阅读说明：本技术 热塑性硫化橡胶 (Thermoplastic vulcanizates ) 是由 P·A·巴达尼 C·M·赫格顿 O·O·楚格 E·P·乔尔丹 H·董 于 2018-12-07 设计创作，主要内容包括：热塑性硫化橡胶组合物包含：(i)至少部分固化的橡胶分散相；(ii)包括至少一种热塑性聚合物的连续热塑性相；(iii)第一聚硅氧烷组合物,其包含物理分散在第一热塑性材料中的迁移硅氧烷聚合物,和(iv)第二聚硅氧烷组合物,其包含键合到第二热塑性材料上的非迁移的硅氧烷聚合物。(The thermoplastic vulcanizate composition comprises: (i) an at least partially cured rubber dispersed phase; (ii) a continuous thermoplastic phase comprising at least one thermoplastic polymer; (iii) (iii) a first polysiloxane composition comprising a migrating silicone polymer physically dispersed in the first thermoplastic material, and (iv) a second polysiloxane composition comprising a non-migrating silicone polymer bonded to the second thermoplastic material.)

1. A thermoplastic vulcanizate composition comprising: (i) an at least partially cured rubber dispersed phase; (ii) a continuous thermoplastic phase comprising at least one thermoplastic polymer; (iii) (iii) a first polysiloxane composition comprising a migrating silicone polymer physically dispersed in the first thermoplastic material, and (iv) a second polysiloxane composition comprising a non-migrating silicone polymer bonded to the second thermoplastic material.

2. The composition of claim 1, wherein the rubber phase (i) comprises an ethylene propylene diene terpolymer.

3. The composition of claim 2, wherein the ethylene propylene diene terpolymer comprises from 40 to 85 weight percent ethylene based on the total weight of ethylene and propylene.

4. The composition of any of claims 1-3, comprising 10 to 80 weight percent of rubber phase (i), based on the total weight of the thermoplastic vulcanizate composition.

5. The composition of any of claims 1-4, wherein the thermoplastic phase (ii) comprises a propylene ethylene copolymer.

6. The composition of any of claims 1-5, wherein the thermoplastic phase (ii) comprises a polypropylene homopolymer.

7. The composition of any of claims 1-6, wherein the composition comprises 5 to 75 weight percent of the thermoplastic phase (ii), based on the total weight of the thermoplastic vulcanizate composition.

8. The composition of any of claims 1-7, wherein the first thermoplastic material in (iii) or the second thermoplastic material in (iv) is the same or different.

9. The composition of any of claims 1-8, wherein the first thermoplastic material in (iii) or the second thermoplastic material in (iv) is selected from polyethylene, polypropylene, or a homopolymer or copolymer thereof.

10. The composition of any of claims 1-9, wherein the composition comprises 0.1 to 20 weight percent of the first polysiloxane composition (iii) based on the total weight of the thermoplastic vulcanizate composition.

11. The composition of any of claims 1-10, wherein the second polysiloxane (iv) is polypropylene bonded.

12. The composition of any of claims 1-11, wherein the composition comprises 0.2 to 20 weight percent of the second polysiloxane composition (iv) based on the total weight of the thermoplastic vulcanizate composition.

13. The composition of any of claims 1-12, wherein the weight ratio of the second polysiloxane composition to the first polysiloxane composition is no greater than 1.

14. The composition of any one of claims 1-13 having a shore a hardness of 50 and greater as measured by ASTM D2240.

15. A method of producing a thermoplastic vulcanizate composition, the method comprising:

(a) feeding at least the following components to the mixer: (i) a cross-linkable rubber, (ii) a thermoplastic polymer, (iii) a first polysiloxane composition comprising a migrating silicone polymer physically dispersed in the first thermoplastic material, and (iv) a second polysiloxane composition comprising a non-migrating silicone polymer bonded to the second thermoplastic material; and

(b) mixing the components (i) - (iv) under conditions such that the thermoplastic polymer melts and the rubber at least partially crosslinks to produce a multiphase product comprising at least partially crosslinked rubber particles dispersed in a matrix comprising thermoplastic polymer.

16. The method of claim 15, wherein the first thermoplastic material in (iii) or the second thermoplastic material in (iv) comprises polyethylene or polypropylene.

17. A method according to claim 15 or claim 16, wherein the viscosity of the silicone polymer of the first polysiloxane composition (iii) is from 30000 to 70000mpa.s (measured at 25 ℃).

18. The method of any one of claims 15-17, wherein the second polysiloxane (iv) is bonded to polypropylene.

19. The method of any one of claims 15-18, wherein the cured composition is fed to the mixer in (a).

20. A vehicle part comprising the thermoplastic vulcanizate composition of any one of claims 1 to 14.

21. The vehicle part of claim 20 wherein said part is selected from the group consisting of exterior weatherseals such as molded corners, molded end caps, glass runs, trunk seals, tailgate seals, hood seals, gap fillers, glass encapsulation, cut line seals, door seals, seals between vehicle hood and radiator, windshield seals, sunroof seals, roof line seals, rear window seals, rocker panels, window frames, and beltline seals.

