COMPOSITION FOR MAKING THERMOPLASTIC POLYURETHANES

Abstract: This invention provides a composition for making thermoplastic polyurethanes, comprising as initial components: (a) from 1 to 80 % by weight of a polydiene diol having from 1.6 to 2 terminal hydroxyl groups per molecule and a number average molecular weight in the range from 500 to 20,000; (b) from 20 to 99 % by weight of a hard segment providing combination comprising an isocyanate having two isocyanate groups per molecule and, as a chain extender, a dimer diol; a process for preparing a thermoplastic polyurethane composition and thermoplastic polyurethane composition resulting therefrom.

Description: COMPOSITION FOR MAKING THERMOPLASTIC POLYURETHANES This invention relates to compositions for making thermoplastic polyurethanes, and to the preparation of thermoplastic polyurethane compositions. Cast and thermoplastic polyurethane compositions based on the reaction of polyisocyanates with polymeric diols are well known for use as elastomers, adhesives, sealants, elastomeric surface coatings, and coatings for metals and plastics. As will be described in detail hereinafter, the polyurethanes of the present invention are based on a polydiene diol, an isocyanate, and a relatively low molecular weight chain extending diol. In this composition the polydiene serves as the soft, rubbery portion of the polyurethane. The dnsocyanate and chain extending diol react together to form a rigid segment of the polymer. Because of the reactivity of isocyanates and alcohols, the polydiene is chemically bound at its termini to the hard segments . In this way a segmented block copolymer is formed. The strength and other physical properties derive from the molecular structure of the segmented block copolymer polyurethane. In their high molecular weight polymerized form, the soft and hard segments are signif cantly incompatible and segregate into separate domains. In this arrangement the soft segments act as rubbery polymers and they are physically crosslinked through the segregation and vitrification or crystallization of the hard segments. It is important that the incompatibility between hard and soft segments exist in the final high molecular weight form. Without this incompatibility a leathery material would result which would have limited useful applications due to poor low temperature properties and a low upper service temperature . While it is important for high molecular weight polyurethanes to have incompatibility between hard and soft segments, this strong incompatibility must not extend to the case of the unreacted components. Intimate contact between reactants is required for full chemical reaction and high polymer formation. If the reactants are incompatible, only low molecular weight polyurethanes are achievable and these have low strengths and are not generally useful. Thus, the most useful segmented block copolymer polyurethanes are ones in which the reactive components demonstrate compatibility but upon reaction and molecular weight advancement segregate into rubbery soft segments and rigid, reinforcing hard segments. It is this balance of compatibility which must be engineered into this multicomponent polymer which yields the excellent physical properties. Conventional polyurethanes utilize polyester and polyether soft segments. Low molecular weight chain extenders having a suitable balance of compatibility with these polyols are well known. This invention utilizes a saturated polydiene diol which has significantly different compatibility characteristics. The utility of the saturated polydiene diol relates to its excellent thermal, UV and hydrolytic stability as well as its excellent low temperature mechanical properties. The novel composition hereinafter described contains a particular type of low molecular weight chain extender which exhibits a suitable balance of compatibility and yields polyurethanes of high strength and hardness. Polyurethane compositions made with polydiene diols and certain diol chain extenders are described in WO 9700901, published on 9 January 1997. The compositions described therein contained chain extenders which were low molecular weight diols. The purpose of such a chain extender is to increase the level of hard segment (the amount of isocyanate plus the amount of chain extender) in the polyurethane composition. There are many applications for these polyurethane compositions that require high hardness and high tensile properties. One example is ski boots which obviously cannot be soft and pliable. The chain extenders described in WO 9700901, both