Table 3 shows.
  • the PBT composites obtained in Examples 15-16 were tested for melt index, and were hot pressed by a flat vulcanizer, and cut into standard tensile strips according to relevant standards for tensile and impact performance tests. The test results are shown in Table 3.
  • the PBT composites obtained by extruding the above Examples 17-19 and Comparative Examples 12-14 were sufficiently dried to be subjected to a melt index test, and standard splines were injected on an injection molding machine for tensile and impact property tests through Escherichia coli.
  • the antibacterial rate of the composite material was tested by the Staphylococcus aureus bacteriostasis test.
  • the test results are shown in Table 4.
  • the PBT composites obtained in Examples 20-21 were tested for melt index and hot pressed by a flat vulcanizer, and cut into standard splines according to relevant standards for tensile and impact performance tests, by Escherichia coli and Staphylococcus aureus.
  • the bacteriostasis test tested the bacteriostasis rate of the composite materials. The test results are shown in Table 4.
  • the tensile properties (tensile strength and elongation at break) of the examples and comparative examples were tested according to the GB/T 1040-1992 standard, and the tensile rate was 50 mm/min; the notched impact strength was tested according to the GB/T1043-1993 standard, and the notch depth was It is 2mm. All mechanical properties were measured after 24 hours in a 23 ° C environment. The melt index was measured at 250 ° C under a standard condition of 2.16 kg. The bacteriostatic rate of the composite material was measured by a plate count method (J. Food Sci. 2012, 77, 280-286). The vinyl acetate based copolymer used was supplied by LANXESS Chemical Company and the remaining chemicals were commercially available products.
  • chain extender can compensate for the degradation of PBT, but the increase in toughness of the composite after adding chain extender, zinc oxide and vinyl acetate based copolymer is not significant (Comparative Example 14), because of the chain extender It will preferentially react with the terminal carboxyl group or terminal hydroxyl group of PBT, thereby greatly reducing the reaction degree of the vinyl acetate-based copolymer with PBT; and the invention adds the chain extender from the feeding port of the twin-screw extruder, which not only ensures The vinyl acetate-based copolymer reacts well with the terminal group of PBT, and further compensates for the catalytic degradation of PBT by zinc oxide through subsequent chain extension, so that the prepared composite material has excellent toughness.
  • the resulting composite material was also very brittle. It can be seen that the PBT composite material obtained by the invention not only has excellent toughness, but also has excellent antibacterial ability, and can be widely applied to antibacterial fibers and fabrics, plastic packaging materials, automobile interior parts, medical consumables and the like.
  • the polyethylene terephthalate composites obtained in Examples 22 and 25 and Comparative Examples 15-17 were sufficiently dried to be subjected to melt index test, and standard splines were injected on the injection molding machine for tensile and impact properties. Test, the test results are shown in Table 5; the tough polyethylene terephthalate composite materials obtained in Examples 23 and 24 were sufficiently dried to be subjected to melt index test, and hot pressed by a flat vulcanizing machine, according to correlation The standard cuts are used for tensile and impact performance tests. The test results are shown in Table 5.
  • PET 80 parts of PET will be recovered, 20 parts of ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 60%, glycidyl methacrylate content of 3%), and 2 parts of nano zinc oxide. (particle size is 30nm) premixed uniformly at room temperature, then the premix is fed from the main feed port to the twin-screw extruder transfer section, and the chain extender ADR43700.75 parts is added to the twin-screw extruder by side feed. In the middle of the meshing section, a tough PET antibacterial composite material was obtained through continuous melt extrusion (extrusion temperature of 260 ° C and screw rotation speed of 150 rpm).
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • PET 85 parts of PET, ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 70%, glycidyl methacrylate content of 2%) 15 parts, 1 part of nano zinc oxide (particle size: 20 nm), melt blending was carried out for 3 minutes in an internal mixer, and then 0.5 part of chain extender ADR4468 was added to continue blending for 2 minutes (blending temperature was 250 ° C) to obtain a ductile PET antibacterial composite material.
  • the above-mentioned ductile PET antibacterial composite material was tested by melt index, and was hot pressed by a flat vulcanizing machine, and cut into standard splines according to relevant standards for tensile and impact performance tests, and tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the composite material, the test results are shown in Table 6.
  • PET ethylene-vinyl acetate-glycidyl methacrylate copolymer (60% vinyl acetate content, glycidyl methacrylate content 3%) 30 parts, 2.5 parts of nano zinc oxide (particle size is 100 nm), 0.3 parts of tetrakis[ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionic acid] pentaerythritol ester, 0.1 part of polyethylene wax, and 1 part of talc powder premixed at room temperature Uniform, then the premix is fed from the main feed port to the conveying section of the twin-screw extruder, and the chain extender SAG-0081.5 part is added to the middle of the meshing section of the twin-screw extruder through the side feed, and is continuously melted and extruded (squeezed).
  • a tough PET antibacterial composite material can be obtained by a temperature of 265 ° C and a screw rotation speed of 200 .
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • a tough PET antibacterial composite material can be obtained through continuous melt extrusion (extrusion temperature of 260 ° C, screw rotation speed of 150 rpm).
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 50%, glycidyl methacrylate content of 5%) 15 parts, nano zinc oxide 2 Parts (particle size 60nm), 0.25 parts of tris[2,4-di-tert-butylphenyl]phosphite, 2.5 parts of sodium benzoate added to the internal mixer for melt blending for 2.5 minutes, then adding chain extender Liuya 0.5 part of methyl diisocyanate was further blended for 2.5 minutes (the blending temperature was 255 ° C) to obtain a tough PET antibacterial composite material.
  • the above-mentioned ductile PET antibacterial composite material was tested by melt index, and was hot pressed by a flat vulcanizing machine, and cut into standard splines according to relevant standards for tensile and impact performance tests, and tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the composite material, the test results are shown in Table 6.
  • PET 100 parts of PET will be recovered, 2 parts of nano zinc oxide (particle size 30nm) will be pre-mixed uniformly at room temperature, then the premix will be added to the conveying section of the twin-screw extruder from the main feed port, and the chain will be extended by the side feed.
  • ADR43700.75 parts were added to the middle of the meshing section of the twin-screw extruder, and a PET antibacterial composite material was obtained through continuous melt extrusion (extrusion temperature of 260 ° C, screw rotation speed of 150 rpm).
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • PET 80 parts of PET will be recovered, 20 parts of ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 60%, glycidyl methacrylate content of 3%), and 2 parts of nano zinc oxide. (particle size is 30nm) premixed uniformly at room temperature, and then the premix is fed from the main feed port to the twin screw extruder conveying section through continuous melt extrusion (extrusion temperature is 260 ° C, screw speed is 150 rpm).
  • a PET antibacterial composite material 80 parts of PET will be recovered, 20 parts of ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 60%, glycidyl methacrylate content of 3%), and 2 parts of nano zinc oxide. (particle size is 30nm) premixed uniformly at room temperature, and then the premix is fed from the main feed port to the twin screw extruder conveying section through
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • PET 80 parts of PET will be recovered, 20 parts of ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 60%, glycidyl methacrylate content of 3%), and 2 parts of nano zinc oxide. (particle size is 30nm), the chain extender ADR43700.75 parts are pre-mixed uniformly at room temperature, and then the premix is fed from the main feed port to the conveying section of the twin-screw extruder and subjected to continuous melt extrusion (extrusion temperature is A PET antibacterial composite material was obtained at 260 ° C and a screw speed of 150 rpm.
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • a PET antibacterial composite material was obtained at an extrusion temperature of 260 ° C and a screw rotation speed of 150 rpm.
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 60%, glycidyl methacrylate content of 3%) 20 parts premixed at room temperature Uniform, then the premix is fed from the main feed port to the conveying section of the twin-screw extruder, and the chain extender ADR43700.75 parts is added to the middle of the meshing section of the twin-screw extruder through the side feed, after continuous melt extrusion (squeezing A PET composite material can be obtained at a temperature of 260 ° C and a screw rotation speed of 150 rpm.
  • the tough PET antibacterial composite material obtained by extrusion is fully dried and then subjected to melt index test, and a standard spline is injected on the injection molding machine for tensile and impact performance test, and the compound is tested by Escherichia coli and Staphylococcus aureus bacteriostatic test.
  • the inhibition rate of the material, the test results are shown in Table 6.
  • the epoxidized nano zinc oxide is prepared by argon-oxidizing nano zinc oxide by mixing nano zinc oxide, ethanol, water and KH560 at a high speed of 95:2:1:2 for 8 minutes.
  • the graft ratio of KH560 was 0.8%.
  • the preparation method of the epoxidized nano zinc oxide is as follows: the nano zinc oxide, the methanol, the water and the KH560 are stirred at a high speed of 80:1.5:1.5:1 for 6 minutes to obtain the epoxidized nano zinc oxide.
  • the graft ratio of KH560 is 0.6%.
  • Example 27 70 parts of polyethylene terephthalate (intrinsic viscosity: 0.85 dL/g), ethylene-vinyl acetate-glycidyl methacrylate copolymer (vinyl acetate content of 60%, methacrylic acid shrinkage Glycerate mass content 3%) 30 parts, epoxidized nano zinc oxide 2.5 parts (particle size 100 nm), tetra [ ⁇ -(3,5-di-tert-butyl-4-hydroxyphenyl)propionic acid] pentaerythritol 0.3 parts of ester, 0.1 part of polyethylene wax, and 1 part of talc powder were pre-mixed uniformly at room temperature, and melt-extruded by a twin-screw extruder (extrusion temperature: 265 ° C, screw rotation speed: 200 rpm) to obtain a composite material.
  • the preparation method of the epoxidized nano zinc oxide is the same as in Example 27.
  • the epoxidized nano zinc oxide is prepared by mixing nano zinc oxide, ethanol, water and KH560 in a weight ratio of 8:72:4:4, reacting at 40 ° C for 16 hours, and obtaining epoxy after purification. Nano-zinc oxide, wherein the graft ratio of KH560 is 1.3%.
  • the epoxidized nano zinc oxide is prepared by mixing nano zinc oxide, ethanol, water and KH560 in a weight ratio of 8:80:6:6, reacting at 50 ° C for 10 hours, and obtaining epoxy after purification. Nano-zinc oxide, wherein the graft ratio of KH560 is 1.7%.