Detailed description of the embodiments

Described herein are thermoplastic vulcanizate (TPV) compositions comprising an at least partially cured rubber phase dispersed within a continuous thermoplastic phase, and at least first and second different polysiloxane compositions, as well as other optional ingredients such as fillers and extenders. The first polysiloxane composition comprises a migrating silicone polymer physically dispersed in a first thermoplastic material, while the second polysiloxane composition comprises a non-migrating silicone polymer bonded to a thermoplastic material. The TPVs disclosed herein have a desirable combination of low COF, good bonding properties, and excellent surface aesthetics even at temperatures up to 120 ℃, which makes them useful in the production of automotive body parts such as glass run corner molds, belt line seal end caps, cut line seals, gap fillers, fuel door seals, body seal low friction skins, weatherseals, gaskets, glass encapsulation, end caps, and others.

With respect to the difference in migration properties between the first and second silicone compositions, it is known that silicone molecules are physically driven to migrate to the surface of the polymer component due to the inherent incompatibility with the non-polar polyolefin material. This physical molecular migration to the surface is slowed by the molecular weight of the polysiloxane being increased, either by changing the chemical make-up of the molecule, or in the case of a second polysiloxane composition, by chemically reacting it with the selected molecule, e.g., a thermoplastic polyolefin. The polysiloxane molecules are then chemically linked to the thermoplastic molecules, which prevents the physical migration of the polysiloxane molecules to the surface of the material and are therefore referred to as non-migratory slip agents. When such molecules are present in the system with the first polysiloxane composition, it has now been found that this combination is very effective in reducing the COF properties of the TPV formulation without affecting its bonding properties and surface quality.

Rubber phase

Rubbers that may be used to form the rubber phase of the compositions of the present invention include those rubbers that are capable of being cured or crosslinked. Reference to a rubber may include mixtures of more than one rubber. Non-limiting examples of rubbers include olefin elastomeric copolymers, butyl rubber, and mixtures thereof. In one or more embodiments, the olefin elastomeric copolymer comprises an ethylene-propylene-non-conjugated diene rubber or a propylene-based rubbery copolymer containing units derived from non-conjugated diene monomers.

The term ethylene-propylene diene rubber (or simply ethylene-propylene rubber) refers to a rubbery copolymer polymerized from ethylene, propylene and at least one diene monomer. The diene monomer may include, but is not limited to, 5-ethylidene-2-norbornene; 5-vinyl-2-norbornene; divinylbenzene; 1, 4-hexadiene; 5-methylene-2-norbornene; 1, 6-octadiene; 5-methyl-1, 4-hexadiene; 3, 7-dimethyl-1, 6-octadiene; 1, 3-cyclopentadiene; 1, 4-cyclohexadiene; dicyclopentadiene; or a combination thereof.

The ethylene-propylene rubber may comprise from about 40 to about 85 weight percent, alternatively from about 50 to about 70 weight percent, alternatively from about 60 to about 66 weight percent, of units derived from ethylene, based on the total weight of ethylene and propylene in the rubber. In addition, the rubber may comprise from about 0.1 to about 15 weight percent, alternatively from about 0.5 to about 12 weight percent, alternatively from about 1 to about 10 weight percent, alternatively from about 2 to about 8 weight percent of units derived from diene monomers. The rubber may comprise, expressed in mole percent, about 0.1 to about 5 mole percent, alternatively about 0.5 to about 4 mole percent, alternatively about 1 to about 2.5 mole percent of units derived from diene monomer. In one or more embodiments, where the diene includes 5-ethylidene-2-norbornene, the ethylene-propylene rubber may include at least 1%, alternatively at least 3%, alternatively at least 4%, alternatively at least 5%, alternatively from about 1 to about 15%, alternatively from about 5% to about 12%, alternatively from about 7% to about 11%, by weight of units derived from 5-ethylidene-2-norbornene. In one or more embodiments, where the diene includes 5-vinyl-2-norbornene, the ethylene-propylene rubber may include at least 1 wt%, alternatively at least 3 wt%, alternatively at least 4 wt%, alternatively at least 5 wt%, alternatively from about 1 to about 15 wt%, alternatively from about 5 to about 12 wt%, alternatively from about 7 to about 11 wt% of units derived from 5-vinyl-2-norbornene.

The weight average molecular weight (M) of the ethylene-propylene rubber_w) Can be used forGreater than 100000g/mol, or greater than 200000g/mol, or greater than 400000g/mol, or greater than 600000 g/mol. Preferably, M of the ethylene-propylene rubber_wLess than 1200000g/mol, or less than 1000000g/mol, or less than 900000g/mol, or less than 800000 g/mol.

Number average molecular weight (M) of useful ethylene-propylene rubbers_n) It may be greater than 20000g/mol, or greater than 60000g/mol, or greater than 100000g/mol, or greater than 150000 g/mol. M of the ethylene-propylene rubber_nMay be less than 500000g/mol, or less than 400000g/mol, or less than 300000g/mol, or less than 250000 g/mol.

Determination of molecular weight (M)_n、M_wAnd M_z) And Molecular Weight Distribution (MWD) techniques can be found in U.S. patent No.4540753, which is incorporated herein by reference, and Macromolecules, 1988, volume 21, page 3360, to vermate et al, which is also incorporated herein by reference.

The ethylene-propylene rubber used herein may also pass the Mooney viscosity (ML) according to ASTM D-1646₍₁₊₄₎125 deg.C) is from about 10 to about 500, or from about 50 to about 450.

In some embodiments, the ethylene-propylene rubber may be characterized by an intrinsic viscosity of about 1 to about 8dl/g, or about 3 to about 7dl/g, or about 4 to about 6.5dl/g, as measured in decalin at 135 ℃ according to ASTM D-1601.

