FILLED POLYMER COMPOSITIONS

Abstract: A filled polymer composition which comprises (A) from 5 to 90 percent of one or more thermoplastic substantially random interpolymers prepared by polymerizing one or more alpha -olefin monomers with one or more vinylidene aromatic monomers and/or one or more hindered aliphatic or cycloaliphatic vinylidene monomers, and optionally with other polymerizable ethylenically unsaturated monomer(s), and (B) from 10 to 95 percent of one or more inorganic fillers, the amounts of (A) and (B) being based on the total weight of (A) and (B). Fabricated articles made from the filled polymer compositions are useful as sound insulating or energy absorbing films or sheets or as floor, wall or ceiling coverings.

Description: FILLED POLYMER COMPOSITIONS This invention relates to filled α-olefin/vinylidene monomer interpolymer compositions, and fabricated articles thereof. Fillers are frequently used to improve the stiffness of polymer compositions, or to decrease the coefficient of linear thermal expansion, or to decrease the overall cost of the polymer composition. However, such fillers are well known to simultaneously decrease impact performance or toughness of the resultant composition. For example, Joseph A. Randosta & Nikhil C. Trivedi in Talc [published in Handbook of Fillers and Reinforcements for Plastics 160 (Harry S. Katz & John V. Milewski eds.)] confirm that the impact performance of polymeric materials is generally decreased by the presence of rigid fillers, especially below the glass transition temperature (Tg) of the matrix material, due to the fillers' action as "stress concentrators". Typically, the filler is incorporated at levels ranging from 1 to 50 weight percent of the formulation, depending upon the filler density. At relatively high levels of filler loading (for example, greater than about 20 percent), typical thermoplastic formulations (for example, polypropylene, an elastomeric rubber and talc) have very poor impact performance and do not function well in uses such as automotive facia. Low temperature impact resistance generally becomes more critical when the formulation is exposed to temperatures approaching the glass transition temperature of the rubber used in the formulation. Sometimes the room temperature impact resistance may even increase for highly filled formulations, but the low temperature impact resistance decreases rapidly with decreasing temperature. The patent application WO 95/09945 discloses a thermoset elastomer composition which comprises a cross-linked substantially random interpolymer of (a) 15 to 70 weight percent of an α-olefin, (b) 30 to 70 weight percent of a vinylidene aromatic compound and (c) 0 to 15 weight percent of a diene. The linked substantially random interpolymer is typically mixed with a filler, an oil, and a curing agent at an elevated temperature to compound them. The amount of the curing agent is typically from 0.5 to 12 weight percent, based on the total weight of the formulation. Carbon black may be added in an amount of up to 50 weight percent, based on the total weight of the formulation, to mask the color, to increase the toughness and/or to decrease the cost of the formulation. The disclosed thermoset formulations are useful in hoses, air ducts, brake cups, roofing materials and as various automotive parts, such as tires and moldings. However, the post-extrusion curing results in a cross-linked thermoset part that can not be reprocessed as a thermoplastic. This limits recyclability of the product. U.S. Patent No. 5,576,374 discloses filled thermoplastic olefinic compositions which have good low temperature impact performance and modulus. They comprise (A) a thermoplastic resin selected from thermoplastic polyurethanes, polyvinyl chlorides, styrenics, engineering thermoplastics, and polyolefins, (B) at least one substantially linear ethylene / α-olefin polymer which is characterized as having: a) a melt flow ratio, l 10 /l 2 , > 5.63, b) a molecular weight distribution, M M n , defined by the equation: M M n < (Vy - 4.63, and c) a critical shear rate at onset of surface melt fracture of at least 50 percent greater than the critical shear rate at the onset of surface melt fracture of a linear ethylene / α-olefin polymer having about the same l 2 and M M n , and (C) at least one filler. The filled thermoplastic olefinic compositions are said to be useful as automotive bumpers, facia, wheel covers and grilles and freezer containers. In view of the wide ranges of desirable properties and uses for thermoplastic polymers, it would be desirable to provide new filled polymer compositions. In one aspect, the present invention relates to a filled polymer composition which comprises: (A) from 5 to 90 percent of one or more thermoplastic substantially random interpolymers prepared by polymerizing one or more α-olefin monomers with one or more vinylidene aromatic monomers and/or one or more hindered aliphatic or cycloaliphatic vinylidene monomers, and optionally with other polymerizable ethylenically unsaturated monomer(s), and (B) from 10 to 95 percent of one or more inorganic fillers, the amounts of (A) and (B) being based on the total weight of (A) and (B). In another aspect, the present invention relates to a fabricated article made from such filled polymer composition. In yet another aspect, the present invention relates to a multilayered structure wherein at least one layer is made from such filled polymer composition. It has been surprisingly found that thermoplastic substantially random interpolymers which have been prepared by polymerizing one or more α-olefin monomers with one or more vinylidene aromatic monomers and/or one or more hindered aliphatic or cycloaliphatic vinylidene monomers, and optionally with other polymerizable ethylenically unsaturated monomer(s) can be blended with high levels of one or more inorganic fillers and that fabricated articles made from filled polymer compositions comprising one or more of such thermoplastic interpolymers and one or more inorganic fillers in the above-mentioned weight ratios have a substantially improved