  • the polyester composite obtained by extruding the above Examples 31-33 and Comparative Examples 24-27 was sufficiently dried to be subjected to a melt index test, and a standard spline was injected on an injection molding machine for tensile and impact property test through the large intestine.
  • Bacillus and Staphylococcus aureus bacteriostasis experiments and inhibition zone experiments tested the inhibition rate of the composite material and the migration behavior of the nano zinc oxide.
  • the test results are shown in Table 7.
  • the polyester composite materials obtained in Examples 34-35 were tested for melt index and hot pressed by a flat vulcanizing machine, and cut into standard splines according to relevant standards for tensile and impact performance tests, through Escherichia coli and golden yellow grapes.
  • the antibacterial activity of the composite and the inhibition zone test were used to test the inhibition rate of the composite material and the migration behavior of the nano zinc oxide.
  • the test results are shown in Table 7.
  • the tensile properties (tensile strength and elongation at break) of the examples and comparative examples were tested according to the GB/T 1040-1992 standard, and the tensile rate was 50 mm/min; the notched impact strength was tested according to the GB/T1043-1993 standard, and the notch depth was It is 2mm. All mechanical properties were measured after 24 hours in a 23 ° C environment.
  • the melt index of polyethylene terephthalate, polybutylene terephthalate and polycarbonate is (260 ° C, 2.16 kg), (250 ° C, 2.16 kg), (300 ° C, 1.2 kg). ) measured under standard conditions.
  • the composite zone inhibition zone experiment uses the Kirby-Bauer test method (eg Am. J. Clin.
  • the composite bacteriostatic rate experiment uses the plate counting method (J. Food Sci. 2012, 77, 280-286).
  • the polyethylene terephthalate used is the product of Changzhou Huarun Company.
  • the polybutylene terephthalate used is the product of Kanghui Petrochemical Company.
  • the polycarbonate used is the product of Taiwan Chimei Company; the recycled polyethylene terephthalate used
  • the glycol ester is the product of Zhejiang Jiali Renewable Resources Co., Ltd.; the remaining chemicals are commercially available products.
  • the modification effect is obviously superior to the modification effect of the traditional toughening agent ethylene-n-butyl acrylate-glycidyl methacrylate copolymer (Comparative Example 16) on recycled PET.
  • the vinyl acetate-based copolymer disclosed by the present invention has a more significant effect on the modification of recycled PET, such as tensile strength and fracture of vinyl acetate-based copolymer modified recycled PET (as in Example 22).
  • Elongation and notched impact strength were 1.43 times, 9.2 times and 4.2 times, respectively, of vinyl acetate-based copolymer modified synthetic PET (Comparative Example 17), while the melt index was modified by vinyl acetate-based copolymer. 18% of PET indicates that recycled PET is more easily reacted with a vinyl acetate-based copolymer to form a comb-like hyperbranched copolymer. It can be seen that the polyethylene terephthalate composite material obtained by the invention has the advantages of high tensile strength, high elongation at break, good impact toughness, and the like, and is suitable for preparing daily necessities and devices with high mechanical properties. .
  • PET (Comparative Example 18) is very brittle, and the composite material (Comparative Example 20) incorporating nano-zinc oxide and vinyl acetate-based copolymer is also inferior in that the nano-zinc oxide induces the PET matrix.
  • the addition of a chain extender can compensate for the degradation of PET, but the increase in toughness of the composite after the addition of chain extender, nano zinc oxide and vinyl acetate based copolymer (Comparative Example 21) is not significant, because of the expansion
  • the chain agent preferentially reacts with the terminal carboxyl group or terminal hydroxyl group of PET, thereby weakening the reaction degree of the vinyl acetate-based copolymer with PET; and the invention adds the chain extender from the feeding port of the twin-screw extruder, which not only ensures The vinyl acetate-based copolymer reacts well with the terminal groups of PET, and further compensates for the catalytic degradation of the recovered zinc by the nano-zinc oxide by subsequent chain extension, so that the prepared composite has excellent toughness.
  • nano zinc oxide, vinyl acetate based copolymer and chain extender in the composite material disclosed in the present invention have a synergistic effect on improving the toughness of the newly synthesized PET material.
  • nano-zinc oxide will catalyze the thermal degradation of newly synthesized PET to produce more active terminal groups. Compared with the newly synthesized PET, it is easier to react with epoxy groups on the vinyl acetate-based copolymer to form comb-like over-expansion in situ.
  • the copolymer, the comb-like hyperbranched copolymer can significantly improve the compatibility and melt viscosity of the vinyl acetate-based copolymer with the PET matrix, and at the same time, the nano-zinc oxide pair is compensated by the chain extender added by the side feed port. Excessive thermal degradation of PET. It can be seen that the PET composite material obtained by the invention not only has excellent toughness, but also has excellent antibacterial ability, and can be widely applied to antibacterial fibers and fabrics, plastic packaging materials, automobile interior parts, medical consumables and the like.
  • PET Comparative Example 24
