Macromers of vinylidene fluoride arylate-terminated poly(vinylidene fluoride) and its copolymeric thermoplastic elastomers

Abstract: Polymers prepared from vinylidene fluoride having controlled molecular weights and sulfate end groups are described. The sulfate end group can be displaced with acrylic-type acids to produce the corresponding acrylate terminated poly(vinylidene fluoride) macromolecular monomers. These macromolecular monomers can be copolymerized with acrylates that give rubbery homopolymers to form thermoplastic elastomers.

Description: FIELD OF THE INVENTION The present invention relates to the polymerization of vinylidene fluoride into functionally terminated polymers which are converted to macromolecular monomers by acid catalyzed displacement reactions with acrylic-type acids. These macromolecular monomers can be copolymerized with acrylates to make thermoplastic elastomers or compatibilizing agents. BACKGROUND F-T. Lin and F-M. Lin in J. Macromol. Sci. Chem., 1989 , A26 (1), 1. This work generally relates to the characterization of NMR peaks in vinylidene fluoride. D. A. House, Chem. Rev. 1962 , 185. This article relates to K₂S₂O₈ initiating systems in the presence of alcohols. J. Oku, R. J. H. Chan, H. K. Hall, Jr., and O. R. Hughes, Polymer Bulletin, 1986 , 16 , 481. This article relates to the synthesis of hydroxy terminated poly(vinylidene fluoride) by homogeneous free radical polymerization. The end group in this polymer is derived from methanol, the polymerization solvent. The macroalcohol is then reacted with methacryloyl chloride to form methacrylate-terminated poly(vinylidene fluoride) containing a methylene (-CH₂-) group in the end group which is reported to copolymerize with methyl methacrylate, producing a thermoplastic. BRIEF DESCRIPTION OF THE DRAWINGS Figures 1 and 2 show the stress/strain curves for blends and graft copolymers poly(VF₂)/poly(ethyl acrylate). SUMMARY OF THE INVENTION Sulfate-terminated vinylidene fluoride polymers of controlled molecular weight are produced by persulfate-initiated emulsion polymerization of vinylidene fluoride in the presence of low molecular weight alcohols. The polymers can be converted to macromolecular monomers by displacement of the sulfate end group with acrylic-type acids in the presence of acid catalysts. The macromolecular monomers can be copolymerized with simple acrylate monomers. When the acrylate is one that gives rubbery homopolymer, the resulting poly(acrylate-co-macromolecular monomer) is a thermoplastic elastomer which can be used in seals, gaskets and molded items. DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a sulfate-terminated poly(vinylidene fluoride) having the formula M⁺ - O₃SO―(A) n ―H wherein said A represents the repeat unit, (CH₂CF₂), which is present in any orientation within the chain, either head to tail, head to head, or both; wherein n is from 8 to 300; and wherein M⁺ is a monovalent cation. Sulfate-terminated poly(vinylidene fluoride) . The present invention relates to vinylidene fluoride (VF₂) polymerized free radically by persulfate initiators in the presence of an alcohol to give polymers with controlled molecular weight and ⁻O₃SO- head groups, structure 1 . Emulsion polymerization under pressure is the preferred method. Both primary and secondary alcohols can be used. They can vary in size from C₁ to C₁₀ with C₁ to C₄ being preferred, and primary alcohols being most preferred. The amount of alcohol can vary from 0.002 moles to 2.5 moles per mole of VF₂, desirably 0.003 moles to 2.0 moles per mole VF₂, and preferably 0.003 moles to 1.5 moles per mole of VF₂. Ideally, this ratio should be maintained by metering. The alcohols are believed not to be chain transfer agents, but rather inhibitors, where the alcohol-derived radical rapidly terminates following hydrogen transfer. This conclusion is based on the surprising observation that alcohol-derived radicals neither start nor end the poly(vinylidene fluoride) chains in this system. The greater partitioning of higher alcohols into the organic phase is believed to make them more effective in limiting the molecular weight. Thus, the amount of alcohol required can vary greatly depending on the specific alcohol used. When carried out by emulsion polymerization, the weight of monomer charged per 100 grams of water can range from 5 to 50g with a preferred amount being from 10 to 25 grams. The preferred surfactant is a salt of perfluorooctanoic acid in an amount from about 0.25 to about 1.5 grams per 100 of monomer. However, typical nonfluorinated anionic surfactants, such as sodium octanoate and dodecylsulfate are also effective. A buffer can be used to stabilize the pH during the polymerization. One preferred buffer