hardness and tensile modulus while generally maintaining good elongation properties, such as strain at break, stress at break and energy at break, as compared to fabricated articles made from a corresponding thermoplastic interpolymer without inclusion of a filler. It has also been surprisingly found that fabricated articles made from filled polymer compositions which comprise one or more of such thermoplastic interpolymers and one or more inorganic fillers in the above-mentioned weight ratios often have a better scratch resistance than filled thermoplastic olefinic compositions disclosed in U.S. patent No. 5,576,374. The term "interpolymer" is used herein to indicate a polymer wherein at least two different monomers are polymerized to make the interpolymer. The term "substantially random" in the substantially random interpolymer resulting from polymerizing one or more a-olefin monomers and one or more vinylidene aromatic monomers or hindered aliphatic or cycloaliphatic vinylidene monomers, and optionally, with other polymerizable ethylenically unsaturated monomer(s) as used herein preferably means that the distribution of the monomers of said interpolymer can be described by the Bernoulli statistical model or by a first or second order Markovian statistical model, as described by J. C. Randall in POLYMER SEQUENCE DETERMINATION. Carbon- 13 NMR Method. Academic Press New York, 1977, pp. 71 -78. Preferably, the substantially random interpolymer resulting from polymerizing one or more a-olefin monomers and one or more vinylidene aromatic monomer, and optionally, with other polymerizable ethylenically unsaturated monomer(s) does not contain more than 15 percent of the total amount of vinylidene aromatic monomer in blocks of vinylidene aromatic monomer of more than 3 units. More preferably, the interpolymer was not characterized by a high degree of either isotacticity or syndiotacticity. This means that in the carbon " ' 3 NMR spectrum of the substantially random interpolymer the peak areas corresponding to the main chain methylene and methine carbons representing either meso diad sequences or racemic diad sequences should not exceed 75 percent of the total peak area of the main chain methylene and methine carbons. The above-mentioned interpolymer(s) suitable in the filled polymer composition of the present invention are thermoplastic, that means they may be molded or otherwise shaped and reprocessed at temperatures above their melting or softening point. They are not cross-linked to a substantial degree, which means that the filled polymer compositions of the present invention do not contain more than 0.4 percent, preferably not more than 0.2 percent, more preferably not more than 0.05 percent of a cross-linking agent, based on the weight of the interpolymer(s). Most preferably, the filled polymer compositions of the present invention do not contain any measurable amount of a cross-linking agent. The interpolymers employed in the present invention include, but are not limited to substantially random interpolymers prepared by polymerizing one or more α-olefin monomers with one or more vinylidene aromatic monomers and/or one or more hindered aliphatic or cycloaliphatic vinylidene monomers, and optionally with other polymerizable ethylenically unsaturated monomer(s). Suitable α-olefin monomers include, for example, α-olefin monomers containing from 2 to 20, preferably from 2 to 12, more preferably from 2 to 8 carbon atoms. Preferred such monomers include ethylene, propylene, butene-1 , 4-methyl-1 -pentene, hexene-1 and octene-1. Most preferred are ethylene or a combination of ethylene with C M - α-olefins. These α-olefins do not contain an aromatic moiety. Suitable vinylidene aromatic monomers which can be employed to prepare the interpolymers employed in the filled polymer compositions of the present invention include, for example, those represented by the following Formula I Ar I (CH 2 ) n R 1 — C = C(R2) (Formula I) wherein R 1 is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; each R 2 is independently selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; Ar is a phenyl group or a phenyl group substituted with from 1 to 5 substituents selected from halo, C, .4 -alkyl, and C,. 4 -haloalkyl; and n has a value from zero to 4, preferably from zero to 2, most preferably zero. Particularly suitable such monomers include styrene and lower alkyl- or halogen-substituted derivatives thereof. Exemplary monovinylidene aromatic monomers include styrene, vinyl toluene, α-methylstyrene, t-butyl styrene or chlorostyrene, including all isomers of these compounds. Preferred monomers include styrene, a-methyl styrene, the lower alkyl- (C, - C 4 ) or phenyl-ring substituted derivatives of styrene, such as for example, ortho-, meta-, and para-methylstyrene, the ring halogenated styrenes, para-vinyl toluene or mixtures thereof. A more preferred aromatic monovinylidene monomer is styrene. By the term "hindered aliphatic or cycloaliphatic vinylidene monomers", it is meant addition polymerizable vinylidene monomers corresponding to the formula: A' I Rl — c = C(R2) 2 wherein A 1 is a sterically bulky, aliphatic or cycloaliphatic substituent of up to 20 carbons, R 1 is selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; each R 2 is independently selected from the group of radicals consisting of hydrogen and alkyl radicals containing from 1 to 4 carbon atoms, preferably hydrogen or methyl; or alternatively R and A 1 together form a ring system. By the term "sterically bulky" is meant that the monomer bearing this substituent is normally incapable of addition polymerization by standard Ziegler- Natta polymerization catalysts at a rate comparable with ethylene polymerizations, α-olefin monomers containing from 2 to 20 carbon atoms and having a linear aliphatic structure such as propylene, butene-1 , hexene-1 and octene-1 are not considered as hindered aliphatic monomers. Preferred hindered aliphatic or cycloaliphatic vinylidene compounds are monomers in which one of the carbon atoms bearing ethylenic unsaturation is tertiary or quaternary substituted. Examples