In some embodiments, the ethylene-propylene rubber used herein may have a glass transition temperature (T) as measured by Differential Scanning Calorimetry (DSC) according to ASTM E-1356 at a heating rate of 5 ℃/minute_g). The T is_gLess than-20 ℃, in other embodiments less than-30 ℃, in other embodiments less than-50 ℃ and in other embodiments from about-20 to about-60 ℃.

Suitable ethylene-propylene rubbers may be manufactured or synthesized using a variety of techniques. For example, these copolymers can be synthesized by using solution, slurry or gas phase polymerization techniques, which employ different catalyst systems. Exemplary catalysts include Ziegler catalystsle-Natta systems such as those including vanadium catalysts, and single site catalysts, including constrained geometry catalysts, including group IV-VI metallocenes. The elastomeric copolymer is available under the trade name Vistalon^TM(ExxonMobil Chemical Co., Houston, Tex.), Keltan^TM(Lanxess)，Nordel^TMIP(Dow)，NORDEL MG^TM(Dow)，Royalene^TM(Lion Copolymer) and Buna^TM(Lanxess) is commercially available.

Typically, the rubber phase comprises from 10 to 80 weight percent, such as from 15 to 70 weight percent, for example from 20 to 60 weight percent, based on the total weight of the thermoplastic vulcanizate composition.

The rubber is at least partially cured by using dynamic vulcanization techniques. Dynamic vulcanization refers to a vulcanization or curing process for rubber contained in a blend comprising rubber and at least one thermoplastic resin. The rubber is vulcanized under shear and extension conditions at a temperature at or above the melting point of the thermoplastic resin. The rubber is preferably simultaneously crosslinked and dispersed (preferably as fine particles) in the thermoplastic resin matrix, although other morphologies such as co-continuous morphology may be present depending on the degree of cure, rubber to plastic viscosity ratio, mixing strength, residence time and temperature.

After dynamic vulcanization, the rubber is in the form of finely dispersed and well dispersed vulcanized or cured rubber particles in a continuous thermoplastic phase or matrix, although a co-continuous morphology is also possible. In those embodiments in which the cured rubber is in the form of finely dispersed and well-dispersed particles in a thermoplastic medium, the rubber particles typically have an average diameter of less than 50 μm, alternatively less than 30 μm, alternatively less than 10 μm, alternatively less than 5 μm, alternatively less than 1 μm. In preferred embodiments, at least 50%, alternatively at least 60%, alternatively at least 75% of the rubber particles have an average diameter of less than 5 μm, alternatively less than 2 μm, alternatively less than 1 μm.

The rubber in the composition is preferably at least partially cured. In one or more embodiments, the rubber is advantageously fully or completely cured. The degree of curing can be determined byThe amount of rubber that can be extracted from a thermoplastic vulcanizate using cyclohexane or boiling xylene as the extractant is measured. Preferably, the rubber has a degree of cure in which no more than 15 wt.%, or no more than 10 wt.%, or no more than 5 wt.%, or no more than 3 wt.% can be extracted by cyclohexane at 23 ℃, as disclosed in U.S. patent No. 4311628; 5100947; and 5157081, which are incorporated herein by reference in their entirety. Alternatively, the rubber has a degree of cure such that the crosslink density is at least 4x10^-5Or at least 7x10^-5Or at least 10x10^-5Mol/ml rubber. See, Crosslink definitions and PhaseMorphologies in dynamic Vulcanized TPEs by Ellul et al, Rubber Chemistry and Technology, Vol.68, pp.573-584 (1995).

The rubber may be dynamically vulcanized using various curing systems known in the art. For example, phenolic resins, hydrosilation (also known as silicon-containing cure systems), and free radical cure systems can be used.

Useful phenolic cure systems are disclosed in U.S. Pat. Nos. 2972600, 3287440, 5952425 and 6437030, which are incorporated herein by reference. In one or more embodiments, the phenolic resin curing agent comprises a resole phenolic resin, which can be prepared by condensing an alkyl substituted phenol or an unsubstituted phenol with an aldehyde, preferably formaldehyde, in a basic medium or by condensing a difunctional phenolic diol. The alkyl substituent of the alkyl-substituted phenol may contain from 1 to about 10 carbon atoms.

Useful phenolic resins are available under the trade name SP-1044, SP-1045(Schenectady International; Schenectady, N.Y.), which may be referred to as alkylphenol-formaldehyde resins.

Examples of the phenolic resin curing agent include those defined according to the following general formula:

wherein Q is selected from-CH₂-，-CH₂-O-CH₂-a divalent group of (a); m is 0 or a positive integer from 1 to 20,and R' is an organic group. In one embodiment, Q is a divalent group-CH₂-O-CH₂-m is 0 or a positive integer from 1 to 10, and R' is an organic group having less than 20 carbon atoms. In other embodiments, m is 0 or a positive integer from 1 to 10, and R' is an organic group having from 4 to 12 carbon atoms.

The phenolic resin may be used in an amount of about 2 to about 6 parts by weight, or about 3 to about 5 parts by weight, or about 4 to about 5 parts by weight, based on 100 parts by weight of the rubber.

The supplemental amount of stannous chloride may comprise from about 0.5 to about 2.0 parts by weight, alternatively from about 1.0 to about 1.5 parts by weight, alternatively from about 1.2 to about 1.3 parts by weight, based on 100 parts by weight of the rubber. In combination therewith, about 0.1 to about 6.0 parts by weight, or about 1.0 to about 5.0 parts by weight, or about 2.0 to about 4.0 parts by weight of zinc oxide can be used. In one or more embodiments, the olefin rubber used with the phenolic curative includes diene units derived from 5-ethylidene-2-norbornene.