is K₂HPO₄ which can be used from 0.05 to 1.5M. Potassium persulfate is the preferred initiator for this system. However, persulfates with other common counter ions, such as sodium or ammonium, are also effective. The amount of persulfate can vary from about 5 to 100 millimoles per mole of monomer with the preferred amount being from 10 to 20 millimoles per mole of monomer. The reaction temperature can vary from ambient to 120°C. However, the range from 50 to 100°C is preferred, with 70° to 90°C being most preferred. At these temperatures, vinylidene fluoride is a gas and develops a pressure that depends on the moles of vinylidene fluoride present, temperature, and the volume of the reactor head space. After the reaction temperature has been reached, the reaction time is typically 2-4 hours at 80-90°C. The molecular weight of the polymer 1 is controlled by the amount and kind of alcohol used. Lower molecular weight polymers are obtained with increasing amounts of alcohol, higher alcohols being more efficient. Generally, primary alcohols are preferred over secondary alcohols. The average number of VF₂ repeat units, n=x+2y, can vary from 8 to 300, with the preferred range depending on the application. Attractive thermoplastic elastomers can be prepared from macromolecular monomers with n equal to 20 to 100, with a preferred range of 20 to 65. When used as compatibilizing agents, the value of n is from 50 to 200 with a preferred range of 75 to 150. Although the repeat unit of poly(vinylidene fluoride) is written as (CH₂CF₂), it is known that the monomer is sometimes incorporated into the chain with reverse addition (head to head) to give small amounts of the sequence (CH₂CF₂CF₂CH₂). These are known variations from the normal head to tail addition. For simplicity, the structure 1 can be expressed as structures 2 or 3 , wherein (CH₂CF₂) or (A) is meant to include the variations described more specifically in the structure 1 , wherein said (CH₂CF₂) or (A) represents the repeat unit which is present in any orientation within the chain, either head to tail, head to head, or both. M⁺ represents a common counterion for the sulfate terminated poly(vinylidene fluoride). These common counterions could be sodium, potassium or ammonium. Nuclear Magnetic Resonance (NMR) spectroscopy is used to characterize the sulfate-terminated poly(vinylidene fluoride). It is performed at 200 MHz with DMSO-d₆ as the solvent. Table I shows the chemical shift and fine structure assignments for the various hydrogens. The chemical structure of the polymer is shown below with H a -H h in Table I being the hydrogen atoms labeled (a)-(h). There is no evidence of alcohol-derived radicals appearing as end-groups in the polymer. H a is the only resonance observed in the region of δ4.0 where the α-hydrogen of the alcohol would appear. Chemical Shifts of Sulfate-Terminated Poly(Vinylidene Fluoride) Chemical Shift (δ) J(Hz) Assignment 3.95(t) 13.5 H a 2.88(m) H b 2.25(m) H c 6.34(t,t) 4.5, 55 H d 1.78(t) 19.4 H e The present invention also pertains to a macromolecular monomer of poly(vinylidene fluoride) having the formula wherein said A represents the repeat unit (CH₂CF₂), which is present in any orientation within the chain, either head to tail, head to head, or both; wherein R¹ represents H or CH₃; and wherein n is as described above. Further the present invention relates to a composition of matter, comprising; a nominally random copolymer of a monomer with a macromolecular monomer, wherein said monomer is one or more acrylates of the formula wherein said R² is H or CH₃, wherein R³ is a C₁-C₁₂ alkyl group and optionally contains the heteroatoms nitrogen, oxygen, or sulphur in the chain or appended to the chain, wherein said macromolecular monomer is of the formula wherein R¹ can be hydrogen or a methyl group, wherein A represents a repeat unit (CH₂CF₂) which is present in any orientation within the chain, either head to tail, head to head, or both; wherein n is as described above, and wherein the weight percent of said (CH₂CF₂) repeat unit is from 3 to 70 weight percent of said random copolymer. More preferably the present invention relates to a composition as described above, wherein the weight percent of said (CH₂CF₂) repeat units in the total composition is from 3 to 50 and said R³ is a C₁-C₁₂ alkyl group free of heteroatoms, and further to a composition as above described, wherein the weight percent of said (CH₂CF₂) repeat units in the total composition is 10 to 50 and said R¹ is hydrogen. The nominally random copolymer in the composition according to the present invention can undergo crystallization of some portion of said (CH₂CF₂) repeat units and wherein said acrylate monomers are ethyl acrylate, butyl