of such substituents include cyclic aliphatic groups such as cyclohexyl, cyclohexenyl, cyclooctenyl, or ring alkyl or aryl substituted derivatives thereof, tert-butyl or norbornyi. Most preferred hindered aliphatic or cycloaliphatic vinylidene compounds are the various isomeric vinyl-ring substituted derivatives of cyclohexene and substituted cyclohexenes, and 5-ethylidene-2-norbomene. Especially suitable are 1-, 3-, and 4-vinylcyclohexene. The interpolymers of one or more α-olefins and one or more monovinylidene aromatic monomers and/or one or more hindered aliphatic or cycloaliphatic vinylidene monomers employed in the present invention are substantially random polymers. These interpolymers usually contain from 0.5 to 65, preferably from 1 to 55, more preferably from 2 to 50, most preferably from 20 to 50 mole percent of at least one vinylidene aromatic monomer and/or hindered aliphatic or cycloaliphatic vinylidene monomer and from 35 to 99.5, preferably from 45 to 99, more preferably from 50 to 98, most preferably from 50 to 80 mole percent of at least one aliphatic α-olefin having from 2 to 20 carbon atoms. Other optional polymerizable ethylenically unsaturated monomer(s) include strained ring olefins such as norbornene and C, .10 alkyl or C._ 10 aryl substituted norbornenes, with an exemplary interpolymer being ethylene/styrene/norbornene. The number average molecular weight (Mn) of the interpolymers is usually greater than 5,000, preferably from 20,000 to 1 ,000,000, more preferably from 50,000 to 500,000. The melt index l 2 according to ASTM D 1238 Procedure A, condition E, generally is from 0.01 to 50 g/10 min., preferably from 0.01 to 20 g/10 min., more preferably from 0.1 to 10 g/10 min., and most preferably from 0.5 to 5 g/10 min. The glass transition temperature (T g ) of the interpolymers is preferably from -40°C to +35°C, preferably from 0°C to +30°C, most preferably from +10°C to +25°C, measured according to differential mechanical scanning (DMS). Polymerizations and unreacted monomer removal at temperatures above the autopolymerization temperature of the respective monomers may result in formation of some amounts of homopolymer polymerization products resulting from free radical polymerization. For example, while preparing the substantially random interpolymer, an amount of atactic vinylidene aromatic homopolymer may be formed due to homopolymerization of the vinylidene aromatic monomer at elevated temperatures. The presence of vinylidene aromatic homopolymer is in general not detrimental for the purposes of the present invention and can be tolerated. The vinylidene aromatic homopolymer may be separated from the interpolymer, if desired, by extraction techniques such as selective precipitation from solution with a non solvent for either the interpolymer or the vinylidene aromatic homopolymer. For the purpose of the present invention it is preferred that no more than 20 weight percent, preferably less than 15 weight percent based on the total weight of the interpolymers of vinylidene aromatic homopolymer is present. The substantially random interpolymers may be modified by typical grafting, hydrogenation, functionalizing, or other reactions well known to those skilled in the art. The polymers may be readily sulfonated or chlorinated to provide functionalized derivatives according to established techniques. The substantially random interpolymers can be prepared as described in US Application number 07/545,403 filed July 3, 1990 (corresponding to EP-A-0,416,815) by James C. Stevens et al. and in allowed U.S. Application Number 08/469,828, filed June 6, 1995, issued as U.S. Patent No. 5,703,187. Preferred operating conditions for such polymerization reactions are pressures from atmospheric up to 3,000 atmospheres and temperatures from -30°C to 200°C. Examples of suitable catalysts and methods for preparing the substantially random interpolymers are disclosed in U.S. Application No. 07/545,403, filed July 3, 1990 (corresponding to EP-A-416,815); U.S. Application Serial No. 547,718, filed July 3, 1990 (corresponding to EP-A-468,651 ); U.S. Application No. 07/702,475, filed May 20, 1991 (corresponding to EP-A-514,828); U.S. Application No. 07/876,268, filed May 1 , 1992 (corresponding to EP-A-520,732); U.S. Application Serial No. 884,966, filed May 15, 1992 (corresponding to WO 93/23412); U.S. Patent No. 5,374,696, filed January 21 , 1993; U.S. Application Serial No. 34,434, filed March 19, 1993 (corresponding to WO 94/01647); U.S. Application No. 08/241 ,523, filed May 12, 1994, (corresponding to WO 94/06834 and EP 0,705,269); as well as U.S. Patents 5,055,438; 5,057,475; 5,096,867; 5,064,802; 5,132,380; 5,189,192; 5,321 ,106; 5,347,024; 5,350,723; 5,374,696; 5,399,635; 5,460,993 and 5,556,928. The substantially random α-olefin/vinylidene aromatic interpolymers can also be prepared by the methods described by John G. Bradfute et al. (W.R. Grace & Co.) in WO 95/32095; by R.B. Pannell (Exxon Chemical Patents, Inc.) in WO 94/00500; and in Plastics Technology, page 25 (September 1992). Also suitable are the substantially random interpolymers which comprise at least one α-olefin/vinyl aromatic/vinyl aromatic/α-olefin tetrad. These interpolymers contain additional signals with intensities greater than three times the peak to peak noise. These signals appear in the chemical shift range 43.75 to 44.25 ppm and 38.0 to 38.5 ppm. Specifically, major peaks are observed at 44.1 , 43.9 and 38.2 ppm. A proton test NMR experiment indicates that the signals in the chemical shift region 43.75 to 44.25 ppm are methine carbons and the signals in the region 38.0 to 38.5 ppm are methylene carbons. In order to determine the carbon- 13 NMR chemical shifts of the interpolymers described, the following procedures and conditions are employed. A five to ten weight percent polymer solution is prepared in a mixture consisting of 50 volume percent 1 ,1 ,2,2- tetrachloroethane-d 2 and 50 volume percent 0.10 molar chromium tris(acetylacetonate) in 1 ,2,4-trichlorobenzene. NMR spectra are acquired at 130°C using an inverse gated decoupling sequence, a 90 degree