polar and apolar, are not very compatible with the polydiene diol and the isocyanate. In order to make compatible compositions with those chain extenders, the level of hard segment, i.e., the amount of isocyanate and chain extender, must be kept relatively low. This limits the resulting hardness and strength achievable in polydiene based polyurethanes. The Examples in WO 9700901 describe compositions containing proportions of hard segment ranging from 13.8 %w to 35.4 %w. Even with this limitation, a special solvent process is required to make the polar chain extenders such as 2-ethyl-l,3- hexanediol and 1, -butanediol sufficiently compatible. This process has the disadvantage that it involves removal and recovery of large proportions of solvent. It would be advantageous to be able to produce these compositions and others of increased strength and hardness without using the solvent method. It has now been found possible to provide thermoplastic polyurethane compositions having advantageous hardness and strength properties. According to the present invention, there is provided a composition for making thermoplastic polyurehtanes, comprising as initial components: (a) from 1 to 80 % by weight of a polydiene diol having from 1.6 to 2 terminal hydroxyl groups per molecule and a number average molecular weight in the range from 500 to 20,000; (b) from 20 to 99% by weight of a hard segment - providing combination comprising an isocyanate having two isocyanate groups per molecule and, as a chain extender, a dimer diol. Preferably the polyene diol has 1.8 to 2, more preferably 1.9 to 2, terminal hydroxyl groups per molecule. Preferably the number average molecular weight (Mn) of the polyene diol is in the range from 1,000 to 10,000. Preferably molar ratio of isocyanate (NCO) to total OH ranges from 0.9 to 1.1. Preferably the polyene diol is a hydrogenated polyisoprene diol or, more preferably, a hydrogenated polybutadiene diol. The polydiene diols used in this invention may conveniently be prepared anionically, e.g. as described in US Patents Nos . 5,376,745, 5,391,663, 5,393,843, 5,405,911, and 5,416,168. The polydiene diols have from 1.6 to 2, more preferably from 1.8 to 2, and most preferably from 1.9 to 2 terminal hydroxyl groups per molecule, and a number average molecular weight in the range from 500 to 20,000, more preferably from 1000 to 10,000. Hydrogenated polybutadiene diols are preferred and these preferably have 1,4-addition between 30% and 70% to minimize viscosity. Polymerization commences with a monolithium or dilithium initiator which builds a living polymer backbone at each lithium site. The conjugated diene is typically 1, 3-butadiene or isoprene. The anionic polymerization is done in solution in an organic solvent, typically a hydrocarbon like hexane, cyclohexane or benzene, although polar solvents such as tetrahydrofuran can also be used. When the conjugated diene is 1, 3-butadiene and when the resulting polymer will be hydrogenated, the anionic polymerization of butadiene in a hydrocarbon solvent like cyclohexane is typically controlled with structure modifiers such as diethylether or glyme (1, 2-diethoxyethane) to obtain the desired amount of 1 , 4-addition . The optimum balance between low viscosity and high solubility in a hydrogenated polybutadiene polymer occurs in the range of 40-60% 1, 4-butadiene content. This butadiene microstructure is achieved during polymerization at 50°C in cyclohexane containing about 6% by volume of diethylether or about 1000 ppm of glyme. Anionic polymerization is terminated by addition of a functionalizing agent, e.g. as described in US Patents 5,391,637, 5,393,843, and 5,418,296, but preferably ethylene oxide, prior to termination. The preferred di-lithium initiator is formed by reaction of two moles of sec-butyllithium with one mole of diisopropenylbenzene . This diinitiator is used to polymerize butadiene in a solvent composed of 90%w cyclohexane and 10%w diethylether. The molar ratio of diinitiator to monomer determines the molecular weight of the polymer. The living polymer is then capped with two moles of ethylene oxide and terminated with two moles of methanol to yield the desired polydiene diol. The polydiene diol can also be made using a mono- lithium initiator which contains a hydroxyl group which has been blocked as the silyl ether (e.g. as in US Patents Nos . 