  • composites with only oxidized nano zinc oxide or unmodified nano zinc oxide are very brittle, but oxidized nano-oxidation
  • the toughness and strength of the zinc material is significantly better than that of the unmodified nano zinc oxide;
  • the composite of the nano zinc oxide and vinyl acetate based copolymer (Comparative Example 27) is also less tough because of nano-oxidation.
  • Degradation of zinc-induced PET polyester matrix leads to embrittlement of the material; the composite material disclosed in the present invention can compensate for the in-situ reaction of the epoxy group on the surface of the oxidized nano zinc oxide with the carboxyl or terminal hydroxyl group of the polyester terminal.
  • the degradation of the ester makes the material toughness excellent; the vinyl acetate-based copolymer reacts with the polyester in situ to form a comb-like hyperbranched copolymer, which can significantly improve the compatibility and melt viscosity of the vinyl acetate-based copolymer with the polyester matrix.
  • the composite material disclosed in the invention has no inhibition zone, because the oxidized nano zinc oxide and the polyester matrix are connected by a chemical bond and do not migrate out from the matrix; at the same time, the nano zinc oxide is modified by epoxidation. The dispersion is more uniform, which makes the composite material more bacteriostatic.
  • polyester composite material obtained by the invention not only has excellent performance, but also has excellent antibacterial ability, and the bacteriostatic agent does not migrate to the outside of the substrate, and can be widely applied to fibers and fabrics, plastic packaging materials, automobile interiors. Parts, medical supplies and other fields.

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Abstract

本发明公开了一种聚酯复合材料及其制备方法，属于聚合物加工与改性技术领域。本发明所述聚酯复合材料包括聚酯65～90份，弹性体5～35份，扩链剂0.05～3份，功能性助剂0.01～5份。本发明的聚酯复合材料不仅具有超高的韧性，还能保持较高的拉伸强度，并且耐水解性能优异，并且可以配合抗菌剂或抗静电剂，能够具备较好抗菌或抗静电附加功能，可广泛应用于纤维织物、塑料结构件、塑料包装或者汽车内饰件领域，前景广阔。

Description

一种聚酯复合材料及其制备方法 技术领域
本发明涉及一种聚酯复合材料及其制备方法，属于聚合物加工与改性技术领域。
背景技术
聚对苯二甲酸丁二醇酯(PBT)和聚对苯二甲酸乙二醇酯(PET)塑料是两大常用的聚酯材料。因其强度高、耐疲劳性、尺寸稳定蠕变小、耐热老化、加工性能好，被广泛应用于汽车、电子电器、工业机械等领域。但PBT和PET也存在着明显的缺点，比如，对缺口十分敏感、缺口冲击强度低，这是它们作为工程塑料的主要缺点，韧性不足也成为推广应用的一大障碍。因此，对PBT和PET的增韧改性研究一直是PBT和PET高性能化的一个重要内容。与官能化弹性体熔融共混是改善聚酯韧性的一种简单、经济且有效的方法。因为官能化弹性体上的官能团会与聚酯上的端基(羧基或羟基)反应实现原位增容，从而提高增韧效率。专利CN201410779308和《低模温玻纤增强PET复合材料的制备与表征》中用官能化弹性体乙烯-丙烯酸正丁酯-甲基丙烯酸缩水甘油酯三元共聚物来改性聚酯，《中空玻璃微珠含量对回收聚对苯二甲酸乙二醇酯/聚碳酸酯基复合泡沫材料性能的影响》中用乙烯-丙烯酸甲酯-甲基丙烯酸缩水甘油酯三元共聚物来增韧PET，然而上述制备方法所得的聚酯材料的缺口冲击强度仍不能满足一些对应用要求较高的产品，且弹性体的加入会明显降低聚酯材料的拉伸强度。同时，PBT等聚酯材料由于存在端羧基、端羟基及大量的酯键，往往不耐水解，因而难以在湿度较大的环境下应用。
弹性体通常是以球状粒子分散在聚酯基体中，形成普通的海岛结构，其增韧效率往往不如“双连续”或“类双连续”的相形态。因此，使聚酯/弹性体共混材料的相形态由海岛结构向双连续相结构转变是进一步提高增韧效率的关键。
此外，随着经济的快速发展，人们对材料的附加功能需求也越来越迫切，比如抗菌、抗静电等功能性质。在抗菌方面，人们通过在PBT材料中加入ZnO来改善其抗菌性，如专利CN 102838852 A在PBT材料中加入含有氧化锌的复合抗菌剂来赋予材料的抗菌性能，然而在熔融加工的过程中，氧化锌的加入会催化PBT的热降解，使材料的韧性显著降低，限制了PBT材料的应用。另外，用于电器外壳等领域的聚酯材料在使用过程中，尤其是在低湿度的环境下，易在材料表面积累电荷，并在一定条件下会释放静电，对人体和电器造成伤害。专利CN 102675836 A发明了一种导电/抗静电聚酯PET复合材料，但其碳纳米管的添加量多，且制备过程繁琐，不利于实现产业化生产。因此，极有必要发明一种韧性稳定且具备较好附加功能的复合材料。
发明内容
针对现有技术的不足，本发明提供了一种聚酯复合材料，在保证与弹性体原位反应增容的同时，使共混材料的相形态由普通的海岛结构向类双连续结构转变，获得了超韧的聚酯复合材料，且还能保持较高的拉伸强度。此外，本发明的组合物还具有优异的耐水解性，可广泛应用于塑料结构件、塑料包装或者汽车内饰件领域。
本发明提供的聚酯复合材料，是先将聚酯和弹性体熔融共混，保证弹性体上的官能团与聚酯的端基(羧基或羟基)充分反应，实现原位反应增容；然后加入扩链剂继续熔融共混，扩大聚酯的分子量，从而提高聚酯基体的粘度，使弹性体由原先的分散相向类连续相转变，形成类双连续结构，从而进一步提高弹性体对聚酯的增韧效果。此外，由于聚酯基体的分子量的扩大，共混物的拉伸强度也得到了明显的提升。由于官能化弹性体和扩链剂与聚酯的端基发生反应，消耗了大量的端羧基和端羟基，从而也显著提高了组合物的耐水解性。
本发明的第一个目的是提供一种聚酯材料或工程塑料组合物，所述材料或组合物的配方按照重量份数配比，包括：聚酯65～90份，弹性体5～35份，扩链剂0.05～3份，功能性助剂0.01～5 份；
所述材料或组合物的制备方法，包括：
将聚酯、弹性体和功能性助剂根据重量份数配比混匀，然后熔融挤出，按照重量份配比加入扩链剂，再进行熔融挤出，即可得到材料；
或者，将聚酯、弹性体和功能性助剂根据重量份数配比混匀，然后熔融共混，按照重量份配比加入扩链剂，再进行熔融共混，即可得到材料；
所述弹性体为含有环氧基团或酸酐基团的弹性体；
所述弹性体含有醋酸乙烯酯的结构单元。
在本发明的一种实施方式中，所述聚酯包括聚对苯二甲酸乙二醇酯(PET)、聚对苯二甲酸丁二醇酯(PBT)和聚碳酸酯(PC)中的至少一种。
在本发明的一种实施方式中，所述聚酯的特性粘度为0.3～1.5dL/g。
在本发明的一种实施方式中，所述扩链剂包括含有多个环氧基团的化合物、含有多个异氰酸酯基团的化合物和酸酐类化合物中的至少一种。
在本发明的一种实施方式中，所述功能性助剂包括抗氧剂、润滑剂、成核剂、抗水解剂和酯交换抑制剂中的至少一种。
在本发明的一种实施方式中，所述抗氧剂包括四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯、三[2，4-二叔丁基苯基]亚磷酸酯和β-(3，5-二叔丁基-4-羟基苯基)丙酸正十八碳醇酯中的至少一种。
在本发明的一种实施方式中，所述润滑剂包括固体石蜡、液体石蜡、聚乙烯蜡、硬脂酸酰胺、甲撑双硬脂酸酰胺、N，N-乙撑双硬脂酸酰胺和季戊四醇硬脂酸酯中的至少一种。
在本发明的一种实施方式中，所述成核剂包括滑石粉、硬脂酸镁、苯甲酸钠和Surlyn8920中的至少一种。
在本发明的一种实施方式中，所述抗水解剂包括N,N'-二(2,6-二异丙基苯基)碳二亚胺；所述酯交换抑制剂为磷酸二氢钠、亚磷酸三苯酯和焦磷酸二氢二钠中的至少一种。
在本发明的一种实施方式中，所述组合物的制备方法具体包括：
将聚酯、弹性体和功能性助剂根据重量份配比预先混均，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂按照重量份配比加入双螺杆挤出机啮合段中部，经过连续熔融挤出即可得到复合材料，其中熔融挤出温度为聚酯熔点以上1～30℃，螺杆转速为100～350rpm；
或者，将聚酯、弹性体和功能性助剂根据重量份配比加入密炼机内进行熔融共混2～5分钟，然后加入扩链剂继续共混1～5分钟即可得到一种工程塑料组合物，其中熔融共混温度为聚酯熔点以上1～30℃。
在本发明的一种实施方式中，当聚酯选用PBT时，所述材料还包括0.1～4份抗菌剂，所述抗菌剂包括氧化锌、氧化银、二氧化钛、氧化铈中的一种或多种。
在本发明的一种实施方式中，所述材料的制备方法，包括：
将PBT、弹性体和抗菌剂根据重量份配数比混匀，然后挤出，按照重量份配比加入扩链剂，再经过连续熔融挤出即可得到材料；
或者，将PBT、弹性体和抗菌剂根据重量份数配比混匀，进行熔融共混，然后按照重量份配比加入扩链剂继续共混，即可得到材料。
在本发明的一种实施方式中，所述熔融共混的温度为聚酯熔点以上1～30℃。
本发明的第二个目的是提供一种PBT复合材料，所述复合材料的配方，按照重量份配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，抗菌剂0～4份，扩链剂0～3份；所述抗菌剂包括氧化锌、氧化银、二氧化钛、氧化铈中的一种或多种。
在本发明的一种实施方式中，所述复合材料的配方，按照重量份配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，抗菌剂0.1～4份，扩链剂0.05～3份，功能性助剂0.01～5份。
在本发明的一种实施方式中，所述复合材料的制备方法包括：将PBT、醋酸乙烯酯基共聚物和抗菌剂根据重量份配数比混匀，然后挤出，按照重量份配比加入扩链剂，再经过连续熔融挤出即可得到材料；
或者，将PBT、醋酸乙烯酯基共聚物和抗菌剂根据重量份数配比混匀，进行熔融共混，然后按照重量份配比加入扩链剂继续共混，即可得到材料。
在本发明的一种实施方式中，所述复合材料的制备方法具体包括：
将PBT、醋酸乙烯酯基共聚物和抗菌剂根据重量份配比在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂加入双螺杆挤出机啮合段中部，经过连续熔融挤出即可得到材料；
或者，将PBT、醋酸乙烯酯基共聚物和抗菌剂根据重量份配比在室温下预混均匀，再将预混物加入密炼机内熔融共混2～5分钟，然后加入扩链剂继续共混1～5分钟即可得到材料。
在本发明的一种实施方式中，熔融共混的温度为PBT熔点以上1～30℃，螺杆转速为100～350rpm。
在本发明的一种实施方式中，所述复合材料的配方，按照重量份配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，0.1～5份环氧化碳基粒子，扩链剂0.05～3份，0.01～5份功能性助剂。
在本发明的一种实施方式中，所述复合材料的制备方法包括：将PBT、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融挤出，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融挤出，最后按照重量份数配比加入扩链剂，继续熔融挤出，即可得到材料；