acrylate, or 2-ethylhexyl acrylate. In the composition according to the present invention preferably n is from 20 to 100, more preferably from 20 to 65 and said R³ is a C₁-C₁₂ alkyl group free of heteroatoms. In a further embodiment the present invention relates to a composition as described above, wherein comonomers, up to an equal weight based on said acrylate monomers, are copolymerized with said acrylate monomer and said macromolecular monomer; said comonomers including styrene, alkyl or halogen substituted styrenes, 1,4-dienes, acrylic acid, methacrylic acid, acrylamide, N-substituted acrylamide, or acrylonitrile. The composition of matter of the present invention comprises an essentially linear polymer of acrylate-type monomers wherein said acrylate repeat unit is of the structure having nominally random variation in the appendages R⁵, wherein said R⁴ on successive repeat units is either hydrogen or methyl and said R⁵ on successive repeat units is either a.) one or more C₁-C₁₂ alkyl radicals which optionally contain nitrogen, oxygen, or sulfur in the chain, or b.) (A) n -H, wherein said A represents (CH₂CF₂), which is present in any orientation within the chain, either head to tail, head to head, or both; wherein the value of n is as described above; and wherein said (A) n -H units in said composition are capable of crystallization. Preferably said C₁-C₁₂ alkyl radicals contain no heteroatoms. Furthermore R⁴ is hydrogen when said R⁵ is an alkyl radical and the value of n is from 20 to 65. The present invention further concerns a thermoplastic elastomer comprising an elastomeric acrylate backbone having appendages therefrom of poly(vinylidene fluoride), wherein each said poly(vinylidene fluoride) appendages have a degree of polymerization n as described above. Said acrylate backbone is derived from alkyl acrylate monomers and macromolecular monomers of poly(vinylidene fluoride); and said alkyl groups are ethyl, butyl, 2-ethylhexyl, or combinations thereof. This invention will be better understood by reference to the following examples which serve to illustrate but not to limit the present invention. Example 1 A 500 mL pressure reactor was fitted with agitator, liquid sampling line, vacuum line, thermowell, and vapor/liquid charging line. The reactor was then evacuated to 13.3 Pa (0.1 mm Hg). A solution comprising 2.46 g (9.12 mmol) K₂S₂O₈, 3.63 g K₂HPO₄, and 1.04 g perfluorooctanoic acid in 208 mL of distilled water was purged with nitrogen. Immediately before transferring to the reactor, 3.49 g of purged ethanol (0.0758 mol) was added, and the mixture was transferred under vacuum. The lower half of the reactor was cooled in liquid nitrogen and VF₂ (36.3 g, 0.568 mol) was distilled into the reactor from a tared lecture bottle. The reactor was warmed, stirring was started (1200 rpm), and the reaction proceeded for 2.7 hours from the time the reactor contents reached 70°C. Typically, approximately 20 minutes were required to reach this temperature. The polymerization was followed by measuring total solids and ended when pressure became constant. The reactor was cooled and the contents discharged. Water was evaporated by gently heating on a hot plate. The salts were removed by stirring with 10% aqueous ammonia. The mixture was centrifuged to recover the polymer particles. They were suspended in fresh water and centrifuged three more times. The solids were dried in a vacuum oven at 50°C overnight. The yield was 10.7 g of polymer, 30% conversion. Example 2 A 5 liter reactor, equipped similarly to the reactor in Example 1, was used for a scaled-up reaction. The reactor was evacuated and filled with nitrogen several times. It was then evacuated and cooled to -10°C. The nitrogen-purged aqueous solution containing 24.6 g (91.2 mmol) K₂S₂O₈, 10.4 g perfluorooctanoic acid, 36.3 g K₂HPO₄, and 34.9 g (0.758 mol) of ethanol in 2.08 liters of water were charged to the reactor after purging with nitrogen in the usual way. This was followed by liquid charging of 363 g (5.68 mol) of VF₂. The temperature controller was set for 84°C and heating was started. When the contents reached 8°C, stirring was started and gradually increased to 900 RPM. The contents reached 70°C in 44 minutes at a pressure of 3.59 MPa (521 psi). An exotherm to 85°C was reached in 57 minutes at a pressure of 3.33 MPa (484 psi). After 155 minutes had elapsed, the temperature had declined to 80°C (3.16 MPa [458 psi]). The reactor was then cooled to 28°C and the contents were discharged, giving a stable, creamy foam. A white solid separated on standing. This latex/solids mixture was centrifuged to remove the solid which was air dried at 70°C. The remaining liquid was evaporated, yielding additional white solid. Both