5,376,745 and 5,416,168). A suitable initiator is hydroxypropyllithium in which the hydroxyl group is blocked as the tπmethylsilyl ether. This mono-lithium initiator can be used to polymerize butadiene n hydrocarbon or polar solvent. The molar ratio of initiator to monomer determines the molecular weight of the polymer. The living polymer is then capped with one mole of ethylene oxide and terminated with one mole of methanol to yield the mono-hydroxy polydiene polymer. The silyl ether is then removed by acid catalyzed cleavage in the presence of water yielding the desired dihydroxy polydiene diol. The polybutadiene diols are hydrogenated such that at least 90%, preferably at least 95%, of the carbon to carbon double bonds in the diols are saturated. Hydrogenation of these polymers and copolymers may be carried out by a variety of well established processes including hydrogenation m the presence of such catalysts as Raney Nickel, nobel metals such as platinum and the like, soluble transition metal catalysts and titanium catalysts, e.g. as in U.S. Patent No. 5,039,755. A particularly preferred catalyst is a mixture of nickel 2-ethylhexanoate and triethylalummum. The polybutadiene polymer should desirably have no less than about 40% 1, 2-butadιene addition because, after hydrogenation, the polymer will be a waxy solid at room temperature if it contained less than about 40% 1, 2-butadιene addition. To minimize viscosity of the diol, the 1, 2-butadιene content should be between about 40 and 60%. The isoprene polymers have no less than 80% 1,4-ιsoprene addition in order to reduce Tg and viscosity. The diene microstructures are typically determined by 13 C nuclear magnetic resonance (NMR) in chloroform. The polydiene diols typically have hydroxyl equivalent weights between about 250 and about 10,000, preferably between 500 and 5,000. Thus, for di-hydroxy polydiene polymers, suitable peak molecular weights will be between 500 and 20,000, preferably between 1,000 and 10,000. The peak molecular weights referred to here are peak molecular weights measured by gel permeation chromatography (GPC) calibrated with polybutadiene standards having known peak molecular weights. These peak molecular weights correspond very closely to the number average mo] ecular weight. The solvent for the GPC analyses is tetrahydrofuran. The isocyanates used m this invention are diisocyanates having a functionality of two isocyanate groups per molecule, since they produce thermoplastic polyurethane compositions when combined with a true diol. Examples of suitable diisocyanates include 4 , 4 ' -diphenylmethane dnsocyanate, mixtures of isomers of diphenylmethane dnsocyanate, toluene dnsocyanate, isophoronediisocyanate, hexamethylenediisocyanate, ethylenednsocyanate and paraphenyl dnsocyanate . Preferably the isocyanate is selected from the group 4 , 4 ' -diphenylmethane dnsocyanate, toluene dnsocyanate, isophorone dnsocyanate, hexamethylene dnsocyanate, ethylene dnsocyanate, and paraphenyl dnsocyanate . Compositions according to the present invention contain a dimer diol as a chain extender. Dimer diols are described in US Patent No. 5,101,009 and the term "dimer diol" is therein defined as referring to a diol compound of the following formula (1) which is obtained by dimerizing an unsaturated fatty acid having between 15 to 21 carbon atoms and then reducing the dimer solution obtained thereby so it is present as a main constituent in an amount of at least 50% by weight of the dimer solution: wherein Ri to R 4 are each unsaturated linear organic groups where the total number of carbon atoms is between 22 to 34, and specifically Ri and R 2 , which may be the same or different, each represent an alkyl group, and R 3 and R 4 , which may be the same or different, each represent an alkylene group. Typical examples of dimer diols within the definition of general formula (1) are those wherein the total number of carbon atoms of Ri, R 2 , R 3 and R 4 is 28, i.e. a dimer diol containing 36 carbon atoms. Preferably the dimer diol contains 36 carbon atoms. A very suitable such dimer acid, derived from dimer acid produced by dimerization of unsaturated Ciβ fatty acids at mid-molecule, is commercially available ex Henkel Corp., USA. The dimer diol chain extender is a critical aspect of the present invention because it is suitably compatible with the polydiene and polyurethane components of the polydiene polyurethane compositions of the present invention. It is so compatible that it can be incorporated into the polyurethane compositions at levels to provide in combination with the isocyanate up to 90 percent hard segment or greater without requiring special solvent-based processing techniques which are required for the commonly used low molecular weight polar diol chain extenders described in