The silicon-containing curing system may include a silicon hydride compound having at least two SiH groups. Useful silicon hydride compounds include, but are not limited to, methylhydrogenpolysiloxanes, methylhydrodimethylsiloxane copolymers, alkylmethyl-co-methylhydrogenpolysiloxanes, bis (dimethylsilyl) alkanes, bis (dimethylsilyl) benzenes, and mixtures thereof.

Catalysts useful for hydrosilylation include, but are not limited to, group VIII transition metals. These metals include, but are not limited to, palladium, rhodium and platinum and complexes of these metals. Useful silicon-containing curing agents and curing systems are disclosed in U.S. patent No. 5936028.

The silane-containing compound may be used in an amount of about 0.5 to about 5.0 parts by weight, or about 1.0 to about 4.0 parts by weight, or about 2.0 to about 3.0 parts by weight, based on 100 parts by weight of the rubber. The supplemental amount of catalyst may comprise from about 0.5 to about 20.0 parts, alternatively from about 1.0 to about 5.0 parts, alternatively from about 1.0 to about 2.0 parts metal per million parts by weight of rubber. In one or more embodiments, the olefin rubber used with the hydrosilylation curing agent includes diene units derived from 5-vinyl-2-norbornene.

The curing system used in practicing the method of the present invention may include a free radical curing agent and an adjuvant. Free radical curing agents include peroxides such as organic peroxides. Examples of organic peroxides include, but are not limited to, di-t-butyl peroxide, dicumyl peroxide, t-butylcumyl peroxide, α, α -bis (t-butylperoxy) diisopropylbenzene, 2, 5-dimethyl-2, 5-di (t-butylperoxy) hexane (DBPH), 1, 1-bis (t-butylperoxy) -3, 3, 5-trimethylcyclohexane, n-butyl-4-4-bis (t-butylperoxy) valerate, benzoyl peroxide, lauroyl peroxide, dilauroyl peroxide, 2, 5-dimethyl-2, 5-di (t-butylperoxy) hexyne-3, and mixtures thereof. In addition, diaryl peroxides, ketone peroxides, peroxydicarbonates, peroxyesters, dialkyl peroxides, hydroperoxides, peroxyketals, and mixtures thereof may be used.

Useful peroxides and their method of use in dynamic vulcanization of thermoplastic vulcanizates are disclosed in U.S. patent No.5656693, which is incorporated herein by reference.

The coagent may include a multifunctional acrylate, a multifunctional methacrylate, or a combination thereof. In other words, the adjuvant comprises two or more organic acrylate or methacrylate substituents. Examples of multifunctional acrylates include diethylene glycol diacrylate, trimethylolpropane triacrylate (TMPTA), ethoxylated trimethylolpropane triacrylate, propoxylated glycerol triacrylate, pentaerythritol triacrylate, bis (trimethylolpropane) tetraacrylate, pentaerythritol tetraacrylate, ethoxylated pentaerythritol triacrylate, cyclohexanedimethanol diacrylate, di (trimethylolpropane) tetraacrylate, or combinations thereof. Examples of multifunctional methacrylates include trimethylolpropane trimethacrylate (TMPTMA), ethylene glycol dimethacrylate, butanediol dimethacrylate, diethylene glycol dimethacrylate, polyethylene glycol dimethacrylate, allyl methacrylate, or combinations thereof.

Thermoplastic phase

The thermoplastic resin phase includes those thermoplastic polymers which include solid, generally high molecular weight plastic resins. Exemplary thermoplastic polymers include crystalline, semi-crystalline, and crystallizable polyolefins, olefin homopolymers and copolymers, and non-olefin resins.

thermoplastic polymers may be formed by polymerizing ethylene or an alpha-olefin such as propylene, 1-butene, 1-hexene, 1-octene, 2-methyl-1-propene, 3-methyl-1-pentene, 4-methyl-1-pentene, 5-methyl-1-hexene and mixtures thereof, copolymers of ethylene and propylene and copolymers of ethylene and/or propylene with another alpha-olefin such as 1-butene, 1-hexene, 1-octene, 2-methyl-1-propene, 3-methyl-1-pentene, 4-methyl-1-pentene, 5-methyl-1-hexene or mixtures thereof are also contemplated, propylene with ethylene or α -olefins in particular, or with C₁₀-C₂₀Reactor, impact and random copolymers of dienes. The comonomer content for these propylene copolymers can range from 1% to about 30% by weight of the polymer, as described in U.S. patent No.6867260, which is incorporated herein by reference. Specifically, the trade name VISTA MAX^TM(ExxonMobil) obtained.

Other suitable polyolefin copolymers may include copolymers of olefins with styrene such as styrene-ethylene copolymers, or polymers of olefins with α, β -unsaturated acids, α, β -unsaturated esters such as polyethylene-acrylate copolymers. The non-olefinic thermoplastic polymer may include polymers and copolymers of styrene, alpha, beta-unsaturated acids, alpha, beta-unsaturated esters, and mixtures thereof. For example, polystyrene, polyacrylates and polymethacrylates may be used. Blends or mixtures of two or more polyolefin thermoplastics such as described herein, or with other polymer modifiers, are also suitable according to the present invention. Useful thermoplastic polymers may also include impact and reactor copolymers.