solid portions were stirred overnight with a 10-fold volume of water, centrifuged, rinsed, and centrifuged again before drying at 50°C overnight. The combined yield was 66.0 g, 18.2% conversion. The following table gives data summarizing the above examples together with several additional polymerizations which were carried out in a similar manner. Table II, columns 7-11 show that the degree of polymerization of sulfate-terminated poly(vinylidene fluoride) can be controlled from between 20 and 60 with an ethanol:VF₂ mol ratio of 0.357 to 0.133. Columns 1-4 further show that DP can be reduced to as low as 10 to 12 when methanol:VF₂ is 2.0. These results show that ethanol is more efficient than methanol in lowering molecular weight. That n-butanol is even more efficient is illustrated in column 5. A DP as low as 14 is obtained when n-butanol:VF₂ is 0.067. Monomer conversion is also influenced by the amount and kind of alcohol used, and it varies from between 4 and 52% under these conditions. In general, there is good agreement between the head and end groups, with their mol ratio being close to 1.0. Moreover, there is no evidence of end groups derived from the alcohol. The sulfate-terminated polymers 1 are precursors to macromolecular monomers of controlled molecular weight. They can react with nucleophilic reagents such as alcohols, thiols, water, or carboxylic acids in so-called nucleophilic displacement reactions, where the nucleophile replaces the sulfate group on the sulfate-terminated poly(vinylidene fluoride) 1 . Acrylate-Terminated Poly(vinylidene fluoride) or alternatively expressed as The macromolecular monomers of this invention can be described by the structures 4 and 5 , wherein said A represents the repeat unit (CH₂CF₂) which is present in any orientation within the chain, either head to tail (x), head to head (y), or both with n representing the total number of such units. The macromolecular monomers 4 are made from the reaction of acrylic (R¹=H) or methacrylic (R¹=CH₃) acid, the sulfate-terminated poly(vinylidene fluoride) 1 , catalytic H₂SO₄, and optionally 2,6-tert-butyl-4-methylphenol (BHT) at elevated temperatures. Sulfate-terminated poly(vinylidene fluoride) with degrees of polymerization (n) from 8 to 300 can be used. The macromolecular monomers can be copolymerized with other monomers to give various graft copolymers that can serve as thermoplastic elastomers or compatibilizing agents. The degrees of polymerization for thermoplastic elastomers are from 8 to 100, desirably from 20 to 100, and with the preferred range being 20 to 65. When used in compatibilizing agents, the degree of polymerization would be from 50 to 200, and preferably from about 75 to 150. Acrylic or methacrylic acid is used as a solvent and reactant in an amount ranging from 3.0 to 30 mL/g of sulfate-terminated poly(VF₂). The preferred amount is from 5.0 to 10 mL/g. Other optional swelling agents or solvents include dimethyl sulfoxide (DMSO), N,N-dimethylformamide (DMF), and N,N-dimethyl acetamide (DMAC). Sulfuric acid catalyzes the reaction. It can be used in an amount of from 0.025 to 0.50 mL/g of sulfate-terminated poly(VF₂). The preferred amount is 0.10-0.25 mL/g. Other strong acids such as phosphoric acid also catalyze the reaction. Butylated hydroxy toluene (BHT) can be included as an antioxidant. The amount can be from 0.0 to 0.020 g/g of sulfate-terminated poly(VF₂). Other phenolic antioxidants may be substituted for BHT. The reaction temperature may range from 50 to 200 o C with the preferred temperature range being 80-120 o C, typically 100 o C. The reaction time varies with temperature. At 100 o C the reaction is accomplished in 1.5 hours. Typically, excess acrylic or methacrylic acid is distilled off and the macromolecular monomer precipitated from a suitable nonsolvent such as hexane. The precipitate is washed in a stirred 5% aqueous NaHCO3 solution, vacuum filtered, rinsed several times with water, and vacuum dried at room temperature overnight. Alternatively, the reaction can be performed under Reaction Processing conditions using an appropriately designed extruder. H-NMR can be used to fully characterize the structure of methacrylate-terminated poly(vinylidene fluoride) 6 . The spectra are for DMSO-d₆ solutions at 200 MHZ. The structural formula for 6 is given below with the hydrogen atoms labeled. These labels identify the chemical shifts for each type of hydrogen in Table III. Chemical Shifts of Methacrylate-Terminated Poly(vinylidene fluoride) Chemical Shift (δ) J(Hz) Assignment 6.11, 5.78(s) H a,b 1.90(s) H c 4.46(t) 13.9 H d 2.88(m) H e 2.24(m) H f 6.33(t,t) 4.5, 55 H g 1.77(t) 19. H h The area under each peak is proportional to the number of hydrogens of that