more detail below. It is theorized that dimer diol is more compatible because the overall contribution of the terminal hydroxy groups to the molecule' s polarity is low because it is carried by a relatively large (e.g. C 36 ) aliphatic backbone. The percentage of hard segment in the polyurethane composition is important because it determines the strength, hardness, and rigidity of the final polyurethane. It is increased by incorporating a larger proportion of dnsocyanate and chain extender. Commonly, these hard segment components are polar and only marginally compatible with other aliphatic components. The user of dimer diol allows construction of saturated polyurethanes of high hardness and strength and polarity because of the decreased polarity of this chain extender and the resulting compatibility with saturated polydiene polyols. The advantages of the dimer diol begin to become more dramatically apparent when the hard segment content of the polyurethane composition is 30% or greater. Dimer diol is much more compatible with the polydiene diol at such concentrations than are the other chain extenders discussed herein. Furthermore, the dimer diol can be used to increase the hard segment content of the composition to as much as 90% or greater. The dimer diol chain extender can be used alone, or in combination with other chain extenders, as it has been found to increase compatibility of other previously used chain extenders which are basically incompatible with these polyurethane compositions and require special processing to get them to fully react with the other components . Examples of such incompatible polar chain extenders include linear chain extenders without carbon side chains such as 1,4-butane diol, 1,3-propane diol, ethylene diamine, and 1,6-hexane diol. Such incompatible chain extenders may comprise from 1 to 90% by weight of the total chain extender present. Other branched chain extenders may also be included but they will not help increase the crystallinity of the polyurethane composition as the linear chain extender will. They will help to increase the hardness and strength in a similar fashion to the dimer diol. Such branched chain extenders include low molecular weight diols which have methyl, ethyl, or higher carbon side chains which make these diols less polar and therefore intrinsically more compatible with the apolar hydrogenated polydienes. Examples of such chain extenders are 2-ethyl-l, 3-hexanediol (PEP diol), 1,2- propane diol, 2-ethyl-2-butyl-l, 3-propane diol (BEP diol), and 2 , 2 , 4-trimethyl-l, 3-pentane diol (TMP diol). In accordance with one preferred embodiment of the invention, the hard segment-providing combination also contains an additional chain extender selected from the group consisting of butane diol, propane diol, butyl- ethyl-propane diol, trimethyl pentane diol, and hexane diol . A preferred way to make thermoplastic polyurethanes is by the prepolymer method where the isocyanate component is reacted first with the polydiene diol to form an isocyanate terminated prepolymer, which can then be reacted further with dimer diol and any other chain extender of choice. The polyurethane compositions can be formulated to make elastomers using a solventless prepolymer method. In the solventless prepolymer method, the polydiene diol is heated to at least 70°C and not more than 100°C, and then mixed with the desired amount of isocyanate for at least 30 minutes under nitrogen flow. The desired amount of dimer diol and other chain extender is added and thoroughly mixed. The mixture is then poured into a heated mould treated with a mould release compound. The polyurethane composition is formed by curing in the mould for several hours at 90 to 110°C. A second preferred way to make thermoplastic polyurethanes is by the one-shot method. In this method the polydiene diol and chain extending diols are mixed and heated to 90°C to 100°C. The dnsocyanate is heated separately to 70°C to 80°C. The dnsocyanate is introduced to the polydiene diol plus chain extending diol mixture and this multicomponent mixture is stirred vigorously for 1 minute. The reacting mixture is poured into a teflon coated mould which is preheated to 105°C and 138 x 10 6 Pa (20,000 psi) pressure and held in this condition for 1 hour. The resulting polyurethane is then post-cured at ambient pressure and 105°C for 16 hours . The polymerization process can be conducted m the presence of catalysts. Catalysts useful in accelerating the NCO/OH reaction are tertiary amines such as tetramethyl butane diamine, and triethylamme, pyπdine, 1, 4-dιaza (2, 