或者，将PBT、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融共混，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融共混，最后按照重量份数配比加入扩链剂，继续熔融共混，即可得到材料。
在本发明的一种实施方式中，所述复合材料的制备方法具体包括：
将PBT、环氧化碳基粒子和功能性助剂根据重量份配比预先混均，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将醋酸乙烯酯基共聚物按照重量份配比加入双螺杆挤出机熔融共混，再通过二号侧喂料将扩链剂按照重量份配比加入双螺杆挤出机经过连续熔融挤出即可得到材料，其中熔融挤出温度为PBT熔点以上1～30℃，螺杆转速为100～350rpm；
或者，将PBT、环氧化碳基粒子和功能性助剂根据重量份配比加入密炼机内进行熔融共混1～3分钟，然后按照重量份配比加入醋酸乙烯酯基共聚物继续共混1～4分钟，最后按照重量份配比加入扩链剂继续共混1～3分钟即可得到材料，其中熔融共混温度为PBT熔点以上1～30℃。
在本发明的一种实施方式中，所述复合材料的配方，按照重量份配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，环氧化纳米氧化锌0.1～4份。
在本发明的一种实施方式中，所述醋酸乙烯酯基共聚物中至少还含有甲基丙烯酸缩水甘油酯和乙烯结构单元。
在本发明的一种实施方式中，所述醋酸乙烯酯基共聚物中醋酸乙烯酯的质量含量为45～75％，甲基丙烯酸缩水甘油酯的质量百分含量为0.5～10％。
在本发明的一种实施方式中，所述醋酸乙烯酯基共聚物还可以包括乙烯-醋酸乙烯酯二元共聚物。
在本发明的一种实施方式中，所述乙烯-醋酸乙烯酯二元共聚物中醋酸乙烯酯的质量含量为45～75％。
在本发明的一种实施方式中，所述聚酯的特性粘度为0.3～1.5dL/g。
在本发明的一种实施方式中，所述抗菌剂氧化物的粒径为10～3000纳米。
在本发明的一种实施方式中，所述抗菌剂氧化物的粒径优选为10～300纳米。
在本发明的一种实施方式中，所述环氧化碳基粒子为环氧化多壁碳纳米管、环氧化石墨 烯、环氧化炭黑中的至少一种。
在本发明的一种实施方式中，所述环氧化碳基粒子的直径为10～300纳米。
在本发明的一种实施方式中，所述功能性助剂包括抗氧剂、润滑剂、成核剂、抗水解剂和酯交换抑制剂中的至少一种。
在本发明的一种实施方式中，所述扩链剂为含有多个环氧基团的化合物、含有多个异氰酸酯基团的化合物和酸酐类化合物中的至少一种。
在本发明的一种实施方式中，所述抗氧剂是四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯、三[2，4-二叔丁基苯基]亚磷酸酯和β-(3，5-二叔丁基-4-羟基苯基)丙酸正十八碳醇酯中的至少一种。
在本发明的一种实施方式中，所述润滑剂为固体石蜡、液体石蜡、聚乙烯蜡、硬脂酸酰胺、甲撑双硬脂酸酰胺、N，N-乙撑双硬脂酸酰胺和季戊四醇硬脂酸酯中的至少一种。
在本发明的一种实施方式中，所述成核剂为滑石粉、硬脂酸镁、苯甲酸钠和Surlyn8920中的至少一种。
在本发明的一种实施方式中，熔融共混的温度为PBT的熔点以上1～30℃。
本发明的第三个目的是提供一种PET复合材料，其特征在于，所述材料的配方按照重量份数配比，包括：回收PET 70-95份，醋酸乙烯酯共聚物5-30份，所述回收PET的特性粘度为0.3～1.0dL/g，所述醋酸乙烯酯基共聚物中醋酸乙烯酯的质量含量为45～75％。
在本发明的一种实施方式中，所述材料中还包括环氧化纳米氧化锌0.1～4份或者纳米氧化锌0.1～4份。
在本发明的一种实施方式中，所述材料中还包括扩链剂0.05-3份。
在本发明的一种实施方式中，当材料包括环氧化纳米氧化锌时，所述材料的制备方法包括：
将PET、醋酸乙烯酯基共聚物、环氧化纳米氧化锌根据重量份配比在室温下预混均匀，然后通过双螺杆挤出机熔融挤出即可得到复合材料，其中熔融挤出温度为PET熔点以上1～30℃，螺杆转速为100～350rpm；
或者，将PET、醋酸乙烯酯基共聚物、环氧化纳米氧化锌根据重量份配比加入密炼机内进行熔融共混3～10分钟，即可得到复合材料，其中熔融共混温度为PET熔点以上1～30℃。
在本发明的一种实施方式中，所述环氧化纳米氧化锌表面至少含有1个环氧基团，其制备方法包括：
将环氧纳米氧化锌、溶剂和环氧基化合物按照重量份配比5～15:65～85:2～30混合，在30～70℃下反应1～24小时，提纯后得到环氧化纳米氧化锌；
或者，将环氧纳米氧化锌、溶剂和环氧基化合物按照重量份配比80～99：0.5～20：0.5～5高速搅拌处理2～10分钟即可得到环氧化纳米氧化锌；
所述溶剂为水、甲醇、乙醇中的至少一种。
在本发明的一种实施方式中，所述环氧基化合物中至少含有一个-Si-O-基团，所述纳米氧化锌粒径为10～300纳米。
在本发明的一种实施方式中，当材料包括纳米氧化锌时，所述材料的制备方法包括：
将PET、醋酸乙烯酯基共聚物、纳米氧化锌根据重量份配比在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂按照重量份配比加入双螺杆挤出机啮合段中部，经过连续熔融挤出即可得到一种韧性PET抗菌复合材料，其中熔融挤出温度为PET熔点以上1～30℃，螺杆转速为100～350rpm；
或者，将PET、醋酸乙烯酯基共聚物、纳米氧化锌根据重量份配比加入密炼机内进行熔融共混2～5分钟，然后加入扩链剂继续共混1～5分钟即可得到一种韧性PET抗菌复合材料，其中熔融共混温度为PET熔点以上1～30℃。
在本发明的一种实施方式中，所述材料还包括环氧化碳基粒子0.1～5份，功能性助剂0.01～5份，扩链剂0.05～3份。
在本发明的一种实施方式中，所述材料的制备方法包括：
将PET、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融挤出，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融挤出，最后按照重量份数配比加入扩链剂，继续熔融挤出，即可得到材料；
或者，将PET、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融共混，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融共混，最后按照重量份数配比加入扩链剂，继续熔融共混，即可得到材料。
在本发明的一种实施方式中，所述材料的制备方法具体包括：
将PET、环氧化碳基粒子和功能性助剂根据重量份配比预先混均，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将醋酸乙烯酯基共聚物按照重量份配比加入双螺杆挤出机熔融共混，再通过二号侧喂料将扩链剂按照重量份配比加入双螺杆挤出机经过连续熔融挤出即可得到材料，其中熔融挤出温度为PET熔点以上1～30℃，螺杆转速为100～350rpm；
或者，将PET、环氧化碳基粒子和功能性助剂根据重量份配比加入密炼机内进行熔融共混1～3分钟，然后按照重量份配比加入醋酸乙烯酯基共聚物继续共混1～4分钟，最后按照重量份配比加入扩链剂继续共混1～3分钟即可得到材料，其中熔融共混温度为PET熔点以上1～30℃。
在本发明的一种实施方式中，所述醋酸乙烯酯基共聚物中至少还含有甲基丙烯酸缩水甘油酯和乙烯结构单元，其中甲基丙烯酸缩水甘油酯的质量百分含量为0.5～10％。
在本发明的一种实施方式中，所述醋酸乙烯酯基共聚物还可以包括乙烯-醋酸乙烯酯二元共聚物。在本发明的一种实施方式中，所述环氧化碳基粒子为环氧化多壁碳纳米管、环氧化石墨烯、环氧化炭黑中的至少一种。
在本发明的一种实施方式中，所述环氧化碳基粒子的直径为10～300纳米。
在本发明的一种实施方式中，所述扩链剂包括含有多个环氧基团的化合物、含有多个异氰酸酯基团的化合物和酸酐类化合物中的至少一种。
在本发明的一种实施方式中，所述功能性助剂包括抗氧剂、润滑剂、成核剂、抗水解剂和酯交换抑制剂中的至少一种。
在本发明的一种实施方式中，所述抗氧剂包括四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯、三[2，4-二叔丁基苯基]亚磷酸酯和β-(3，5-二叔丁基-4-羟基苯基)丙酸正十八碳醇酯中的至少一种。
在本发明的一种实施方式中，所述润滑剂包括固体石蜡、液体石蜡、聚乙烯蜡、硬脂酸酰胺、甲撑双硬脂酸酰胺、N，N-乙撑双硬脂酸酰胺和季戊四醇硬脂酸酯中的至少一种。
在本发明的一种实施方式中，所述成核剂包括滑石粉、硬脂酸镁、苯甲酸钠和Surlyn8920中的至少一种。
在本发明的一种实施方式中，所述抗水解剂包括N,N'-二(2,6-二异丙基苯基)碳二亚胺；所述酯交换抑制剂为磷酸二氢钠、亚磷酸三苯酯和焦磷酸二氢二钠中的至少一种。
本发明的第四个目的是提供一种塑料包装或者塑料结构件，所述塑料包装或者塑料结构件包含上述的复合材料。
本发明的第五个目的是提供一种汽车内饰件，所述汽车内饰件包含上述的复合材料。
本发明的第六个目的是提供一种电器外壳，其特征在于，所述电器外壳包含上述的复合材料。
本发明的第七个目的是提供一种抗菌纤维或织物，所述抗菌纤维或织物包含上述的复合材料。
本发明的有益效果：
1、本发明的聚酯复合材料中由于醋酸乙烯酯基共聚物和扩链剂与聚酯的端基发生反应，消耗了大量的端羧基和端羟基，从而显著提高了组合物的耐水解性。
2、本发明聚酯材料是先将聚酯和弹性体熔融共混，保证弹性体上的官能团与聚酯的端基(羧基或羟基)充分反应，实现原位反应增容。然后加入扩链剂继续熔融共混，扩大聚酯的分子量，从而提高聚酯基体的粘度，使弹性体由原先的分散相向类连续相转变，形成类双连续结构，从而进一步提高弹性体对聚酯的增韧效果。此外，由于聚酯基体的分子量的扩大，组合物的拉伸强度也得到了明显的提升。
3、本发明聚酯材料是先将聚酯和环氧化碳基粒子熔融共混，然后再加入弹性体共混，这样能使碳基粒子选择性地分布在聚酯基体中，并且保证弹性体与聚酯的端基充分反应，实现原位反应增容；最后加入扩链剂继续熔融共混，扩大聚酯的分子量，从而提高聚酯基体的粘度，使弹性体的粒径和粒间距显著减小，从而进一步提高弹性体对聚酯的增韧效果；同时，弹性体粒径和粒间距的减小，使选择性分散在聚酯基体中的碳基粒子也更容易形成网络导电结构，从而能够在碳基粒子的添加量很低的条件下使聚酯材料的电导率达到抗静电的范围，即10 -11～10 -4S/cm。
4、本发明聚酯材料通过金属氧化物类抗菌剂和扩链剂的添加，材料的抑菌性能得到明显提高，同时能弥补抗菌剂对聚酯基体的热降解，从而使聚酯复合材料保持高韧性。
5、本发明聚酯复合材料通过环氧化纳米氧化锌的添加，使材料的抑菌性能得到明显提高，并且有效抑制了氧化锌在聚酯基体内的迁移；同时环氧化纳米氧化锌还能与聚酯发生原位反应，削弱了氧化锌对聚酯的降解作用，使材料具有优异的机械性能，如冲击强度。
6、本发明聚酯复合材料的制备方法简单高效，易于实现工业化生产，前景广阔。
具体实施方式
下面结合实施例和对比例详细描述本发明，但实施例不应限制本发明的范围。
实施例1
将PBT 80份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将1份扩链剂ADR4370加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到复合材料。
实施例2
将PET 80份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份、三[2，4-二叔丁基苯基]亚磷酸酯0.2份和β-(3，5-二叔丁基-4-羟基苯基)丙酸正十八碳醇酯0.2份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将0.8份扩链剂ADR4468加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为255℃，螺杆转速为180rpm)即可得到复合材料。
实施例3
将PBT 75份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物10份、乙烯-醋酸乙烯酯二元共聚物15份、四[β-(3,5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.15份、三[2,4-二叔丁基苯基]亚磷酸酯0.15份和固体石蜡0.1份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将1.2份扩链剂六亚甲基二异氰酸酯加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为235℃，螺杆转速为210rpm)即可得到复合材料。
实施例4
将PET 85份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物3份、乙烯-醋酸乙烯酯二元共聚物12份、四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.2份、聚乙烯蜡0.1份和苯甲酸钠0.3份加入密炼机内熔融共混3分钟，然后加入1.3份扩链剂均苯四甲酸酐继续共混2分钟(共混温度为260℃)即可得到复合材料。
实施例5