pulse width and a pulse delay of five seconds or more. The spectra are referenced to the isolated methylene signal of the polymer assigned at 30.000 ppm. It is believed that these new signals are due to sequences involving two head- to-tail vinyl aromatic monomer preceded and followed by at least one α-olefin insertion, for example, an ethylene/styrene/styrene/ethylene tetrad wherein the styrene monomer insertions of said tetrads occur exclusively in a 1 ,2 (head-to-tail) manner. It is understood by one skilled in the art that for such tetrads involving a vinyl aromatic monomer other than styrene and an α-olefin other than ethylene, that the ethylene/vinyl aromatic monomer/vinyl aromatic monomer/ethylene tetrad will give rise to similar carbon- 13 NMR peaks but with slightly different chemical shifts. These interpolymers are prepared by conducting the polymerization at temperatures of from -30°C to 250°C in the presence of such catalysts as those represented by the formula / \ (my„ MR' 2 \ < P wherein each Cp is independently, each occurrence, a substituted cyclopentadienyl group π-bound to M; E is C or Si; M is a group IV metal, preferably Zr or Hf, most preferably Zr; each R is independently, each occurrence, H, hydrocarbyl, silahydrocarbyl, or hydrocarbylsilyl, containing up to 30 preferably from 1 to 20 more preferably from 1 to 10 carbon or silicon atoms; each R' is independently, each occurrence, H, halo, hydrocarbyl, hyrocarbyloxy, silahydrocarbyl, hydrocarbylsilyl containing up to 30, preferably from 1 to 20, more preferably from 1 to 10 carbon or silicon atoms, or two R' groups together can be a C 0 hydrocarbyl substituted 1 ,3-butadiene; m is 1 or 2; and optionally, but preferably in the presence of an activating cocatalyst, such as tris(pentafluorophenyi) borane or methylalumoxane (MAO). Particularly suitable substituted cyclopentadienyl groups include those illustrated by the formula: (R)3 wherein each R is independently, each occurrence, H, hydrocarbyl, silahydrocarbyl, or hydrocarbylsilyl, containing up to 30 preferably from 1 to 20 more preferably from 1 to 10 carbon or silicon atoms, or two R groups together form a divalent derivative of such group. Preferably, R independently each occurrence is (including where appropriate ail isomers) hydrogen, methyl, ethyl, propyi, butyl, pentyl, hexyl, benzyl, phenyl or silyl or (where appropriate) two such R groups are linked together forming a fused ring system such as indenyl, fluorenyl, tetrahydroindenyl, tetrahydrofluorenyi, or octahydrofluorenyl. Particularly preferred catalysts include, for example, racemic- (dimethylsilanediyl(2-methyl-4-phenylindenyl))zirconium dichloride, racemic- (dimethylsilanediyl(2-methyl-4-phenylindenyl))zirconium 1 ,4-diphenyl-1 ,3-butadiene, racemic-(dimethylsilanediyl(2-methyl-4-phenylindenyl))zirconium di-C1-4 alkyl, racemic- (dimethylsilanediyl(2-methyl-4-phenylindenyl))zirconium di-C1-4 alkoxide, or any combination thereof. Additional preparative methods for the interpolymer component (A) of the present invention have been described in the literature. Longo and Grassi (Makromol. Chem., Volume 191 , pages 2387 to 2396 [1990]) and D'Anniello et al. (Journal of Applied Polymer Science, Volume 58, pages 1701 to 1706 [1995]) reported the use of a catalytic system based on methylalumoxane (MAO) and cyclopentadienyltitanium trichloride (CpTiCI 3 ) to prepare an ethylene-styrene copolymer. Xu and Lin (Polymer Preprints, Am. Chem. Soc, Div. Polym. Chem., volume 35, pages 686, 687 [1994]) have reported copolymerization using an MgCIJTiCI 4 /NdCIJAI(iBu) 3 catalyst to give random copolymers of styrene and propylene. Lu et al. (Journal of Applied Polymer Science, volume 53, pages 1453 to 1460 [1994]) have described the copolymerization of ethylene and styrene using a TiCI 4 /NdCIJ MgCI 2 /AI(Et) 3 catalyst. Sernetz and Mulhaupt, (Macromol. Chem. Phys., volume 197, pages 1071 to 1083 [1997]) have described the influence of polymerization conditions on the copolymerization of styrene with ethylene using Me 2 Si(Me 4 Cp)(N-tert- butyl)TiCIJmethylaluminoxane Ziegler-Natta catalysts. The manufacture of α-olef in/vinyl aromatic monomer interpolymers such as propylene/styrene and butene/styrene are described in U. S. Patent No. 5,244,996. The filled polymer composition of the present invention comprises (A) from 5 to 90 percent, of one or more of the above-described thermoplastic interpolymers, and (B) from 10 to 95 percent of one or more inorganic fillers, with the amounts of (A) and (B) being based on the total weight of (A) and (B). The preferred amounts of inorganic filler depend on the desired end-use of the filled polymer compositions of the present invention. For example, when producing floor, wail or ceiling tiles, the amount of the inorganic filler(s) (B) preferably is from 50 to 95 percent, more preferably from 70 to 90 percent, based on the total weight of (A) and (B). On the other hand, when producing floor, wall or ceiling sheetings, the amount of the inorganic filler(s) (B) preferably is from 10 to 70 percent, more preferably from 15 to 50 percent, based on the total weight of (A) and (B). For several applications filler contents of from 40 to 90 percent, more preferably from 55 to 85 percent, based on the total weight of (A) and (B), are preferred. Preferred inorganic fillers are ionic inorganic materials. Preferred examples of inorganic fillers are talc, calcium carbonate, alumina trihydrate, glass fibers, marble dust, cement dust, clay, feldspar, silica or glass, fumed silica, alumina, magnesium oxide, magnesium hydroxide, antimony oxide, zinc oxide, barium sulfate, aluminum silicate, calcium silicate, titanium dioxide, titanates, glass microspheres or chalk. Of these fillers, barium sulfate, talc, calcium carbonate, silica/glass, glass fibers, alumina, alumina trihyrate and titanium dioxide, and mixtures thereof are preferred. The most preferred inorganic fillers are talc, calcium carbonate, barium sulfate, glass fibers or mixtures thereof. It has been surprisingly found that the α-olefin/vinylidene aromatic interpolymers display a high compatibility