2, 2) bicyclo-octane and organometallic compounds such as tin dioctoate and dibutyl tin dilaurate . These catalysts are used at levels ranging from 0.001% by weight to 1.0% by weight. The invention further provides a process for preparing a thermoplastic polyurethane composition which comprises reacting together the components of a composition of the invention as defined above, the dimer diol, and additional chain extender, when used, being reacted during or after reaction between the polyene diol and the isocyanate. Further in accordance with the invention, there is provided a thermoplastic polyurehane composition whenever prepared according to the above process, optionally containing at least one additional component selected from fillers and stabilisers. A wide variety of fillers can be used in formulations with the present invention. Suitable fillers include calcium carbonate, clays, talcs, zinc oxide, titanium dioxide, silica and the like. The amount of filler usually is n the range of 0 to about 800 phr (per hundred parts by weight of resin, i.e. of (a) + (b) ) , depending on the type of filler used and on the application for which the formulation is intended. Preferred fillers are silica and titanium dioxide. The filler should be thoroughly dried in order that adsorbed moisture will not interfere with the reaction between the polyisocyanate and the saturated, polyhydroxylated polydiene polymer. Stabilizers known in the art may also be incorporated into the composition. These may be for protection during the life of the product against, for example, oxygen, ozone and ultra-violet radiation. These may also be for stabilization against thermo- oxidative degradation during elevated temperature processing. Antioxidants and UV inhibitors which interfere with the urethane curing reaction must be avoided. Preferred antioxidants are the sterically hindered phenolic compounds like butylated hydroxy toluene. Preferred UV inhibitors are UV absorbers such as benzotriazole compounds. The amount of stabilizer in the formulation will depend greatly on the intended application of the product. If processing and durability requirements are modest, the amount of stabilizer in the formulation will be less than about 1 phr. If the polyurethane will be mixed at high temperature or if the product must survive many years in service, stabilizer concentration could be as much as about 10 phr. A particularly preferred embodiment of the present invention provides a composition for making thermoplastic polyurethanes comprising, as initial components, 1 to 80% by weight of a hydrogenated polybutadiene diol having from 1.9 to 2.0 terminal hydroxyl groups per molecule, 1,4-addition in the range from 40% to 60%, and a number average molecular weight in the range from 1,000 to 10,000, and 20 to 99% by weight of a hard segment-providing combination comprising an isocyanate having two isocyanate groups per molecule and dimer diol such that an overall NCO/OH molar ratio of 0.9 to 1.1 exists. A second particularly preferred embodiment of the present invention provides a composition for making thermoplastic polyurethanes comprising from 1 to 80% by weight of a hydrogenated polybutadiene diol having from 1.9 to 2.0 terminal hydroxyl groups per molecule, 1,4- addition in the range from 40% to 60%, and a number average molecular weight in the range from 1000 to 10,000, and 20 to 99% by weight of a hard segment- providing combination comprising an isocyanate having two isocyanate groups per molecule and a mixed chain extender comprising a dimer diol plus one or more diols from the group consisting of 2-ethyl-l, 3-hexane diol, 2, 2, 4-trimethyl-l, 3-pentane diol, 2-ethyl-2-butyl-l, 3- propane diol, 1,4-butane diol, and 1,6-hexane diol, such that an overall NCO/OH molar ratio of 0.9 to 1.1 exists. The invention will be further understood from the following illustrative examples thereof, in which: A linear, hydrogenated butadiene diol polymer having 1.93 terminal hydroxyl groups per molecule, a number average molecular weight (Mn) of 3400, and a 1,2- addition of butadiene of 50%, was obtained from Shell Chemical Company, USA, labeled KLP-L2203. This polymer is a viscous liquid at 25°C but flows readily at slightly elevated temperatures (2.5 Pa . s (2500 centipoise) viscosity at 60°C) . This long chain diol was dried by heating it to 90°C under a nitrogen flow for several hours before reacting it. This was carried out in a 500 milliliter glass reaction kettle. The isocyanate used was 4 , 4 ' -diphenylmethane diisocyanate (MDI) . It was obtained from Aldrich Chemical Co. in