将PBT 75份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物25份、三[2，4-二叔 丁基苯基]亚磷酸酯0.4份、硬脂酸酰胺0.2份和硬脂酸镁0.3份加入密炼机内熔融共混3分钟，然后加入0.7份扩链剂ADR4468继续共混3分钟(共混温度为240℃)即可得到一种复合材料。
实施例6
在实施例1的基础上，将乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物替换成乙烯-丙烯酸正丁酯-甲基丙烯酸缩水甘油酯三元共聚物(即乙烯-正丁基丙烯酸酯-甲基丙烯酸缩水甘油酯三元共聚物)，其他组分和条件保持一致，制备得到一种聚酯复合材料。
对比例1
参照实施例1，不添加官能化弹性体和扩链剂制备复合材料：将PBT 100份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份由双螺杆挤出机连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
对比例2
参照实施例1，不添加扩链剂制备复合材料：将PBT 80份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
对比例3
参照实施例1，以乙烯-醋酸乙烯酯二元共聚物作为弹性体制备复合材料：将PBT 80份、乙烯-醋酸乙烯酯二元共聚物20份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将1份扩链剂ADR4370加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
对比例4
参照实施例1，一次性混合制备复合材料：将PBT 80份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份、四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份和ADR4370扩链剂1份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
对比例5
参照实施例1中复合材料的配方组分，采用先扩链剂扩链，后加入弹性体的方法制备复合材料：将PBT 80份、1份扩链剂ADR4370和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
将上述实施例1-3和对比例1-5挤出得到的复合材料在注塑机上注射标准样条用以拉伸和冲击性能测试，测试结果如表1所示(老化0h)。将实施例4-6得到的复合材料通过平板硫化机热压成型，并根据相关标准裁成标准样条用以拉伸和冲击性能测试，测试结果如表1所示(老化0h)。将实施例和对比例的样条置于环境老化箱中在70℃/80％RH条件下进行恒温恒湿老化实验，每隔一定时间(24h、48h、72h、96h)取出一批样品，对其拉伸性能和冲击性能进行测定，评估复合材料的耐水解性，测试结果如表1所示。
表1复合材料性能测定
实施例 老化0h 老化24h 老化48h 老化72h 老化96h
实施例1 38,480,90 38,420,87 36,380,83 32,210,71 24,86,46
实施例2 40,460,86 39,430,85 37,350,81 25,93,39 15,45,16
实施例3 34,375,95 33,340,93 31,295,88 19,102,42 11,23,9
实施例4 41,320,75 39,280,72 36,234,65 35,200,54 21,97,32
实施例5 35,430,88 34,413,84 32,384,72 28,280,65 16,113,28
实施例6 36,345,72 35,310,70 33,242,67 29,175,57 18,69,29
对比例1 50,8,3 30,5,2 13,2,1 -- --
对比例2 34,180,61 25,78,32 14,25,8 -- --
对比例3 36,22,5 35,18,4 33,15,4 19,9,2 10,4,1
对比例4 36,51,12 36,44,11 34,38,9 23,18,5 11,8,2
对比例5 36,26,7 35,21,6 34,18,4 21,10,2 11,5,1
注：表格中每个格子里的三个数字从左到右分别表示拉伸强度、断裂伸长率和缺口冲击强度的值，单位分别是MPa、％和kJ/m 2。
实施例和对比例中所得到复合材料的拉伸性能(拉伸强度和断裂伸长率)根据GB/T1040-1992标准测试，拉伸速率为50mm/min；缺口冲击强度根据GB/T1043-1993标准测试，缺口深度为2mm。所有力学性能均在23℃环境中放置24小时后测得。所用乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物由朗盛化学公司提供，其余化学品为普通市售产品。
由表1中数据(老化0h)可知，纯PBT(对比例1)很脆；仅加了乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物后的复合材料(对比例2)的韧性虽有较明显提高，但仍远不如本发明的复合材料(如实施例1)。与纯PBT和对比例2中的复合材料相比，本发明的断裂伸长率分别提高了59.0倍和1.7倍，缺口冲击强度分别提高了28.0倍和0.5倍。这是因为本发明的制备方法是先使聚酯基体与官能化弹性体充分反应实现原先反应增容，后又加入适量扩链剂提高聚酯的分子量，从而提高基体的粘度，使共混物的相形态由原先的海岛结构向类双连续结构转变，从而进一步提高了弹性体对聚酯基体的增韧效果。此外，由于聚酯基体的分子量的显著增大，使所得复合材料的拉伸强度也明显高于对比例2中的复合材料。然而，若没有弹性体上的官能团与聚酯反应产生增容作用，就算在后续加入扩链剂也不能起到有效的增韧效果(如对比例3)。而将聚酯、弹性体和扩链剂同时加入挤出机主喂料口进行共混，得到的复合材料(对比例4)的韧性也远不如本发明(如实施例1)。因为官能化弹性体和扩链剂与聚酯的反应存在竞争，而分子量较小且官能团较多的扩链剂会优先与聚酯反应，增大反应的空间位阻，使得弹性体很难再与聚酯反应，起不到很好的增容作用。此外，采用先加入扩链剂扩链，后加入弹性体得到的复合材料(对比例5)的韧性也很差。由此可见，官能化弹性体与聚酯充分反应而产生的原位增容作用与扩链剂的扩链作用对聚酯的增韧存在协同效应。从实施例1和实施例6还可以看出，同样是官能化弹性体，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物比乙烯-丙烯酸正丁酯-甲基丙烯酸缩水甘油酯三元共聚物的增韧效果更好。
由表1中数据可知，纯PBT(对比例1)和仅加了乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物后的复合材料(对比例2)的耐水解性很差，在老化24h后力学性能就显著下降，而本发明的复合材料的耐水解性能优异，在老化72h或96h之后力学性能才有明显的下降。端羧基和端羟基的存在会促进聚酯的水解，而本发明利用官能化弹性体和扩链剂与聚酯端基的反应，消耗了大量的端羧基和端羟基，所以能够显著提高复合材料的耐水解性能。
可见，通过本发明获得的聚酯复合材料不仅具有优异的韧性，还能保持较高的拉伸强度， 并且耐水解性能优异，可广泛应用于塑料结构件、塑料包装、汽车内饰件等领域。
实施例7
将PBT 80份、环氧化多壁碳纳米管0.4份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份加入双螺杆挤出机熔融共混，再通过二号侧喂料将1份扩链剂ADR4370加入双螺杆挤出机经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到聚酯材料。
实施例8
将PET 80份、环氧化多壁碳纳米管0.3份、三[2，4-二叔丁基苯基]亚磷酸酯0.2份和β-(3，5-二叔丁基-4-羟基苯基)丙酸正十八碳醇酯0.2份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份加入双螺杆挤出机熔融共混，再通过二号侧喂料将0.8份扩链剂ADR4468加入双螺杆挤出机经过连续熔融挤出(挤出温度为255℃，螺杆转速为180rpm)即可得到聚酯材料。
实施例9
将PBT 75份、环氧化石墨烯0.3份、四[β-(3,5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.15份、三[2,4-二叔丁基苯基]亚磷酸酯0.15份和固体石蜡0.1份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物8份和乙烯-醋酸乙烯酯二元共聚物17份加入双螺杆挤出机熔融共混，再通过二号侧喂料将1.2份扩链剂六亚甲基二异氰酸酯加入双螺杆挤出机经过连续熔融挤出(挤出温度为235℃，螺杆转速为210rpm)即可得到聚酯材料。
实施例10
将PET 85份、环氧化多壁碳纳米管0.5份、四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.2份、聚乙烯蜡0.1份和苯甲酸钠0.3份加入密炼机内进行熔融共混2分钟，然后加入乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物15份继续共混3分钟，最后加入1.3份扩链剂均苯四甲酸酐继续共混2分钟(共混温度为260℃)即可得到聚酯材料。
实施例11
将PET 70份、环氧化多壁碳纳米管0.6份、四[β-(3,5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.2份、三[2,4-二叔丁基苯基]亚磷酸酯0.2份和磷酸二氢钠0.2份加入密炼机内进行熔融共混1分钟，然后加入乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物10份和乙烯-醋酸乙烯酯二元共聚物20份继续共混4分钟，最后加入0.8份扩链剂ADR4370继续共混2分钟(共混温度为250℃)即可得到聚酯材料。
实施例12
将PBT 75份、环氧化炭黑0.35份、三[2，4-二叔丁基苯基]亚磷酸酯0.4份、硬脂酸酰胺0.2份和硬脂酸镁0.3份加入密炼机内进行熔融共混1.5分钟，然后加入乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物25份继续共混3分钟，最后加入0.7份扩链剂ADR4468继续共混1.5分钟(共混温度为240℃)即可得到聚酯材料。
对比例6
参照实施例7，以乙烯-醋酸乙烯酯二元共聚物作为弹性体制备聚酯材料：将PBT 80份、环氧化多壁碳纳米管0.4份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将乙烯-醋酸乙烯酯二元共聚物20份加入双螺杆挤出机熔融共混，再通过二号侧喂料将1份扩链剂ADR4370加入双螺杆挤出机经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到一种聚酯材料。
对比例7
参照实施例7，不添加环氧化碳基粒子制备聚酯材料：将PBT 80份和四[β-(3，5-二叔丁 基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份加入双螺杆挤出机熔融共混，再通过二号侧喂料将1份扩链剂ADR4370加入双螺杆挤出机经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到聚酯材料。
对比例8
参照实施例7，不添加扩链剂制备聚酯材料：将PBT 80份、环氧化多壁碳纳米管0.4份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过一号侧喂料将乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份加入双螺杆挤出机经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到一种聚酯材料。
对比例9
参照实施例7，同时加入环氧化碳基粒子和弹性体制备聚酯材料：将PBT 80份、环氧化多壁碳纳米管0.4份、乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物20份和四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，再通过二号侧喂料将1份扩链剂ADR4370加入双螺杆挤出机经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到一种聚酯材料。
将上述实施例7-9和对比例6-9挤出得到的聚酯材料在注塑机上注射标准样条用以拉伸、冲击和导电性能测试，测试结果如表2所示。将实施例10-12得到的复合材料通过平板硫化机热压成型，并根据相关标准裁成标准样条用以拉伸、冲击和导电性能测试，测试结果如表2所示。将实施例和对比例的样条置于环境老化箱中在70℃/80％RH条件下进行恒温恒湿老化实验，在48h后取出样条，对其拉伸性能和冲击性能进行测定，评估聚酯材料的耐水解性，测试结果如表2所示。