with inorganic fillers. The composition of the present invention may contain a coupling agent, such as maleic anhydride grafted polyethylene or maleic anhydride grafted polypropylene or a known silane/silicone coupling agent. However, the presence of a coupling agent is not required, even if the filler content is 55 weight percent or more. Even in the absence of a coupling agent fabricated articles of the present invention still exhibit good filler holding and good solid state properties. This is unexpected, since many of the above-mentioned α-olefin/vinylidene aromatic interpolymers are largely unfunctionalized. The filled polymer composition of the present invention may optionally contain up to 50 weight percent, preferably up to 30 weight percent, more preferably up to 20 weight percent, most preferably up to 10 weight percent, of one or more additional polymeric components, such as those described below. However, the total amount of the α- olefin/vinylidene aromatic interpolymer(s) (A) and the inorganic filler(s) (B) generally is at least 50 percent, preferably at least 70 percent, more preferably at least 80 percent and most preferably at least 90 percent, based on the total weight of the filled polymer composition of the present invention. Preferred additional, optional polymers are monovinylidene aromatic polymers or styrenic block copolymers. The most preferred additional, optional polymers are homopolymers or interpolymers of aliphatic α-oiefins having from 2 to 20 carbon atoms or α- olefins having from 2 to 20 carbon atoms and containing polar groups. Suitable monovinylidene aromatic polymers include homopolymers or interpolymers of one or more monovinylidene aromatic monomers, or interpolymers of one or more monovinylidene aromatic monomers and one or more monomers interpolymerizable therewith other than an aliphatic α-olefin. Suitable monovinylidene aromatic monomers are represented by the following formula: Ar I R 1 — C = CH wherein R 1 and Ar have the meanings stated in Formula I above. Exemplary monovinylidene aromatic monomers are those listed under Formula I further above, particularly styrene. Examples of suitable interpolymerizable comonomers other than a monovinylidene aromatic monomer include, for example, C 4 -C 6 conjugated dienes, especially butadiene or isoprene; ethylenically unsaturated nitriles such as acrylonitrile, methacrylonitrile, or ethacrylonitrile, ethylenically unsaturated anhydrides such as maleic anhydride; ethylenically unsaturated amides such as acrylamide, or methacrylamide; ethylenically unsaturated carboxylic acids (both mono- and difunctional) such as acrylic acid and methacrylic acid; esters (especially lower, for example, C,-C 6 , alkyl esters) of ethylenically unsaturated carboxylic acids such as methyl methacrylate, ethyl acrylate, hydroxyethylacrylate, n-butyl acrylate or methacrylate, 2-ethyl-hexylacrylate etc.; ethylenically unsaturated dicarboxylic acid imides such as N-alkyl or N-aryl maleimides such as N-phenyl maleimide. Preferred monomers include maleic anhydride, methyl methacrylate, N-phenyl maleimide and acrylonitrile. In some cases it is also desirable to copolymerize a cross-linking monomer such as a divinyl benzene into the monovinylidene aromatic polymer. The polymers of monovinylidene aromatic monomers with other interpolymerizable comonomers preferably contain, polymerized therein, at least 50 percent by weight and, preferably, at least 90 percent by weight of one or more monovinylidene aromatic monomers. Styrenic block polymers are also useful as an additional, optional polymer in the filled polymer composition of the present invention. The term "block copolymer" is used herein to mean elastomers having at least one block segment of a hard polymer unit and at least one block segment of a rubber monomer unit. However, the term is not intended to include thermoeiastic ethylene interpolymers which are, in general, random polymers. Preferred block copolymers contain hard segments of styrenic type polymers in combination with saturated or unsaturated rubber monomer segments. The structure of the block copolymers useful in the present invention is not critical and can be of the linear or radial type, either diblock or triblock, or any combination of thereof. Suitable unsaturated block copolymers include those represented by the following formulas: A-B-R(-B-A) n or A x -(BA-) y -BA wherein each A is a polymer block comprising a monovinylidene aromatic monomer, preferably styrene, and each B is a polymer block comprising a conjugated diene, preferably isoprene or butadiene, and optionally a monovinylidene aromatic monomer, preferably styrene; R is the remnant of a multifunctional coupling agent; n is an integer from 1 to 5; x is zero or 1 ; and y is a number from zero to 4. Methods for the preparation of such block copolymers are known in the art. Suitable catalysts for the preparation of useful block copolymers with unsaturated rubber monomer units include lithium based catalysts and especially lithium-aikyls. U.S. Patent No. 3,595,942 describes suitable methods for hydrogenation of block copolymers with unsaturated rubber monomer units to form block copolymers with saturated rubber monomer units. The structure of the polymers is determined by their methods of polymerization. For example, linear polymers result by sequential introduction of the desired rubber monomer into the reaction vessel when using such initiators as lithium-alkyis or dilithiostilbene, or by coupling a two segment block copolymer with a difunctional coupling agent. Branched structures, on the other hand, may be obtained by the use of suitable coupling agents having a functionality with respect to the block copolymers with unsaturated rubber monomer units of three or more. Coupling may be effected with multifunctional coupling agents such as dihaloalkanes or alkenes and divinyl benzene as well as with certain polar compounds such as silicon halides, siloxanes or esters of monohydric alcohols with carboxylic acids. The presence of any coupling residues in the polymer may be ignored for an adequate description