The thermoplastic polymer may include propylene-based polymers, including those solid, generally high molecular weight plastic resins that contain primarily units derived from the polymerization of propylene. In certain embodiments, at least 75%, alternatively at least 90%, alternatively at least 95%, alternatively at least 97%, of the units of the propylene-based polymer are derived from the polymerization of propylene. In particular embodiments, these polymers include propylene homopolymers.

In certain embodiments, the propylene-based polymer may also include units derived from the copolymerization of ethylene and/or alpha-olefins such as 1-butene, 1-hexene, 1-octene, 2-methyl-1-propene, 3-methyl-1-pentene, 4-methyl-1-pentene, 5-methyl-1-hexene and mixtures thereof.

The propylene-based polymer may include a semi-crystalline polymer. These polymers may be characterized by a crystallinity of at least 25 wt.%, or at least 55 wt.%, or at least 65%, or at least 70 wt.%. Crystallinity can be determined by dividing the heat of fusion of the sample by the heat of fusion of the 100% crystalline polymer (which is assumed to be 290 joules/gram for polypropylene).

In one or more embodiments, the propylene-based polymer may be polymerized by H_fIs at least 52.3J/g, or exceeds 100J/g, or exceeds 125J/g, or exceeds 140J/g.

In one or more embodiments, useful propylene-based polymers may be polymerized by M_wIs from about 50 to about 2000kg/mol, or from about 100 to about 600 kg/mol. They may also pass through M_nIs from about 25 to about 1000kg/mol, or from about 50 to about 300kg/mol, as measured by GPC with polystyrene standards.

In one or more embodiments, useful propylene-based polymers can have an MFR (ASTM D-1238, 2.16kg at 230 ℃) of less than 100dg/min, or less than 50dg/min, or less than 10dg/min, or less than 5 dg/min. In these or other embodiments, the MFR of the propylene-based polymer may be at least 0.1dg/min, or 0.2dg/min, or at least 0.5 dg/min.

In aOr in various embodiments, useful propylene-based polymers_m) And may be from about 110 c to about 170 c, or from about 140 c to about 168 c, or from about 160 c to about 165 c. Their glass transition temperature (T)_g) And may be from about-10 c to about 10 c, or from about-3 c to about 5 c, or from about 0 c to about 2 c. In one or more embodiments, their crystallization temperature (T)_c) And may be at least about 75 deg.c, or at least about 95 deg.c, or at least about 100 deg.c, or at least 105 deg.c, or from 105 deg.c to 130 deg.c.

The propylene-based polymer may be synthesized using suitable polymerization techniques known in the art, such as, but not limited to, conventional ziegler-natta type polymerization, and catalyzed using single-site organometallic catalysts, including, but not limited to, metallocene catalysts.

In particular embodiments, the propylene-based polymer comprises a homopolymer of high crystallinity isotactic or syndiotactic polypropylene. Such polypropylene may have a density of about 0.89 to about 0.91g/cc and highly isotactic polypropylene may have a density of about 0.90 to about 0.91 g/cc. In addition, high and ultra-high molecular weight polypropylenes with fractional flow rates may be used. In one or more embodiments, the polypropylene resin can be characterized by an MFR (ASTM D-1238; 2.16kg at 230 ℃) that is less than or equal to 10dg/min, or less than or equal to 1.0dg/min, or less than or equal to 0.5 dg/min.

In one or more embodiments, the thermoplastic phase includes a polyethylene resin in addition to a polypropylene resin. In one or more embodiments, such polyethylene resins comprise at least 90%, alternatively at least 95%, alternatively at least 99%, of polymer units derived from ethylene. In one or more embodiments, the polyethylene resin is a polyethylene homopolymer.

In one or more embodiments, the polyethylene used in conjunction with the polypropylene can be characterized by a weight average molecular weight of from about 100 to 250kg/mol, alternatively from about 110 to 220kg/mol, alternatively from about 150 to 200 kg/mol. Such polyethylenes can be characterized by a polydispersity of less than 12, or less than 11, or less than 10, or less than 9.

In one or more embodiments, the polyethylene used in conjunction with the polypropylene can be characterized by a melt index of 1.2 to 12dg/min, alternatively 0.4 to 10dg/min, alternatively 0.5 to 8.0dg/min, as measured in accordance with ASTM D-1238 at 190 ℃ and 2.16kg load.

In one or more embodiments, the polyethylene used in conjunction with the polypropylene can be characterized by an intrinsic viscosity of 0.5 to 10dl/g, or 1.0 to 9.0dl/g, or 1.5 to 8.0dl/g, as determined in accordance with ASTM D1601 and D4020.

In one or more embodiments, the polyethylene used in combination with the polypropylene resin may be characterized by a density greater than 0.93g/cc, or greater than 0.94g/cc, or greater than 0.95g/cc, as measured according to ASTM D4883.

Polymers that can be used as polyethylene in combination with polypropylene can be generally referred to as high density polyethylene resins. For example, useful high density polyethylene resins include those available under the trade name HDPE HD 7960.13 (ExxonMobil).

Typically, the thermoplastic phase comprises from 5 to 75 weight percent, such as from 7 to 60 weight percent, for example from 10 to 55 weight percent, based on the total weight of the thermoplastic vulcanizate composition.