表2聚酯材料性能测定
Figure PCTCN2018118179-appb-000001
实施例和对比例中所得到聚酯材料的拉伸性能(拉伸强度和断裂伸长率)根据GB/T1040-1992标准测试，拉伸速率为50mm/min；缺口冲击强度根据GB/T1043-1993标准 测试，缺口深度为2mm。所有力学性能均在23℃环境中放置24小时后测得。聚酯材料的电导率采用四探针电导率仪测得。所用乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物由朗盛化学公司提供，其余化学品为普通市售产品。
由表2中数据可知，纯PBT(对比例1)很脆且电导率极低；仅加了乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物和扩链剂后的聚酯材料(对比例7)的韧性虽有明显提高，但其电导率仍是极低。若将本发明中的弹性体乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯三元共聚物用乙烯-醋酸乙烯酯二元共聚物来替代(对比例6)，由于弹性体与聚酯基体之间不存在界面反应，使得两相之间的相容性很差，且弹性体的粒径和粒间距大，使得聚酯材料的韧性和电导率都远远不如本发明的聚酯材料(如实施例7)。若聚酯材料中不加入扩链剂(对比例8)，在熔融共混过程中基体的粘度不高，不能进一步减小弹性体粒子的粒径和粒间距，所以对比例8的聚酯材料的力学性能和电导率也明显不如本发明。将环氧化碳基粒子和弹性体同时加入聚酯中共混得到的聚酯材料(对比例9)由于不能将碳基粒子选择性分布在聚酯基体中，所以很难形成导电网络，因此对比例9的聚酯材料的电导率也远远不如本发明。与纯PBT(对比例1)相比，本发明(如实施例7)的断裂伸长率和缺口冲击强度分别提高了62.8倍和29.7倍，电导率提高了8个数量级，从原先的绝缘材料转变为抗静电材料。此外，由于扩链剂使聚酯基体的分子量显著增大，加上碳基粒子的增强作用，本发明的聚酯材料仍能保持很高的拉伸强度。
由表2中数据可知，纯PBT(对比例1)的耐水解性很差，在老化48h后力学性能就显著下降；而本发明的聚酯材料(如实施例7)的耐水解性能优异，在老化48之后力学性能只有轻微地下降。端羧基和端羟基的存在会促进聚酯的水解，而本发明利用环氧化碳基粒子、官能化弹性体和扩链剂与聚酯端基的反应，消耗了大量的端羧基和端羟基，所以能够显著提高聚酯的耐水解性能。
可见，通过本发明获得的聚酯材料不仅具有优异的力学性能，还能在导电碳基粒子添加量很低的情况下获得抗静电性能，并且耐水解性能优异，可广泛应用于塑料结构件、电器外壳等领域。
实施例13
将PBT 80份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)20份在室温下预混均匀，然后将预混物由双螺杆挤出机连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到PBT复合材料。
实施例14
将PBT 75份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为50％，甲基丙烯酸缩水甘油酯质量含量为5％)8份，乙烯-醋酸乙烯酯二元共聚物(醋酸乙烯酯质量含量为50％)17份，β-(3，5-二叔丁基-4-羟基苯基)丙酸正十八碳醇酯0.2份，季戊四醇硬脂酸酯0.1份在室温下预混均匀，然后将预混物由双螺杆挤出机连续熔融挤出(挤出温度为235℃，螺杆转速为180rpm)即可得到PBT复合材料。
实施例15
将PBT 80份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)5份，乙烯-醋酸乙烯酯二元共聚物(醋酸乙烯酯质量含量为50％)15份，四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.5份在室温下预混均匀，然后将预混物加入密炼机内进行熔融共混8分钟(共混温度为230℃)，即可得到PBT复合材料。
实施例16
将PBT 85份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)15份，三[2，4-二叔丁基苯基]亚磷酸酯0.4份，硬脂酸酰胺0.2份，苯甲酸钠1份在室温下预混均匀，然后将预混物加入密炼机内进行熔融共混5分钟(共混温度为240℃)，即可得到PBT复合材料。
对比例10
将PBT 100份由双螺杆挤出机连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到PBT材料。
对比例11
将PBT 80份，乙烯-丙烯酸正丁酯-甲基丙烯酸缩水甘油酯共聚物20份在室温下预混均匀，然后将预混物由双螺杆挤出机连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到复合材料。
将上述实施例13-14和对比例10-11挤出得到的PBT复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，测试结果如表3所示。将实施例15-16得到的PBT复合材料做熔融指数测试，并通过平板硫化机热压成型，根据相关标准裁成标准样条用以拉伸和冲击性能测试，测试结果如表3所示。
表3实施例12-16和对比例10-11得到的PBT复合材料性能测试
Figure PCTCN2018118179-appb-000002
实施例17
将PBT 80份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)20份，氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将0.75份扩链剂ADR4370加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)即可得到复合材料。
实施例18
将PBT 80份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)20份，氧化锌4份(粒径为50nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将1.2份扩链剂ADR4370加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为235℃，螺杆转速为150rpm)即可得到复合材料。
实施例19
将PBT 70份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)10份，乙烯-醋酸乙烯酯二元共聚物(醋酸乙烯酯质量含量为60％)20份，二氧化钛2.5份(粒径为100nm)，四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份，聚乙烯蜡0.1份，滑石粉1份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将1.5份扩链剂SAG-008加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为245℃，螺杆转速为200rpm)即可得到复合材料。
实施例20
将PBT 75份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)5份，乙烯-醋酸乙烯酯二元共聚物(醋酸乙烯酯质量含量为50％)20 份，氧化银1份(粒径为20nm)在室温下预混均匀，再将预混物加入密炼机内熔融共混3分钟，然后加入0.5份扩链剂ADR4468继续共混2分钟(共混温度为235℃)即可得到复合材料。
实施例21
将PBT 85份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为50％，甲基丙烯酸缩水甘油酯质量含量为5％)15份，氧化铈3份(粒径为60nm)，三[2，4-二叔丁基苯基]亚磷酸酯0.25份，苯甲酸钠2.5份在室温下预混均匀，再将预混物加入密炼机内进行熔融共混2.5分钟，然后加入扩链剂六亚甲基二异氰酸酯0.5份继续共混2.5分钟(共混温度为235℃)即可得到复合材料。
对比例12
将PBT 100份，氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将0.75份扩链剂ADR4370加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
对比例13
将PBT 80份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)20份，氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
对比例14
将PBT 80份，醋酸乙烯酯基共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3.1％)20份，氧化锌2份(粒径为30nm)，扩链剂ADR43700.75份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，经过连续熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
将上述实施例17-19和对比例12-14挤出得到的PBT复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表4所示。将实施例20-21得到的PBT复合材料做熔融指数测试，并通过平板硫化机热压成型，根据相关标准裁成标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表4所示。
表4实施例17-21和对比例12-14得到的PBT复合材料性能测试
Figure PCTCN2018118179-appb-000003
Figure PCTCN2018118179-appb-000004
实施例和对比例中拉伸性能(拉伸强度和断裂伸长率)根据GB/T1040-1992标准测试，拉伸速率为50mm/min；缺口冲击强度根据GB/T1043-1993标准测试，缺口深度为2mm。所有力学性能均在23℃环境中放置24小时后测得。熔融指数在250℃，2.16kg标准条件下测得。复合材料抑菌率实验采用平板计数法(J.Food Sci.2012,77,280-286)。所用醋酸乙烯酯基共聚物由朗盛化学公司提供，其余化学品为普通市售产品。
由表3中数据可知，与纯PBT(对比例10)相比，采用醋酸乙烯酯基共聚物改性的PBT(如实施例13)的断裂伸长率、缺口冲击强度分别提高21.5倍和18.7倍，同时熔融指数显著降低，这是因为醋酸乙烯酯基共聚物与PBT发生反应原位形成梳状超支化结构，显著改善了两组分的相容性，提高了PBT的韧性和熔体粘度，而且该改性效果明显优于传统增韧剂乙烯-丙烯酸正丁酯-甲基丙烯酸缩水甘油酯共聚物对PBT的改性效果(对比例11)。
由表4中数据可知，纯PBT很脆(对比例10)，加入氧化锌和醋酸乙烯酯基共聚物的复合材料的韧性也较差(对比例13)，这是因为氧化锌诱导PBT基体热降解；添加扩链剂能够弥补PBT的降解，但同时添加扩链剂、氧化锌和醋酸乙烯酯基共聚物之后的复合材料的韧性提高并不显著(对比例14)，这是因为扩链剂会优先与PBT的端羧基或端羟基反应，从而大幅度减弱醋酸乙烯酯基共聚物与PBT的反应程度；而本发明将扩链剂从双螺杆挤出机侧喂料口加入，不仅保证了醋酸乙烯酯基共聚物与PBT的末端基团反应充分，还通过后续扩链作用弥补了氧化锌对PBT的催化降解，因此所制备的复合材料的韧性优异。然而，若不加入醋酸乙烯酯基共聚物(对比例12)，所得复合材料也很脆。可见，本发明获得的PBT复合材料不仅具有优异的韧性，还具有优异的抗菌能力，可广泛应用于抗菌性纤维及织物、塑料包装材料、汽车内饰件、医用耗材领域等。
实施例22
将回收聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份在室温下预混均匀，然后将预混物由双螺杆挤出机连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即得到复合材料。
实施例23
将回收聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)85份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)15份，三[2，4-二叔丁基苯基]亚磷酸酯0.4份，硬脂酸酰胺0.2份，苯甲酸钠1份加入密炼机内进行熔融共混5分钟(共混温度为265℃)，即可得到复合材料。
实施例24
将回收聚对苯二甲酸乙二醇酯(特性粘度为0.65dL/g)80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为70％，甲基丙烯酸缩水甘油酯质量含量为2％)20份，四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.5份加入密炼机内进行熔融共混8分钟(共混温度为250℃)，即得到复合材料。
实施例25