type, and these data converted to mol ratios are given in Table V. GPC molecular weight distributions for the acrylate terminated poly(VF₂) can also be obtained when performed with a solvent that prevents sorption on the column. Methyl pyrrolidone containing 0.05 ppm of LiBr appears to work well (Table IV). In general, the molecular weight distributions are bimodal, though they approach a unimodal distribution at DP 60. Since K and a values for poly(VF₂) are unknown, true molecular weights can be estimated by applying the polystyrene calibrations, then adjusting those molecular weights by a factor (0.61) that corresponds to the comparative extended chain formula weights. This should be a reasonable approximation in this case since methyl pyrrolidone is a good solvent for poly(VF₂). The GPC results nicely complement the H-NMR results since the latter gives only a single, average value for DP . Comparison of GPC and H-NMR Determined Molecular Weight of the Macromolecular Monomers 6 GPC MOL WEIGHT X 10⁻³ H-NMR Mn Mw Peaks Mw/Mn DP DP 4.08 15.3 1.32,10.7 3.75 64 60 2.94 10.6 0.903,7.99 3.60 46 34 1.60 5.15 1.36,9.40 3.22 25 20 This invention will be better understood by reference to the following examples which serve to illustrate but not to limit the present invention. Example 3 A three neck, 100 mL flask was fitted with distillation column/water cooled condenser, bubbler, magnetic stirring bar, thermocouple, and septum. Ten grams of sulfate-terminated poly(vinylidene fluoride), 75 mL of methacrylic acid, and 0.0186 g BHT were charged to the reactor. The mixture was stirred and 2.5 mL of conc H₂SO₄ was injected. The flask was heated to 100°C and maintained at that temperature for 1.5 hours. The flask was then cooled to 55-58°C at which time the bubbler was removed and about one-third of the methacrylic acid was distilled off at 667-933 Pa (5-7 mm Hg). After cooling to room temperature, the reactor contents were precipitated from 300 mL of rapidly stirred hexane. A gummy yellow/brown precipitate formed. The solid was separated from the hexane by centrifuging. The precipitate was vigorously stirred with 300 mL of 5% aqueous NaHCO₃, during which time the solid became harder and lightened in color. The mixture was vacuum filtered, rinsed several times with water, and vacuum dried overnight at room temperature. The yield was 9.55 grams. The following table gives data to summarize the above examples plus several additional syntheses which were carried out in a similar manner. Table V shows five different reactions of methacrylic acid with sulfate-terminated poly(vinylidene fluoride) to produce macromolecular monomers. The degree of polymerization ( DP ) of the macromolecular monomer is similar to that of the sulfate-terminated poly(vinylidene fluoride), and the yields are very good. The utility of this macromolecular monomer is that it can be copolymerized with other monomers to impart useful properties originating from the poly(vinylidene fluoride) grafts. Physical crosslinks originating from the crystallization of these grafts is one example. These domains have excellent solvent resistance and thermal stability (mp 150-170°C). Copolymers of Macromolecular Monomer with Other Monomers The macromolecular monomers 5 can be copolymerized with one or more acrylates of structure 7 under homogeneous free radical conditions; wherein R² = H or methyl and R³ can be a C₁ to C₁₂ radical, which can optionally contain the heteroatoms nitrogen, oxygen, or sulphur in the chain or appended to the chain. Examples of R₃ include butyl, nonyl, dodecyl, oxa and thialkyl, epoxy and thioepoxyalkyl, halogenated alkyl, aminoalkyl. The preferred R¹ group in the macromolecular monomer 5 is H or CH₃, while the preferred R³ groups in the acrylate monomers 7 are C₂ to C₈ alkyl free of heteroatoms. Optionally, other monomers that copolymerize with acrylates and methacrylates can also be used, including styrene and alkyl or halogen-substituted styrenes, 1,4-dienes, acrylic acid and methacrylic acid, acrylamide, N-substituted acrylamides and acrylonitrile. When such optional comonomers are used they can be present up to an amount equal to said acrylate monomers or desirably less than 80 weight percent of the amount of acrylate monomers, and preferably less than 60 weight percent of the amount of the acrylate monomers. The weight percent of the macromolecular monomer 5 in the copolymer can range from 3 to 70, and is preferably 10 to 50. The weight percent of poly(VF₂) in the copolymer can range from 3 to 50 and is preferably 10 to 50. If the resulting copolymer is to be a thermoplastic elastomer, the weight percent macromolecular monomer 5 is preferably 10-40. The copolymerization can be performed in a solvent in which