Polysiloxanes

Polysiloxanes are silicon polymers in which silicon atoms are bonded to one another via oxygen atoms and the valencies of the silicon not occupied by oxygen are saturated via organic radicals. The polyorganosiloxane compound has the formula R_nSiO_(4-n)/2Wherein n is 1 to 3. The free valency on the oxygen atom determines the functionality of each siloxane unit, such that the organosiloxane may be monofunctional (generally represented by the letter M), difunctional (generally represented by the letter D) or trifunctional (generally represented by the letter T). More information on polysiloxane Chemistry can be found in Walter Noll, Chemistry and Technology of Silicones, date 1962, Chapter I, pages 1-23), the entire contents of which are incorporated herein by reference. The terms "polysiloxane" and "polyorganosiloxane" are used interchangeably herein.

Many polysiloxanes include those silicone polymers and oligomers, including those of the formula-R₂A monomeric unit of SiO-, wherein each R is independently an organic group such as a hydrocarbyl group, i.e., contains a D functionality unit. Exemplary types of hydrocarbyl groups in these compounds include alkyl, alkenyl, aryl. These polysiloxane compounds may also be referred to as silicones. Exemplary types of polysiloxanes include poly (hydro) (alkyl) siloxanes, polydialkylsiloxanes, polydiarylsiloxanes and poly (hydro) (aryl) siloxanes, poly (alkyl) (aryl) -siloxanes. Specific examples of the polysiloxane include polydimethylsiloxane, polydiethylsiloxane, polymethylethylsiloxane, polydipropylsiloxane, polydibutylsiloxane, polydiphenylsiloxane, poly (hydro) (methyl) siloxane, poly (hydro) (phenyl) siloxane and poly (methyl) (phenyl) siloxane.

A first polysiloxane composition

The first polysiloxane composition comprises a migrating siloxane polymer physically dispersed in a thermoplastic material which may be any homopolymer or copolymer of ethylene and/or an alpha-olefin such as propylene, 1-butene, 1-hexene, 1-octene, 2-methyl-1-propene, 3-methyl-1-pentene, 4-methyl-1-pentene, 5-methyl-1-hexene and mixtures thereof. In a preferred embodiment, the thermoplastic material is a polypropylene homopolymer. The first polysiloxane composition may comprise 20-50 wt%, for example about 25 wt% of the siloxane polymer.

In one or more embodiments, the first polysiloxane comprises from about 10 to 15000 or even more repeating units of the formula:

R_nSiO_(4-n)/2

wherein each R group is the same or different and is independently selected from monovalent hydrocarbon radicals having from 1 to about 18 carbon atoms and n is from 0 to 4. In certain embodiments, R is an alkyl or aryl group having from 1 to about 8 carbon atoms, such as methyl, ethyl, propyl, isobutyl, hexyl, phenyl or octyl; alkenyl groups such as vinyl; or haloalkyl such as 3, 3, 3-trifluoropropyl. In particular embodiments, at least 50% of all R groups are methyl groups, and in certain of these embodiments, substantially all R groups are methyl groups.

In certain embodiments, the first polysiloxane further comprises R groups selected based on the desired curing mechanism of the composition comprising the first polysiloxane. Typically, the curing mechanism relies on condensation curing or addition curing, but is usually via an addition curing process. For the condensation reaction, the two or more R groups per molecule should be hydroxyl or hydrolysable groups such as alkoxy groups having up to 3 carbon atoms. For addition reactions, two or more R groups per molecule may be unsaturated organic groups, typically alkenyl or alkynyl groups, preferably having up to 8 carbon atoms. When it is intended to cure the composition containing the first polysiloxane by an addition reaction, then preferably R is an alkenyl group such as vinyl, allyl, 1-propenyl, isopropenyl or hexenyl.

In one or more embodiments, the first polysiloxane comprises one or more polymers defined by the formula:

R₂R¹SiO[(R₂SiO)_x(RR¹SiO)_y]SiR₂R¹

wherein each R is the same or different and is as previously described, preferably each R group is methyl or ethyl; r¹Is an alkenyl group, such as vinyl or hexenyl; x is an integer and y is 0 or an integer. In one embodiment, the second polysiloxane comprises two or more alkenyl groups.

In some embodiments, the viscosity of the first polyorganosiloxane is 30000-70000mpa.s (measured at 25 ℃).

In some embodiments, the first polyorganosiloxane can be hydroxyl terminated.

One suitable commercially available material that can be used as the first silicone composition is MB 25-501, which is available from Dow Corning.

Typically, the thermoplastic vulcanizate compositions described herein comprise from 0.2 to 20 weight percent, such as from 0.5 to 15 weight percent, such as from 0.5 to 10 weight percent, of the first polysiloxane composition.

Second polysiloxane composition

The second silicone composition comprises a non-migrating polysiloxane bonded to a thermoplastic material.

The second polysiloxane is reactively dispersed in a thermoplastic material which may be any homopolymer or copolymer of ethylene and/or an alpha-olefin such as propylene, 1-butene, 1-hexene, 1-octene, 2-methyl-1-propene, 3-methyl-1-pentene, 4-methyl-1-pentene, 5-methyl-1-hexene and mixtures thereof. In a preferred embodiment, the thermoplastic material is a polypropylene homopolymer.

Suitable methods for reactively bonding polysiloxanes to organic thermoplastic polymers such as polyolefins are disclosed in international patent publication nos. wo2015/132190 and WO2015/150218, the entire contents of which are incorporated herein by reference.

In some embodiments, the second polyorganosiloxane may contain predominantly D and/or T units and contain some alkenyl functionality, which aids in reaction with the polymer matrix. There is a covalent bond between the polyorganosiloxane and the polypropylene.