将回收聚对苯二甲酸乙二醇酯(特性粘度为0.6dL/g)75份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为50％，甲基丙烯酸缩水甘油酯质量含量为5％)25份，β-(3，5-二叔丁基-4-羟基苯基)丙酸正十八碳醇酯0.2份，季戊四醇硬脂酸酯0.1份在室温下预混均匀，然后将预混物由双螺杆挤出机连续熔融挤出(挤出温度为255℃，螺杆转速为180rpm)即可得到复合材料。
对比例15
将回收聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)100份由双螺杆挤出机熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即得到复合材料。
对比例16
将回收聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)80份，乙烯-正丁基丙烯酸酯-甲基丙烯酸缩水甘油酯共聚物20份在室温下预混均匀，然后将预混物由双螺杆挤出机连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即得到复合材料。
对比例17
将新合成的聚对苯二甲酸乙二醇酯(特性粘度为0.95dL/g)80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份在室温下预混均匀，然后将预混物由双螺杆挤出机连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即得到复合材料。
将实施例22、25和对比例15-17得到的聚对苯二甲酸乙二醇酯复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，测试结果如表5所示；将实施例23、24得到的韧性聚对苯二甲酸乙二醇酯复合材料经充分干燥后做熔融指数测试，并通过平板硫化机热压成型，根据相关标准裁成标准样条用以拉伸和冲击性能测试，测试结果如表5所示。
表5实施例22-25和对比例15-17得到的PET复合材料性能测试
Figure PCTCN2018118179-appb-000005
实施例26
将回收PET 80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份，纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂ADR43700.75份加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)得到一种韧性PET抗菌复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
实施例27
将回收PET 85份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为70％，甲基丙烯酸缩水甘油酯质量含量为2％)15份，纳米氧化锌1份(粒径为20nm)，加入密炼机内熔融共混3分钟，然后加入0.5份扩链剂ADR4468继续共混2分钟(共混温度为250℃)，得到一种韧性PET抗菌复合材料。
将上述韧性PET抗菌复合材料做熔融指数测试，并通过平板硫化机热压成型，根据相关标准裁成标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试 复合材料的抑菌率，测试结果如表6所示。
实施例28
将回收PET 70份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)30份，纳米氧化锌2.5份(粒径为100nm)，四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份，聚乙烯蜡0.1份，滑石粉1份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂SAG-0081.5份加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为265℃，螺杆转速为200rpm)即可得到一种韧性PET抗菌复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
实施例29
将新合成PET 80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份，纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂ADR43700.75份加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即可得到一种韧性PET抗菌复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
实施例30
将新合成PET 85份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为50％，甲基丙烯酸缩水甘油酯质量含量为5％)15份，纳米氧化锌2份(粒径为60nm)，三[2，4-二叔丁基苯基]亚磷酸酯0.25份，苯甲酸钠2.5份加入密炼机内进行熔融共混2.5分钟，然后加入扩链剂六亚甲基二异氰酸酯0.5份继续共混2.5分钟(共混温度为255℃)，即可得到一种韧性PET抗菌复合材料。
将上述韧性PET抗菌复合材料做熔融指数测试，并通过平板硫化机热压成型，根据相关标准裁成标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
对比例18
将回收PET 100份由双螺杆挤出机连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即得到一种PET复合材料，将该复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
对比例19
将回收PET 100份，纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂ADR43700.75份加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)得到一种PET抗菌复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
对比例20
将回收PET 80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份，纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段经过连续熔融挤出(挤 出温度为260℃，螺杆转速为150rpm)得到一种PET抗菌复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
对比例21
将回收PET 80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份，纳米氧化锌2份(粒径为30nm)，扩链剂ADR43700.75份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，经过连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)得到一种PET抗菌复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
对比例22
将新合成PET 100份，纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，经过连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即可得到一种PET抗菌复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
对比例23
将新合成PET 80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂ADR43700.75份加入双螺杆挤出机啮合段中部，经过连续熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即可得到一种PET复合材料。
将挤出得到的韧性PET抗菌复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验测试复合材料的抑菌率，测试结果如表6所示。
表6实施例26-30和对比例18-23得到的PET复合材料性能测试
Figure PCTCN2018118179-appb-000006
Figure PCTCN2018118179-appb-000007
实施例31
将聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份，环氧化纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后通过双螺杆挤出机熔融挤出(挤出温度为260℃，螺杆转速为150rpm)得到复合材料。
所述环氧化纳米氧化锌的制备方法为：将纳米氧化锌、乙醇、水和KH560按照重量份配比95：2：1：2高速搅拌处理8分钟即可得到环氧化纳米氧化锌，其中KH560的接枝率为0.8％。
实施例32
将聚对苯二甲酸丁二醇酯(特性粘度为0.9dL/g)80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为50％，甲基丙烯酸缩水甘油酯质量含量为4％)20份，环氧化纳米氧化锌3份(粒径为20nm)在室温下预混均匀，然后通过双螺杆挤出机熔融挤出(挤出温度为240℃，螺杆转速为150rpm)得到复合材料。
所述环氧化纳米氧化锌的制备方法为：将纳米氧化锌、甲醇、水和KH560按照重量份配比80：1.5：1.5：1高速搅拌处理6分钟即可得到环氧化纳米氧化锌，其中KH560的接枝率为0.6％
实施例33
将聚对苯二甲酸乙二醇酯(特性粘度为0.85dL/g)70份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)30份，环氧化纳米氧化锌2.5份(粒径为100nm)，四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.3份，聚乙烯蜡0.1份，滑石粉1份在室温下预混均匀，通过双螺杆挤出机熔融挤出(挤出温度为265℃，螺杆转速为200rpm)即可得到复合材料。所述环氧化纳米氧化锌的制备方法为同实施例27。
实施例34
将聚碳酸酯(特性粘度为1.5dL/g)85份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为70％，甲基丙烯酸缩水甘油酯质量含量为2％)15份，环氧化纳米氧化锌1份(粒径为20nm)，加入密炼机内熔融共混4分钟(共混温度为250℃)，得到复合材料。
所述环氧化纳米氧化锌的制备方法为：将纳米氧化锌、乙醇、水和KH560按照重量份配比8:72:4:4混合，在40℃下反应16小时，提纯后得到环氧化纳米氧化锌，其中KH560的接枝率为1.3％。
实施例35
将聚对苯二甲酸乙二醇酯(特性粘度为0.65dL/g)75份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)25份，环氧化纳米氧化锌1.5份(粒径为20nm)，四[β-(3，5-二叔丁基-4-羟基苯基)丙酸]季戊四醇酯0.4份，硬脂酸酰胺0.2份，苯甲酸钠1份加入密炼机内熔融共混5分钟(共混温度为250℃)，得到复合材料。
所述环氧化纳米氧化锌的制备方法为：将纳米氧化锌、乙醇、水和KH560按照重量份配比8:80:6:6混合，在50℃下反应10小时，提纯后得到环氧化纳米氧化锌，其中KH560的接枝率为1.7％。
对比例24
将聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)100份由双螺杆挤出机熔融挤出(挤出温度为260℃，螺杆转速为150rpm)即得到复合材料。
对比例25
将聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)100份，未改性纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后通过双螺杆挤出机熔融挤出(挤出温度为260℃，螺杆转速为150rpm)得到复合材料。
对比例26
将聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)100份，环氧化纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后通过双螺杆挤出机熔融挤出(挤出温度为260℃，螺杆转速为150rpm)得到一种性能优异的接触抗菌聚酯复合材料。所述环氧化纳米氧化锌的制备方法同实施例26。
对比例27
将聚对苯二甲酸乙二醇酯(特性粘度为0.7dL/g)80份，乙烯-醋酸乙烯酯-甲基丙烯酸缩水甘油酯共聚物(醋酸乙烯酯质量含量为60％，甲基丙烯酸缩水甘油酯质量含量为3％)20份，未改性纳米氧化锌2份(粒径为30nm)在室温下预混均匀，然后通过双螺杆挤出机熔融挤出(挤出温度为260℃，螺杆转速为150rpm)得到复合材料。