of the block copolymers forming a part of the composition of this invention. Suitable block copolymers having unsaturated rubber monomer units includes, but is not limited to, styrene-butadiene (SB), styrene-isoprene(SI), styrene- butadiene-styrene (SBS), styrene-isoprene-styrene (SIS), α-methylstyrene-butadiene-α- methylstyrene and α-methylstyrene-isoprene-α-methylstyrene. The styrenic portion of the block copolymer is preferably a polymer or interpolymer of styrene and its analogs and homologs including α-methylstyrene and ring- substituted styrenes, particularly ring-methylated styrenes. The preferred styrenics are styrene and α-methylstyrene, and styrene is particularly preferred. Block copolymers with unsaturated rubber monomer units may comprise homopolymers of butadiene or isoprene or they may comprise copolymers of one or both of these two dienes with a minor amount of styrenic monomer. Preferred block copolymers with saturated rubber monomer units comprise at least one segment of a styrenic unit and at least one segment of an ethylene-butene or ethylene-propylene copolymer. Preferred examples of such block copolymers with saturated rubber monomer units include styrene/ethylene-butene copolymers, styrene/ethylene- propylene copolymers, styrene/ethylene-butene/styrene (SEBS) copolymers, styrene/ethylene-propylene/styrene (SEPS) copolymers. Hydrogenation of block copolymers with unsaturated rubber monomer units is preferably effected by use of a catalyst comprising the reaction products of an aluminum alkyl compound with nickel or cobalt carboxylates or alkoxides under such conditions as to substantially completely hydrogenate at least 80 percent of the aliphatic double bonds while hydrogenating no more than 25 percent of the styrenic aromatic double bonds. Preferred block copolymers are those where at least 99 percent of the aliphatic double bonds are hydrogenated while less than 5 percent of the aromatic double bonds are hydrogenated. The proportion of the styrenic blocks is generally between 8 and 65 percent by weight of the total weight of the block copolymer. Preferably, the block copolymers contain from 10 to 35 weight percent of styrenic block segments and from 90 to 65 weight percent of rubber monomer block segments, based on the total weight of the block copolymer. The average molecular weights of the individual blocks may vary within certain limits. In most instances, the styrenic block segments will have number average molecular weights in the range of 5,000 to 125,000, preferably from 7,000 to 60,000 while the rubber monomer block segments will have average molecular weights in the range of 10,000 to 300,000, preferably from 30,000 to 150,000. The total average molecular weight of the block copolymer is typically in the range of 25,000 to 250,000, preferably from 35,000 to 200,000. Further, the various block copolymers suitable for use in the present invention may be modified by graft incorporation of minor amounts of functional groups, such as, for example, maleic anhydride by any of the methods well known in the art. Block copolymers useful in the present invention are commercially available, such as, for example, supplied by Shell Chemical Company under the designation of KRATON™ and supplied by Dexco Polymers under the designation of VECTOR™. Preferred additional, optional polymers are homopolymers or interpolymers of aliphatic α-olefins having from 2 to 20, preferably 2 to 18, more preferably 2 to 12, carbon atoms or α-olefins having from 2 to 20, preferably 2 to 18, more preferably 2 to 12, carbon atoms and containing polar groups. Suitable aliphatic α-olefin monomers which introduce polar groups into the polymer include, for example, ethylenically unsaturated nitriles such as acrylonitrile, methacrylonitrile, and ethacrylonitrile; ethylenically unsaturated anhydrides such as maleic anhydride; ethylenically unsaturated amides such as acrylamide, or methacryiamide; ethylenically unsaturated carboxylic acids (both mono- and difunctional) such as acrylic acid and methacrylic acid; esters (especially lower, for example, C,-C 6 , alkyl esters) of ethylenically unsaturated carboxylic acids such as methyl methacrylate, ethyl acrylate, hydroxyethylacrylate, n-butyl acrylate or methacrylate, 2-ethyl-hexylacrylate; ethylenically unsaturated dicarboxyiic acid imides such as N-alkyl or N-aryl maleimides such as N-phenyl maleimide. Preferably such monomers containing polar groups are acrylic acid, vinyl acetate, maleic anhydride and acrylonitrile. Halogen groups which can be included in the polymers from aliphatic α-olefin monomers include fluorine, chlorine and bromine; preferably such polymers are chlorinated polyethylenes (CPEs) or poiyvinyl chloride. Preferred olefinic polymers for use in the present invention are homopolymers or interpolymers of an aliphatic, including cycloaliphatic, α-olefin having from 2 to 18 carbon atoms. Suitable examples are homopolymers of ethylene or propylene, and interpolymers of two or more α-olefin monomers. Other preferred olefinic polymers are interpolymers of ethylene and one or more other α-olefins having from 3 to 8 carbon atoms. Preferred comonomers include 1-butene, 4-methyl-1-pentene, 1-hexene, and 1-octene. The olefinic polymer may also contain, in addition to the a-olefin, one or more non-aromatic monomers interpolymerizable therewith. Such additional interpolymerizable monomers include, for example, C 4 -C 20 dienes, preferably, butadiene or 5 ethylidene-2-norbomene. The olefinic polymers can be further characterized by their degree of long or short-chain branching and the distribution thereof. One class of olefinic polymers is generally produced by a high pressure polymerization process using a free radical initiator resulting in the traditional long-chain branched low density polyethylene (LDPE). LDPE employed in the present composition usually has a density of less than 0.94 g/cc (ASTM D 792) and a melt index of from 0.01 to 100, and preferably from 0.1 to 50 grams per 10 minutes (as determined by ASTM Test Method D 1238, condition I). Another class is the linear olefin polymers