the macromolecular monomer and acrylate monomer 7 are soluble. Examples include DMSO, DMF, or DMAC. Alternatively, if the macromolecular monomer swells or dissolves in the monomer at the polymerization temperature, the reaction might be done with little or no solvent. Copolymerization with little or no solvent is referred to as reaction processing and can be performed in an appropriately designed extruder. Solvents are used in amounts sufficient to achieve a miscible system, wherein the radical chain ends can access all of the monomers, and to allow for mixing of the reactants and polymeric product. This amount can be from 0 to 15 times the combined weight of monomers. Polymerization is performed with free radical initiators. With 2,2-azobis(2-methylbutanenitrile), the range is from 0.50 to 4.0 mg of initiator/mmol of acrylate 7 . Since both monomer and macromolecular monomer are acrylate type monomers, any of the free radical initiators typically used for acrylate monomers can be used such as persulfates, azo, and peroxide initiators. When performed in solution, the preferred initiators are the azo type with AIBN or 2,2-azobis(2-methylbutanenitrile) being the most preferred. The polymerizations are done in an inert atmosphere of nitrogen or argon. The choice of initiator depends on the polymerization temperature desired and can be from ambient to 200°C (reaction processing). With 2,2-azobis(2-methylbutanenitrile), the preferred temperature is about 55-65°C. The copolymer can be recovered by precipitation from methanol and centrifugation. Drying is performed under vacuum at 80°C. This invention will be better understood by reference to the following examples which serve to illustrate but not to limit the present invention. Example 4 Analytical Scale, Copolymerization of Macromolecular Monomer with Ethyl Acrylate A 100 mL, 3-neck flask, fitted with a paddle stirrer, condenser/bubbler, thermocouple/controller, nitrogen inlet, and septum was charged with 3.00 g of the macromolecular monomer 6 and 40 mL of DMSO (HPLC grade). The mixture was stirred and purged with nitrogen or argon. The flow of argon or nitrogen was reduced and 8.1 mL of nitrogen-purged ethyl acrylate (7.5 g, 0.075 mol) was injected into the reactor. The reactor was then heated to 60°C. A solution of 0.124 g (0.630 mmol) of 2,2-azobis(2-methylbutanenitrile) in 30 mL DMSO (HPLC grade) was purged and metered into the reaction flask at 0.80 mL/min for 22.5 min., thereby delivering 73 mg, 0.38 mmol of initiator. The conversion to copolymer was followed by percent solids. After 2.7 hours, the reactor was cooled, and the homogeneous, viscous reaction mixture was added to 800 mL of vigorously stirred methanol. After stirring 1 hour, the mixture was centrifuged and the recovered solid rinsed with fresh methanol and centrifuged three additional times. The solids were air dried, then vacuum dried at 80°C to yield 5.32 g of light brown rubber. The methanol solution was evaporated to recover 1.8 g of soft and somewhat sticky polymer. Example 5 Preparative Scale, Copolymerization of Macromolecular Monomer with Ethyl Acrylate The reaction was performed in a 3-neck 1 L flask with paddle stirrer, condenser/bubbler, and 3 port adapter, thermocouple/controller, and two septa. The flask was charged with 430 mL of DMSO (HPLC grade), 23 g of macromolecular monomer 6 , and the mixture was purged with argon. Under reduced argon flow, 56.9 g (0.569 mol) of argon-purged ethyl acrylate was then added and the reactor heated to 60°C. Ten mL of a degassed solution of 1.4296 g of 2,2-azobis(2-methylbutanenitrile) in 25 mL DMSO was then injected. An exotherm occurred which maintained the temperature at 63-64°C. The solution rapidly became viscous and difficult to both stir and remove samples. Heating was stopped after 64 min. reaction time and the reaction mixture diluted with 100 mL of DMSO to facilitate transfer. The apparently homogeneous solution was added to 4.5 liters of methanol that was vigorously stirred with a propeller stirrer. The mixture was centrifuged and the recovered solids rinsed with fresh methanol and centrifuged an additional three times. The solids were air dried and then vacuum dried at 80°C overnight giving 48.4 g of tan rubber. A methanol soluble fraction of 5.0 g was also recovered. The following table gives data to summarize the above examples plus several additional polymerizations which were carried out in a similar manner. The H-NMR spectra of the copolymers show that the macromolecular monomer is polymerized. The vinyl hydrogen atoms, normally at δ6.11 and δ5.78 are absent while the end group, CF₂H, at δ6.3 is prominent and readily observable. Table VI shows that ethyl acrylate conversions of 43 to 78% are