将上述实施例31-33和对比例24-27挤出得到的聚酯复合材料经充分干燥后做熔融指数测试，并在注塑机上注射标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验和抑菌圈实验测试复合材料的抑菌率和纳米氧化锌的迁移行为，测试结果如表7所示。将实施例34-35得到的聚酯复合材料做熔融指数测试，并通过平板硫化机热压成型，根据相关标准裁成标准样条用以拉伸和冲击性能测试，通过大肠杆菌和金黄色葡萄球菌抑菌实验和抑菌圈实验测试复合材料的抑菌率和纳米氧化锌的迁移行为，测试结果如表7所示。
表7实施例31-35和对比例24-27所得复合材料的性能结果
Figure PCTCN2018118179-appb-000008
实施例和对比例中拉伸性能(拉伸强度和断裂伸长率)根据GB/T1040-1992标准测试，拉伸速率为50mm/min；缺口冲击强度根据GB/T1043-1993标准测试，缺口深度为2mm。所有力学性能均在23℃环境中放置24小时后测得。聚对苯二甲酸乙二醇酯、聚对苯二甲酸丁二醇酯、聚碳酸酯的熔融指数分别在(260℃，2.16kg)、(250℃，2.16kg)、(300℃，1.2kg)标准条件下测得。复合材料抑菌圈实验采用Kirby-Bauer测试方法(如Am.J.Clin.Pathol.1966,45, 493-496.)，复合材料抑菌率实验采用平板计数法(J.Food Sci.2012,77,280-286)。所用聚对苯二甲酸乙二醇酯为常州华润公司产品，所用聚对苯二甲酸丁二醇酯为康辉石化公司产品，所用聚碳酸酯为台湾奇美公司产品；所用回收聚对苯二甲酸乙二醇酯为浙江嘉丽再生资源有限责任公司产品；其余化学品为市售产品。
由表5中数据可知，与单纯的回收PET(对比例15)相比，采用醋酸乙烯酯基共聚物改性的回收PET(如实施例22)的断裂伸长率、缺口冲击强度分别提高64.7倍和21.7倍，同时熔融指数显著降低，这是因为醋酸乙烯酯基共聚物与回收PET发生反应原位形成梳状超支化结构，显著改善了两组分的相容性，提高了回收PET的韧性和熔体粘度，而且该改性效果明显优于传统增韧剂乙烯-正丁基丙烯酸酯-甲基丙烯酸缩水甘油酯共聚物(对比例16)对回收PET的改性效果。与新合成PET相比，本发明公开的醋酸乙烯酯基共聚物对回收PET的改性效果更显著，例如醋酸乙烯酯基共聚物改性回收PET(如实施例22)的拉伸强度、断裂伸长率和缺口冲击强度分别为醋酸乙烯酯基共聚物改性新合成PET(对比例17)的1.43倍、9.2倍和4.2倍，而熔融指数却为醋酸乙烯酯基共聚物改性新合成PET的18％，说明回收PET更容易与醋酸乙烯酯基共聚物发生反应形成梳状超支化共聚物。由此可见，通过本发明获得的聚对苯二甲酸乙二醇酯复合材料具有拉伸强度高、断裂伸长率高、冲击韧性好等优点，适合制备对机械性能要求高的日常用品和器件。
由表6中数据可知，PET(对比例18)很脆，加入纳米氧化锌和醋酸乙烯酯基共聚物的复合材料(对比例20)的韧性也较差，这是因为纳米氧化锌诱导PET基体热降解；添加扩链剂能够弥补PET的降解，但同时添加扩链剂、纳米氧化锌和醋酸乙烯酯基共聚物之后的复合材料(对比例21)的韧性提高并不显著，这是因为扩链剂会优先与PET的端羧基或端羟基反应，从而减弱醋酸乙烯酯基共聚物与PET的反应程度；而本发明将扩链剂从双螺杆挤出机侧喂料口加入，不仅保证了醋酸乙烯酯基共聚物与PET的末端基团反应充分，还通过后续扩链作用弥补了纳米氧化锌对回收PET的催化降解，因此所制备的复合材料的韧性优异。而与对比例22-23相比，本发明公开的复合材料中纳米氧化锌、醋酸乙烯酯基共聚物和扩链剂对提高新合成PET材料的韧性还具有协同效应。首先纳米氧化锌会催化新合成PET的热降解产生更多活性的末端基团，与新合成PET相比更容易与醋酸乙烯酯基共聚物上的环氧基团反应，原位形成梳状超支化共聚物，这种梳状超支化共聚物能够显著提高醋酸乙烯酯基共聚物与PET基体的相容性和熔体粘度，同时通过侧喂料口加入的扩链剂弥补了纳米氧化锌对PET的过度热降解。可见，本发明获得的PET复合材料不仅具有优异的韧性，还具有优异的抗菌能力，可广泛应用于抗菌性纤维及织物、塑料包装材料、汽车内饰件、医用耗材领域等。
由表7中数据可知，PET(对比例24)和只加环氧化纳米氧化锌或未改性纳米氧化锌的复合材料(对比例25-26)都很脆，但加环氧化纳米氧化锌的材料的韧性和强度明显优于加未改性纳米氧化锌的材料；加入纳米氧化锌和醋酸乙烯酯基共聚物的复合材料(对比例27)的韧性也较差，这是因为纳米氧化锌诱导PET聚酯基体降解导致材料脆化；本发明公开的复合材料由于环氧化纳米氧化锌表面的环氧基团与聚酯端羧基或端羟基发生原位反应，能很好的弥补聚酯的降解而使材料韧性优异；醋酸乙烯酯基共聚物与聚酯原位反应形成梳状超支化共聚物，能够显著提高醋酸乙烯酯基共聚物与聚酯基体的相容性和熔体粘度，赋予聚酯优异的韧性。本发明公开的复合材料无抑菌圈出现，这是因为环氧化纳米氧化锌与聚酯基体通过化学键相连接，不会从基体中迁移出来；同时纳米氧化锌经过环氧化改性后，分散更均匀，使得复合材料的抑菌率也更高。值得说明的是，氧化锌催化聚酯发生适度降解产生更多的端羟基和端羧基，能够提高聚酯与环氧基团和醋酸乙烯酯基共聚物的反应程度，反而有力于聚酯材料性能的提高，即本发明中环氧化纳米氧化锌和醋酸乙烯酯基共聚物对提高聚酯材料的性能具有协同效应。可见，通过本发明获得的聚酯复合材料不仅具有优异的性能，还具有优异的抗菌能力，而且抑菌剂不会迁移到基体外面，可广泛应用于纤维及织物、塑料包装材料、汽车内饰件、医用耗材等领域。
所属领域的普通技术人员应当理解：以上任何实施例的讨论仅为示例性的，并非旨在暗示本公开的范围(包括权利要求)被限于这些例子；在本发明的思路下，以上实施例或者不同实施例中的技术特征之间也可以进行组合，并存在如上所述的本发明的不同方面的许多其它变化，为了简明它们没有在细节中提供。因此，凡在本发明的精神和原则之内，所做的任何省略、修改、等同替换、改进等，均应包含在本发明的保护范围之内。

Claims (27)

  1. 一种聚酯材料或工程塑料组合物，其特征在于，所述材料或组合物的配方按照重量份数配比，包括：聚酯65～90份，弹性体5～35份，扩链剂0.05～3份，功能性助剂0.01～5份；
    所述材料或组合物的制备方法，包括：
    将聚酯、弹性体和功能性助剂根据重量份数配比混匀，然后熔融挤出，按照重量份配比加入扩链剂，再进行熔融挤出，即可得到材料；
    或者，将聚酯、弹性体和功能性助剂根据重量份数配比混匀，然后熔融共混，按照重量份配比加入扩链剂，再进行熔融共混，即可得到材料；
    所述弹性体为含有环氧基团或酸酐基团的弹性体；
    所述弹性体含有醋酸乙烯酯的结构单元。
  2. 根据权利要求1所述的材料或工程塑料组合物，其特征在于，所述聚酯包括聚对苯二甲酸乙二醇酯、聚对苯二甲酸丁二醇酯和聚碳酸酯中一种或多种。
  3. 根据权利要求1所述的材料或工程塑料组合物，其特征在于，当聚酯选用PBT时，所述材料还包括0.1～4份抗菌剂，所述抗菌剂包括氧化锌、氧化银、二氧化钛、氧化铈中的一种或多种。
  4. 根据权利要求3所述的材料或工程塑料组合物，其特征在于，所述材料的制备方法，包括：
    将PBT、弹性体和抗菌剂根据重量份配数比混匀，然后挤出，按照重量份配比加入扩链剂，再经过连续熔融挤出即可得到材料；
    或者，将PBT、弹性体和抗菌剂根据重量份数配比混匀，进行熔融共混，然后按照重量份配比加入扩链剂继续共混，即可得到材料。
  5. 一种PBT复合材料，其特征在于，所述复合材料的配方，按照重量份数配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，抗菌剂0-4份，扩链剂0-3份；所述抗菌剂包括氧化锌、氧化银、二氧化钛、氧化铈中的一种或多种。
  6. 根据权利要求5所述的材料，其特征在于，所述醋酸乙烯酯基共聚物至少包含甲基丙烯酸缩水甘油酯和乙烯结构单元。
  7. 根据权利要求6所述的材料，其特征在于，所述醋酸乙烯酯基共聚物还可以包括乙烯-醋酸乙烯酯二元共聚物。
  8. 根据权利要求5所述的材料，其特征在于，所述复合材料的配方，按照重量份数配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，0.1～4份抗菌剂，扩链剂0.05～3份。
  9. 根据权利要求8所述的材料，其特征在于，所述材料的制备方法，包括：
    将PBT、醋酸乙烯酯基共聚物和抗菌剂根据重量份数配比混匀，然后挤出，按照重量份配比加入扩链剂，再经过连续熔融挤出即可得到材料；
    或者，将PBT、醋酸乙烯酯基共聚物和抗菌剂根据重量份数配比混匀，进行熔融共混，然后按照重量份配比加入扩链剂继续共混，即可得到材料。
  10. 根据权利要求5所述的材料，其特征在于，所述复合材料的配方，按照重量份数配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，0.1～5份环氧化碳基粒子，扩链剂0.05～3份，0.01～5份功能性助剂。
  11. 根据权利要求10所述的材料，其特征在于，所述材料的制备方法包括：
    将PBT、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融挤出，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融挤出，最后按照重量份数配比加入扩链剂，继续熔融挤出，即可得到材料；
    或者，将PBT、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融共混，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融共混，最后按照重量份数配比加入扩链剂，继续熔融共混，即可得到材料。
  12. 根据权利要求5所述的材料，其特征在于，所述复合材料的配方，按照重量份数配比，包括：PBT 65～90份，醋酸乙烯酯基共聚物5～35份，环氧化纳米氧化锌0.1～4份。
  13. 一种PET复合材料，其特征在于，所述复合材料的配方按照重量份数配比，包括：回收PET 70-95份，醋酸乙烯酯基共聚物5-30份，所述回收PET的特性粘度为0.3～1.0dL/g，所述醋酸乙烯酯基共聚物中醋酸乙烯酯的质量含量为45～75％。
  14. 根据权利要求13所述的材料，其特征在于，所述醋酸乙烯酯基共聚物中至少还含有甲基丙烯酸缩水甘油酯和乙烯结构单元，其中甲基丙烯酸缩水甘油酯的质量百分含量为0.5～10％。
  15. 根据权利要求13所述的材料，其特征在于，所述材料还包括环氧化纳米氧化锌0.1～4份或者纳米氧化锌0.1～4份。
  16. 根据权利要求15所述的材料，其特征在于，所述材料还可以包括扩链剂0.05～3份。
  17. 根据权利要求16所述的材料，其特征在于，当材料包括纳米氧化锌时，所述材料的制备方法包括：
    将PET、醋酸乙烯酯基共聚物、纳米氧化锌根据重量份配比在室温下预混均匀，然后将预混物由主喂料口加入双螺杆挤出机输送段，通过侧喂料将扩链剂按照重量份配比加入双螺杆挤出机啮合段中部，经过连续熔融挤出即可得到PET复合材料，其中熔融挤出温度为PET熔点以上1～30℃，螺杆转速为100～350rpm；
    或者，将PET、醋酸乙烯酯基共聚物、纳米氧化锌根据重量份配比加入密炼机内进行熔融共混，然后加入扩链剂继续共混即可得到PET复合材料，其中熔融共混温度为PET熔点以上1～30℃。
  18. 根据权利要求13所述的材料，其特征在于，所述材料还包括环氧化碳基粒子0.1～5份，扩链剂0.05～3份，功能性助剂0.01～5份。
  19. 根据权利要求18所述的材料，其特征在于，所述材料的制备方法包括：
    将PET、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融挤出，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融挤出，最后按照重量份数配比加入扩链剂，继续熔融挤出，即可得到材料；
    或者，将PET、环氧化碳基粒子和功能性助剂根据重量份数配比混均，然后熔融共混，按照重量份配比加入醋酸乙烯酯基共聚物，再进行熔融共混，最后按照重量份数配比加入扩链剂，继续熔融共混，即可得到材料。
  20. 一种塑料包装或者塑料结构件，其特征在于，所述塑料包装或者塑料结构件包含权利要求1-19任一所述的复合材料。
  21. 一种汽车内饰件，其特征在于，所述汽车内饰件包含权利要求1-19任一所述的复合材料。
  22. 一种电器外壳，其特征在于，所述电器外壳包含权利要求10或11所述的复合材料。
  23. 一种电器外壳，其特征在于，所述电器外壳包含权利要求18或19所述的复合材料。
  24. 一种抗菌纤维或织物，其特征在于，所述抗菌纤维或织物包含权利要求3或4任一所述的复合材料。
  25. 一种抗菌纤维或织物，其特征在于，所述抗菌纤维或织物包含权利要求8或9所述的复合材料。
  26. 一种抗菌纤维或织物，其特征在于，所述抗菌纤维或织物包含权利要求12所述的复合材料。
  27. 一种抗菌纤维或织物，其特征在于，所述抗菌纤维或织物包含权利要求15-17所述的复合材料。
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