In some embodiments, the number average molecular weight of the second polyorganosiloxane is 200000 to 2000000 g/mol. The number average molecular weight of the reaction product of the polyorganosiloxane and the polymer matrix is generally at least 1.1 times, preferably at least 1.3 times, the number average molecular weight of the base polyorganosiloxane.

In some embodiments, the second polyorganosiloxane composition has a gum loading (gum staining) of 20 to 50 wt%.

One suitable commercially available material that may be used as the second polyorganosiloxane composition is HMB-0221, which is available from Dow Corning in masterbatch form.

Typically, the thermoplastic vulcanizate compositions described herein comprise from 0.2 to 20 wt.%, such as from 0.2 to 15 wt.%, such as from 0.2 to 10 wt.% of the second polysiloxane.

In some embodiments, the weight ratio of the second polysiloxane to the first polysiloxane is no greater than 1, for example, from 0.5 to 1.

Additional additives

The thermoplastic vulcanizate compositions described herein may include any or all of the optional additives typically included in thermoplastic elastomer compositions.

Additives that may optionally be included include those reinforcing and non-reinforcing fillers or extenders conventionally used in the compounding of polymeric materials. Useful fillers include carbon black, calcium carbonate, clay, silica, talc and titanium dioxide.

Plasticizers, extender oils, synthetic process oils, or combinations thereof may also optionally be added to the blend. The extender oil may include, but is not limited to, aromatic, naphthenic, and paraffinic extender oils. Exemplary synthetic processing oils are poly linear alpha olefins, poly branched alpha olefins, and hydrogenated poly alpha olefins. The compositions of the present invention may include organic esters, alkyl ethers, or combinations thereof. U.S. patent nos. 5290886 and 5397832 are incorporated in this regard. The addition of certain low to medium molecular weight organic esters and alkyl ether esters to the compositions of the present invention significantly reduces the Tg of the polyolefin and rubber components, as well as the overall composition, and improves low temperature properties, particularly flexibility and strength. These organic esters and alkyl ether esters typically have a molecular weight of less than about 10000. It is believed that the improved effect is achieved by partitioning the ester into both the polyolefin and rubber components of the composition. Particularly suitable esters include monomeric and oligomeric materials having an average molecular weight of less than about 2000, and preferably less than about 600. The ester should be compatible or miscible with both the polyolefin and rubber components of the composition; i.e. it is mixed with other components to form a single phase. It has been found that the most suitable esters are aliphatic mono-or diesters or alternatively oligomeric aliphatic esters or alkyl ether esters. Polymeric aliphatic and aromatic esters have been found to be significantly less effective, and phosphate esters are largely ineffective. Synthetic polyalphaolefins may also be used to lower the Tg.

Oligomer extenders may also optionally be used. Preferred oligomeric extenders include copolymers of isobutylene and butene or butadiene with supplemental comonomersThe copolymer of (1). These oligomeric extenders typically have a number average molecular weight of less than 1000. Useful oligomeric extenders are commercially available. For example, an oligomeric copolymer of isobutylene and butene may be sold under the trade name Polybutene^TM(Soltex; Houston, Tex.) Indopol^TM(BP; UK) and Parapol^TM(ExxonMobil) is commercially available. Oligomer copolymers comprising butadiene are available under the trade name Ricon Resin^TM(Ricon resins, Inc.; Octagon, Colorado) is commercially available.

Polymer processing additives may also optionally be added. These processing additives may include polymeric resins having very high melt flow indices. These polymeric resins include both linear and branched molecules having melt flow rates greater than about 500dg/min, or greater than about 750dg/min, or greater than about 1000dg/min, or greater than about 1200dg/min, or greater than about 1500 dg/min. Mixtures of various branched or various linear polymer processing additives, as well as mixtures of both linear and branched polymer processing additives, may be used. The preferred linear polymer processing additive is a polypropylene homopolymer. Preferred branched polymer processing additives include diene-modified polypropylene polymers. Thermoplastic vulcanizates including similar processing additives are disclosed in U.S. patent No.6451915, which is incorporated herein by reference.

The amounts of the cross-linkable rubber, the thermoplastic polymer, the first and second polysiloxanes, and optional additives are generally controlled to produce a thermoplastic vulcanizate composition having a shore a hardness of 50 and greater as measured by ASTM D2240.

Production of thermoplastic vulcanizates

The thermoplastic vulcanizate compositions described herein are produced as follows: the crosslinkable rubber, the thermoplastic polymer, the first and second polysiloxanes, and any optional additives are fed to a mixer, such as a screw extruder, and the components are then mixed under conditions such that the thermoplastic polymer melts and the rubber at least partially crosslinks to produce a multiphase product comprising at least partially crosslinked rubber particles dispersed in a matrix comprising the thermoplastic polymer. Suitable conditions include temperatures of 170 ℃ to 250 ℃, for example 190 ℃ to 230 ℃.

In a preferred embodiment, the first and second polysiloxanes are fed to a mixer along with the cross-linkable rubber and thermoplastic polymer.

Use of thermoplastic vulcanizate compositions

The thermoplastic vulcanizate compositions described herein are useful in a variety of applications, particularly for producing articles such as vehicle parts, particularly interior and exterior parts, for automobiles, aircraft, rail cars (train cars), All Terrain Vehicles (ATVs), snowmobiles, boats, motorboats, motorcycles, and any other 2, 4 or more wheeled vehicles. Specific vehicle parts include, but are not limited to, for example, exterior weatherseals, glass runs, molded corners, fuel door seals, body seal low friction skins, trunk seals, tailgate seals, cowl seals, gap fillers, glass encapsulation, cut line seals, door seals, seals between the cowl and the radiator, windshield seals, sunroof seals, roof line seals, rear window seals, rocker panels, window frames, and belt-line (belt-line) seals, end caps, and others. One particular waistline seal is shown and described in U.S. patent No. 6368700. Other specific automotive exterior weatherseals may be found in http \ \ www.santoprene.com.