readily achieved and that nearly all of the copolymerized ethyl acrylate and macromolecular monomer were recovered in the final product. The H-NMR-determined weight percent of poly(vinylidene fluoride) shows a high incorporation of macromolecular monomer. Characteristics of the Thermoplastic Elastomer Formed Acrylate polymers formed by free radical polymerizations are often found to contain insoluble fractions due to crosslinking reactions. A sample of 0.200 g of copolymer from Run 2, Table VI was dissolved in 10 mL DMSO and stirred 20 hours at 60-65°C. The solution was filtered through a coarse sintered glass filter funnel with Celite filter aids. A gravimetric determination showed that 67% of the polymer was soluble indicating that some crosslinking had occurred. The term thermoplastic elastomer means a material combining the good mechanical properties of a thermoset elastomer or rubber, like acrylate rubbers, with the ability of thermoplastics to be molded and remolded. The advantage provided by such materials is that they avoid the costly curing process of thermoset elastomers. The curing processes are costly for many reasons. They are time consuming and require accurate measurements of curing agents and their thorough incorporation. When thermoset materials are cured, they can no longer be reprocessed without breaking chemical bonds. Thermoplastic elastomers (TPE) have hard and soft segments or domains in the polymer molecule or compound. The soft regions are responsible for rubberlike properties while the hard regions act as physical crosslinks, adding strength and toughness to the TPE. In this invention, the acrylate polymer is generally the elastomer or soft regions while the poly(vinylidene fluoride) segments are the hard regions. Poly(vinylidene fluoride) is a crystalline polymer. When grafted to rubbery polyacrylates, the poly(vinylidene fluoride) chains associate into crystalline domains, producing physical crosslinks that function in the same way as chemical crosslinks in creating good mechanical properties. The mere incorporation of a thermoplastic polymer in an elastomer can enhance properties in some cases, but they tend not to act as physical crosslinks because there is little or no chemical connectivity between the thermoplastic and the elastomer. To demonstrate the improvement of thermoplastic elastomers over physical blends of two homopolymers, stress/strain curves for blends and graft copolymers are incorporated in this description as Figures 1 and 2. The copolymers used in Figures 1 and 2 are from Table VI. At about 20 and 30% VF₂, the blends have a pronounced "knee" in the stress/strain curve and they undergo flow with permanent extension during the strain measurements. The corresponding copolymers, on the other hand, are much more elastic and return to nearly their original shape when broken. Moreover, the area under the stress-strain curve is significantly greater for most of the copolymers. These data are preliminary in that only one test specimen for each composition was tested rather than groups of 3 or 5. Indeed, the copolymers show advantages over the blends in that they are more elastic, undergo less flow under strain; and in most cases, they absorb more mechanical energy. Thus, the crystalline, poly(VF₂) phase clearly provides physical crosslinks in this system. Dynamic Scanning Colorimetry (DSC) and microscopy measurements clearly confirm that these copolymers have the morphology required of thermoplastic elastomers. The macromolecular monomer segments readily crystallize with melting peaks in the vicinity of 160°C. Table VII shows the DSC-measured melting peaks and ΔH for various macromolecular monomers and copolymers. Moreover, optical microscopy performed on the copolymer containing 33% VF₂ (Run #2 Table VI) recrystallized isothermally from the melt (135°C) shows a dense, uniform distribution of spherulites on the order of about 4-5 µm. Still smaller spherulites develop when crystallized from DMSO solution. The crystallites must generally be small since the molded samples are translucent. In Table VII, rows 1-3 show that both the macromolecular monomers and copolymers are crystalline with a melting point in the 120-160°C range. The two columns of ΔH values confirm that in most cases, the poly(vinylidene fluoride) component develops nearly the same degree of crystallinity as do homopolymers of vinylidene fluoride. Thermoplastic elastomers are used in automotive, wire and cable, adhesives, footwear, and mechanical goods. The high crystalline melting point of the poly(vinylidene fluoride) domains together with their excellent solvent resistance makes these acrylate-based thermoplastic elastomers useful in seals, gaskets, and molded items.