which have an absence of long- chain branching, as the traditional linear low density polyethylene polymers (heterogeneous LLDPE) or linear high density polyethylene polymers (HDPE) made using Ziegler polymerization processes (for example, U.S. Patent No. 4,076,698), sometimes called heterogeneous polymers. HDPE consists mainly of long linear polyethylene chains. The HDPE employed in the present composition usually has a density of at least 0.94 grams per cubic centimeter (g/cc) as determined by ASTM Test Method D 1505, and a melt index (ASTM- 1238, condition I) in the range of from 0.01 to 100, and preferably from 0.1 to 50 grams per 10 minutes. The heterogeneous LLDPE employed in the present composition generally has a density of from 0.85 to 0.94 g/cc (ASTM D 792), and a melt index (ASTM-1238, condition I) in the range of from 0.01 to 100, and preferably from 0.1 to 50 grams per 10 minutes. Preferably the LLDPE is an interpolymer of ethylene and one or more other α- olefins having from 3 to 18 carbon atoms, more preferably from 3 to 8 carbon atoms. Preferred comonomers include 1-butene, 4-methyl-1-pentene, 1-hexene, and 1-octene. Another class is that of the uniformly branched or homogeneous polymers (homogeneous LLDPE). The homogeneous polymers contain no long-chain branches and have only branches derived from the monomers (if having more than two carbon atoms). Homogeneous polymers include those made as described in U.S. Patent 3,645,992 (Elston), and those made using single-site catalysts in a reactor having relatively high olefin concentrations, as described in U.S. Patent Nos. 5,026,798 and 5,055,438 (Canich). The uniformly branched/homogeneous polymers are those polymers in which the comonomer is randomly distributed within a given interpolymer molecule and wherein the interpolymer molecules have a similar ethylene/comonomer ratio within that interpolymer. The homogeneous LLDPE employed in the present composition generally has a density of from 0.85 to 0.94 g/cc (ASTM D 792), and a melt index (ASTM-1238, condition I) in the range of from 0.01 to 100, and preferably from 0.1 to 50 grams per 10 minutes. Preferably the LLDPE is an interpolymer of ethylene and one or more other α-olefins having from 3 to 18 carbon atoms, more preferably from 3-8 carbon atoms. Preferred comonomers include 1 -butene, 4-methyl-1-pentene, 1-hexene, and 1-octene. Further, there is the class of substantially linear olefin polymers (SLOP) that may advantageously be used in component (B) of the blends of the present invention. These polymers have a processability similar to LDPE, but the strength and toughness of LLDPE. Similar to the traditional homogeneous polymers, the substantially linear ethylene/α-olefin interpolymers have only a single melting peak, as opposed to traditional Ziegler polymerized heterogeneous linear ethylene/α-olefin interpolymers which have two or more melting peaks (determined using differential scanning calorimetry). Substantially linear olefin polymers are disclosed in U.S. Patent Nos. 5,380,810; 5,272,236 and 5,278,272. The density of the SLOP as measured in accordance with ASTM D-792 is generally from 0.85 g/cc to 0.97 g/cc, preferably from 0.85 g/cc to 0.955 g/cc, and especially from 0.85 g/cc to 0.92 g/cc. The melt index, according to ASTM D-1238, Condition 190°C/2.16 kg (also known as l 2 ), of the SLOP is generally from 0.01 g/10 minutes to 1000 g/10 minutes, preferably from 0.01 g/10 minutes to 100 g/10 minutes, and especially from 0.01 g/10 minutes to 10 g/10 minutes. Also, included are the ultra low molecular weight ethylene polymers and ethylene/α-olefin interpolymers described in the WO patent application no. 97/01181 entitled Ultra-low Molecular Weight Polymers, filed on January 22, 1997. These ethylene/α-olefin interpolymers have l 2 melt indices greater than 1 ,000, or a number average molecular weight (Mn) less than 11 ,000. The more preferred homopolymers or interpolymers of aliphatic α-olefins having from 2 to 20 carbon atoms and optionally containing polar groups are homopolymers of ethylene; homopolymers of propylene, copolymers of ethylene and at least other α-olefin containing from 4 to 8 carbon atoms; copolymers of propylene and at least other α-olefin containing from 4 to 8 carbon atoms; copolymers of ethylene and at least one of acrylic acid, vinyl acetate, maleic anhydride or acrylonitrile; copolymers of propylene and at least one of acrylic acid, vinyl acetate, maleic anhydride or acrylonitrile; and terpolymers of ethylene, propylene and a diene. Especially preferred are LDPE, HDPE, heterogeneous and homogeneous LLDPE, SLOP, polypropylene (PP), especially isotactic polypropylene and rubber-toughened polypropylenes, or ethylene-propylene interpolymers (EP), or ethylene- vinyl acetate copolymers, or ethylene-acrylic acid copolymers, or any combination thereof. The filled polymer composition of the present invention may contain one or more additives, for example antioxidants, such as hindered phenols or phosphites; light stabilizers, such as hindered amines; plasticizers, such as dioctylphthalate or epoxidized soy bean oil; tackifiers, such as known hydrocarbon tackifiers; waxes, such as polyethylene waxes; processing aids, such as oils, stearic acid or a metal salt thereof; crosslinking agents, such as peroxides or silanes; colorants or pigments to the extent that they do not interfere with desired physical properties of the filled polymer composition of the present invention. The additives are employed in functionally equivalent amounts known to those skilled in the art, generally in amounts of up to 30, preferably from 0.01 to 5, more preferably from 0.02 to 1 percent by weight, based upon the total weight of the filled polymer composition. The filled polymer compositions can be compounded by any convenient method, such as dry blending of interpolymer(s), the filler(s) and optional additives and subsequently melt mixing, either directly in the extruder used to make the finished article, or by pre-melt mixing in a separate extruder (for example, a Banbury mixer). Dry blends of the compositions can also