The present invention will now be described in more detail with reference to the following non-limiting examples.

Comparative and examples 1 to 13

13 different PP/EPDM TPV formulations according to the invention (examples 1-13) and two different control injection molding grade PP/EPDM formulations (controls 1 and 2) were reactively compounded on a 53mm twin screw extruder pilot line (with an L/D ratio of about 47). The details of these formulations are given in tables 1A and 1B, where the relative amounts of materials in the formulations are listed on the basis of 100 parts oil-free rubber. The EPDM rubber used was high MW Vistalon 3666, which contained 64 wt% ethylene (based only on copolymerized ethylene and propylene) and 3.5 wt% ethylidene norbornene (based on total rubber mass). V3666 contains 75 parts of Paralux 6001 paraffinic oil (group II) based on 100 parts of dry rubber. The PP in the formulation can be roughly divided into two categories: homopolymeric PP and random copolymers of PP. Vistamaxx 3000 is also added as a second thermoplastic resin to help improve bonding properties. Other chemicals added to the formulation include carbon black masterbatch, and clay as a rubber distribution filler. A cure package is added during compounding to dynamically vulcanize the rubber phase. Additional amounts of group II Paralux 6001 oil were also fed to the extruder to extend the rubber phase and maintain processability. In examples 1-3, 9 and 10, to each formulation was added an ultra-high molecular weight polysiloxane of the nonmobile or non-migratory type, available as HMB-0221 from Dow Corning in the form of a masterbatch. In examples 4-6, to each formulation was added an ultra high molecular weight migrating type silicone oil, available as a masterbatch from Dow Corning as MB 25-501. In examples 7, 8 and 11-13 of the present invention, a combination of migrating silicone MB 25-501 and non-migrating silicone HMB-0221 was added to each formulation. In each case, the masterbatch pellets are fed at the hopper with the other components of the formulation. In the case of controls 1 and 2, the polysiloxane was omitted.

TABLE 1A

TABLE 1B

The compounded TPV pellets were injection molded into 4x6 "x 2mm plaques and their physical properties such as hardness, tensile strength, and COF were measured. Dog bone samples for tensile testing were punched out across the flow direction and testing was performed at room temperature using the ASTM D412 protocol. Hardness was measured using ASTM D2240, shore a, 15 seconds. COF properties are measured against glass lenses. In this test, a glass lens attached to a superluminescent light emitting diode (slid) was abutted against a lens from 2mm thickA10 mm wide strip cut from the injection-molded plate was moved at a speed of 600mm/min and a weight of 350g was used. For compression set measurements, pellets were molded into 0.5 "thick plates and button shaped samples were drilled. Measurements were then made on these button-shaped samples at 25% compression for 22h and at RT and an elevated temperature of about 70 ℃. Capillary measurements were performed at 204 ℃ using a two-well Rosand capillary rheometer and the data were corrected using Bagley and Rabinowitsch corrections. At 1200s^-1Is calculated based on a fitted linear regression of the corrected viscosity versus shear rate data. Bonding to the densified thermoset EPDM and TPV substrates was measured by first preparing a bonded dog bone specimen and then testing it on an Instron machine. The bonded bone shaped specimens were prepared by injection molding one half of the specimen directly onto the other half of the dense thermoset EPDM or TPV substrate. Half of the substrate is prepared by cutting at the middle of the entire substrate. The entire dense thermoset EPDM or TPV dog bone substrate is stamped from the extruded strip.

The test results are summarized in tables 2A and 2B, from which it can be seen that controls 1 and 2 exhibit typical desired formulations of approximately 80 shore a hardness with overall acceptable physical properties and bond strength to thermoset EPDM and TPV, but with very high COF values. Examples 1-3, 9 and 10 show that the use of non-migrating slip agents of the HMB-0221 type successfully reduces the COF without significantly affecting the hardness and bond strength of the TPV formulation. Examples 4-6 used similar amounts of migration-type slip agents (MB 25-501) as in examples 1-3. While this type of slip agent reduces the COF value, it is not as effective as a non-migrating slip agent and an increase in hardness is also seen. In examples 7 and 11 of the present invention, where a combination of migrating and non-migrating slip agents is used, where the amount of non-migrating slip agent is about 3/4 of the amount of migrating slip agent, surprisingly even lower COF values are obtained. The use of both types of substrates also slightly improves the bonding performance. Example 13 of the present invention used a similar strategy in a slightly different formulation to obtain a material with a lower hardness in the target hardness range of about 70 shore a. Similar COF properties are obtained even at lower hardness levels.

Examples 8 and 12 of the present invention also used a combination of migrating and non-migrating slip agents, but the ratio of non-migrating slip agent to migrating type slip agent was reversed, i.e., the ratio was about 1.4. The COF was reduced, but not as good as their counterparts the inventive formulations 7 and 11.

Various modifications and alterations that do not depart from the scope and spirit of this invention will become apparent to those skilled in the art. The present invention is not limited to only the exemplary embodiments described herein.

TABLE 2A

TABLE 2B

RT ═ room temperature