Claims: A sulfate-terminated poly(vinylidene fluoride) having the formula M⁺ ⁻ O₃SO―(A) n ―H wherein said A represents the repeat unit, (CH₂CF₂), which is present in any orientation within the chain, either head to tail, head to head, or both; wherein n is from 8 to 300; and wherein M⁺ is a monovalent cation. A sulfate-terminated poly(vinylidene fluoride) according to Claim 1, wherein said polymer is made by emulsion polymerization and wherein said value of n is from 20 to 100. A sulfate-terminated poly(vinylidene fluoride) according to Claim 2, wherein said value of n is from 20 to 65, and wherein M⁺ is K⁺, Na⁺, or NH 4 + . A sulfate-terminated poly(vinylidene fluoride) according to Claim 1, wherein said polymer is made by emulsion polymerization, and wherein said value of n is from 50 to 200. A macromolecular monomer of poly(vinylidene fluoride) having the formula wherein said A represents the repeat unit (CH₂CF₂), which is present in any orientation within the chain, either head to tail, head to head, or both; wherein R¹ represents H or CH₃; and wherein n is from 8 to 300. A macromolecular monomer of poly(vinylidene fluoride) according to Claim 5, wherein said value of n is from 20 to 100. A macromolecular monomer of poly(vinylidene fluoride) according to Claim 5, wherein the value of n of said macromolecular monomer is from 20 to 65. A macromolecular monomer of poly(vinylidene fluoride) according to Claim 5, wherein said value of n is from 50 to 200. A composition of matter, comprising; a nominally random copolymer of a monomer with a macromolecular monomer, wherein said monomer is one or more acrylates of the formula wherein said R² is H or CH₃, wherein R³ is a C₁-C₁₂ alkyl group and optionally contains the heteroatoms nitrogen, oxygen, or sulphur in the chain or appended to the chain, wherein said macromolecular monomer is of the formula wherein R¹ can be hydrogen or a methyl group, wherein A represents a repeat unit (CH₂CF₂) which is present in any orientation within the chain, either head to tail, head to head, or both; wherein n is from 8 to 300, and wherein the weight percent of said (CH₂CF₂) repeat unit is from 3 to 70 weight percent of said random copolymer. A composition according to Claim 9, wherein the weight percent of said (CH₂CF₂) repeat units in the total composition is from 3 to 50 and said R³ is a C₁-C₁₂ alkyl group free of heteroatoms. A composition according to Claim 9, wherein the weight percent of said (CH₂CF₂) repeat units in the total composition is 10 to 50 and said R¹ is hydrogen. A composition according to Claim 9, wherein the nominally random copolymer is capable of undergoing crystallization of some portion of said (CH₂CF₂) repeat units and wherein said acrylate monomers are ethyl acrylate, butyl acrylate, or 2-ethyl hexyl acrylate. A composition according to Claim 9, wherein n is from 20 to 100 and said R³ is a C₁-C₁₂ alkyl group free of heteroatoms. A composition according to Claim 9, wherein n is from 20 to 65. The composition of Claim 9; wherein comonomers, up to an equal weight based on said acrylate monomers, are copolymerized with said acrylate monomer and said macromolecular monomer; said comonomers including styrene, alkyl or halogen substituted styrenes, 1,4-dienes, acrylic acid, methacrylic acid, acrylamide, N-substituted acrylamide, or acrylonitrile. The composition of Claim 15, wherein said n is from 20 to 100. The composition of Claim 15, wherein said n is from 20 to 65. The composition of Claim 15, wherein said n is from 50 to 200. A thermoplastic elastomer, comprising an elastomeric acrylate backbone having appendages therefrom of poly(vinylidene fluoride), wherein each said poly(vinylidene fluoride) appendages have a degree of polymerization from 8 to 300, and wherein said acrylate backbone is derived from alkyl acrylate monomers and macromolecular monomers of poly(vinylidene fluoride); and said alkyl groups are ethyl, butyl, 2-ethylhexyl, or combinations thereof. The thermoplastic elastomer of claim 19, wherein n is from 20 to 65.

Inventors: NICHOLAS PAUL PETER, NICHOLAS, PAUL PETER
Applicants: GOODRICH CO B F, THE B.F. GOODRICH COMPANY
Application year: 1992
Main classification: C08F299
IPC codes: C08F299, C08F14, C08L57, C08F8, C08F290