flaked form and was stored in a freezer prior to use. The diisocyanate was handled in a nitrogen filled dry box when dispensing it. The dimer diol was obtained from Henkel Corp. and was dried using molecular sieves. The chain extending short chain diols were dried in a vacuum at 50-60°C for 2-3 hours before use . The thermoplastic polyurethanes were synthesized using the prepolymer method. All of the diisocyanate required was added to the dried hot polymer. The reaction between long chain diol and diisocyanate was carried out at 90°C for 90 minutes. During the course of the reaction, the viscous mixture was stirred continuously using a high torque air driven mechanical stirrer. At the end of the prepolymer synthesis, a mass of prepolymer was added to a preheated glass jar. The required amount of hot chain extending diol (dimer diol alone or in combination with another diol) was then added to the prepolymer and stirred using a high speed "Cafcamo" mixer. This was carried out for two to three minutes and then the mixture was poured into a release agent-coated aluminum pan. The polyurethane cure was completed in a vacuum at 90°C for 16 hours. The overall molar ratio of NCO/OH was 1.00 in all cases. Samples for mechanical testing were prepared by melt pressing the thermoplastic polyurethane at 150 to 170°C in a Carver press. Samples having a thickness of 0.03 cm (12 mil) were prepared for dynamic mechanical testing (DMA) and tensile testing. The tensile strength and elongation results were not significantly different when measured on 0.32 cm (1/8 inch) thick samples. The hardness measurements were made on 0.32 cm (1/8 inch) thick samples stacked to a 0.64 cm (1/4 inch) thickness. The results are shown in the accompanying tables. The dynamic mechanical tests were performed using an Imass "Rheovibron" apparatus operated at 11 Hz. The dynamic response of the material was measured from - 100°C to 200°C. The low temperature soft segment T g was indicated by the maximum in the tan decta as the material warmed from the fully vitrified state. The flow temperature was defined as the temperature at which the elastic modulus began its precipitous drop accompanying softening of the hard segment. Tensile properties were measured using an "Instron" tensile tester. An elongation rate of 10 mches/mmute was used. Hardness was measured using a durometer fitted with a Shore A probe. Values were recorded instantly upon probe-sample contact and after a 10 second relaxation Example 1 Thermoplastic polyurethanes were made by the solventless prepolymer method as generally described using pure dimer diol as the chain extender. Polyurethanes containing hard segments of 22, 30, 37.5, 45, 80, and 90% by weight were prepared. The physical properties of the resulting polymers are listed under entries PU1 to PU6 in Table 1. The suitable balance of compatibility achieved in this system allowed incorporation of hard segment contents as high as 90% by weight. The resulting strength ranged from 552 x 10 3 Pa (80 psi) at 22% hard segment to 27 x 10 6 Pa (3911 psi) at 80% hard segment. Instantaneous Shore A hardness ranged from 48 at 22% hard segment to 87 at 90% hard segment . Comparative Example 1 Thermoplastic polyurethanes were made by the prepolymer method as generally described using pure 2-butyl-2-ethyl-l, 3-propane diol as the chain extender. Polyurethanes containing 22, 30, 45, and 80% hard segment by weight were prepared. The physical properties of the resulting polymers are listed under entries PUA to PUD in Table 1. While low hard segment contents exhibited good physical properties, hard segment content above 45% showed poor compatibility and poor properties. The maximum observed strength of 23 x 10 6 Pa (3350 psi) occurs at 30% hard segment. At 45% hard segment the strength decreases to 11.7 x 10 6 Pa (1700 psi) and further decreases to 2.62 x 10 6 Pa (380 psi) at 80% hard segment. Comparative Example 2 Thermoplastic polyurethanes were made by the prepolymer method as generally described using pure butane diol as the chain extender. Polyurethanes containing 20, 25, and 30% hard segment by weight were prepared. The physical properties of the resulting polymers are listed under entries PUE through PUG in Table 1. Only low amounts of hard segment can be incorporated in this system before the poor compatibility limits the extent of reaction and the resulting physical properties. The highest strength (8.14 x 10 6 Pa (1180 psi)) was achieved at 20% hard segment. As the hard segment content was increased to 25% and 30% the strength was reduced to 6.76 x 10 6 Pa (980 psi) and 1.17 x 10 6 Pa (170 psi) respectively. TABLE 1 Physical Properties of Polyurethane Elastomers Having a Single Chain Extending Diol * chain extended with pure butyl-ethyl-propane diol (BEPD) + chain extended with pure butane diol Example 2 Thermoplastic polyurethanes were made by the prepolymer method as generally described using a mixture of dimer diol and 2-butyl-2-ethyl-l, 3-propane diol. Hard segment content ranged from 30 to 45% by weight. The dimer diol made up 50 or 75% by weight of the required mass of chain extender. The compositions and resulting properties of these polyurethanes are listed under entries PU7 to PU 11 in Table 2. The compatibilizmg effect of dimer diol is seen by comparison of the properties of PUll which had 45% hard segment with a 75/25 mixture of dimer diol/BEP diol and PUC of Table 1 which had 45% hard segment with 100% BEP diol. The improved compatibility of this blend of chain extenders results in improved strength and elongation. Example 3 A thermoplastic polyurethane was made by the prepolymer method as generally described using a mixture of dimer diol and butane diol . The hard segment content was 30% by weight. Dimer diol made up 50% by weight of the required mass of chain extender. The resulting physical properties are listed under entry PU12 in Table 2. The compatibility effect of dimer diol is seen by comparing the properties of PU12 and PUG of Table 1 which had 30% hard segment with 100% butane diol. The presence of the dimer diol allowed a further extent of reaction and this resulted in significantly increased flow temperature, strength, and elongation. Example 4 A thermoplastic polyurethane was made as for PU7 in Example 2, except that instead of the previously described butadiene diol polymer there was used a butadiene diol polymer having Mn of 3525 (by 1H NMR) and equivalent weight 2060 g/mol OH, synthesised using sec- butyl lithium and diisopropyl benzene as initiator system. The resulting physical properties are listed under entry PU13 in Table 2, and these are seen to be broadly similar to those of PU7. TABLE 2 Physical Properties of Polyurethane Elastomers Having a Mixed Chain Extending Diol * remainder BEP diol + remainder butane diol

Claims: C L A I M S 1. A composition for making thermoplastic polyurethanes, comprising as initial components: (a) from 1 to 80% by weight of a polydiene diol having from 1.6 to 2 terminal hydroxyl groups per molecule and a number average molecular weight in the range from 500 to 20,000; (b) from 20 to 99% by weight of a hard segment- providing combination comprising an isocyanate having two isocyanate groups per molecule and, as a chain extender, a dimer diol. 2. A composition according to claim 1 wherein the polydiene diol has from 1.9 to 2 hydroxyl groups per molecule . 3. A composition according to claim 1 or 2 wheiein the polydiene diol has a number average molecular weight n the range from 1,000 to 10,000. 4. A composition according to claim 1, 2 or 3 wherein the polydiene diol is a hydrogenated polybutadiene diol or a hydrogenated polyisoprene diol. 5. A composition according to anyone of Claims 1 to 4 wherein the hard segment-providing combination also contains an additional chain extender selected from the group consisting of butane diol, propane diol, butyl- ethyl-propane diol, tπmethyl pentane diol, and hexane diol. 6. A composition according to any one of Claims 1 to 5 wherein the overall NCO to OH molar ratio ranges from 0.9 to 1.1. 7. A composition according to any one of Claims 1 to 6 wherein the isocyanate is selected from the group 4 , 4 ' -diphenylmethane diisocyanate, toluene diisocyanate, isophorone diisocyanate, hexamethylene diisocyanate, ethylene diisocyanate, and paraphenyl diisocyanate. 8. A composition according to any one of Claims 1 to 7 wherein the dimer diol contains 36 carbon atoms. 9. A process for preparing a thermoplastic polyurethane composition which comprises reacting together the components of a composition according to anyone of Claims 1 to 8, the dimer diol, and additional chain extender, when used, being reacted during or after reaction between the polyene diol and the isocyanate. 10. A thermoplastic polyurethane composition whenever prepared according to Claim 9 optionally containing at least one additional component selected from fillers and stabilisers.

Inventors: HANDLIN DALE LEE JR, MASSE MICHAEL ALAN, HANDLIN, DALE, LEE, JR., MASSE, MICHAEL, ALAN
Applicants: SHELL INT RESEARCH, SHELL INTERNATIONALE RESEARCH MAATSCHAPPIJ B.V.
Application year: 1997
Main classification: G08G18
IPC codes: C08G18