be directly injection molded without pre-melt mixture. The blends can be processed to fabricated articles by any suitable means known in the art. For example, the filled polymer composition can be processed to films or sheets or to one or more layers of a multilayered structure by know processes, such as calendering, blowing, casting or (co-)extrusion processes. Injection molded, compression molded, extruded or blow molded parts can also be prepared from the filled polymer compositions of the present invention. Alternatively, the filled polymer compositions can be processed to foams or fibers. Useful temperatures for processing the interpoiymer(s) in combination with the filler(s) and optional additives to the fabricated articles generally are 100°C to 300°C, preferably from 120°C to 250°C, more preferably from 140°C to 200°C. The fabricated articles of the present invention may be foamed. The foam layer may be produced by an extrusion process or from expandable or foamable particles, moldable foam particles, or beads from which a sheet is formed by expansion and/or coalescing and welding of those particles. The foam structure may be made by a conventional extrusion foaming process. The structure is generally prepared by heating a polymer material to form a plasticized or melt polymer material, incorporating therein a known blowing agent to form a foamable gel, and extruding the gel through a die to form the foam product. Prior to mixing with the blowing agent, the polymer material is heated to a temperature at or above its glass transition temperature or melting point. The blowing agent may be incorporated or mixed into the melt polymer material by any means known in the art such as with an extruder, mixer or blender. The blowing agent is mixed with the melt polymer material at an elevated pressure sufficient to prevent substantial expansion of the melt polymer material and to generally disperse the blowing agent homogeneously therein. Optionally, a nucleator may be blended in the polymer melt or dry blended with the polymer material prior to plasticizing or melting. The foamable gel is typically cooled to a lower temperature to optimize physical characteristics of the foam structure. The gel is then extruded or conveyed through a die of desired shape to a zone of reduced or lower pressure to form the foam structure. The die can have a substantially rectangular orifice to produce a sheet of the desired width and height. Alternatively, the die can have multiple orifices to produce polymer strands which can be cut to beads. The zone of lower pressure is at a pressure lower than that in which the foamable gel is maintained prior to extrusion through the die. The lower pressure may be superatmospheric or subatmospheric (vacuum), but is preferably at an atmospheric level. The foam structure may also be formed into foam beads suitable for molding into articles. To make the foam beads, discrete resin particles such as granulated resin pellets are suspended in a liquid medium in which they are substantially insoluble such as water; impregnated with a blowing agent by introducing the blowing agent into the liquid medium at an elevated pressure and temperature in an autoclave or other pressure vessel; and rapidly discharged into the atmosphere or a region of reduced pressure to expand to form the foam beads. This process is well taught in U.S. Patent Nos. 4,379,859 and 4,464,484. The foam beads may then be molded by any means known in the art, such as charging the foam beads to the mold, compressing the mold to compress the beads, and heating the beads such as with steam to effect coalescing and welding of the beads to form the article. Optionally, the beads may be impregnated with air or other blowing agent at an elevated pressure and temperature prior to charging to the mold. Further, the beads may be heated prior to charging. The foam beads may then be molded to sheets by a suitable molding method known in the art. Some of the methods are taught in U.S. Patent Nos. 3,504,068 and 3,953,558. Various additives may be incorporated in the foam structure, such as stability control agents, nucleating agents, pigments, antioxidants, acid scavengers, ultraviolet absorbers, flame retardants, processing aids or extrusion aids. Some of the additives are described in more detail above. Fabricated articles of the present invention which are made from filled polymer compositions comprising one or more thermoplastic interpolymers and one or more inorganic fillers in the above-mentioned weight ratios have a substantially improved hardness and tensile modulus while generally maintaining good elongation properties, such as elongation at break, stress at break and energy at break, as compared to fabricated articles made from one or more corresponding thermoplastic interpolymers without inclusion of a filler. Furthermore, the fabricated articles of the present invention generally have good thermal resistance and, depending on the type of filler, improved ignition resistance. The filled polymer compositions of the present invention can readily be extruded onto a substrate. Alternatively the filled polymer compositions of the present invention can be extruded, milled, or calendered as unsupported films or sheets, for example for producing floor tiles, wall tiles, floor sheeting, wall coverings, or ceiling coverings. They are particularly useful as sound insulating or energy absorbing layers, films, sheets or boards. Films, sheets or boards of a wide thickness range can be produced. Depending on the intended end-use, useful thicknesses generally are from 0.5 to 20 mm, preferably from 1 to 10 mm. Alternatively, injection molded parts or blow molded articles, such as toys, containers, building and construction materials, automotive components, and other durable goods can be produced from the filled polymer compositions of the present invention. The following examples are provided to illustrate the present invention. The examples are not intended to limit the scope of the present invention and they should not be so interpreted. Amounts are in weight parts or weight percentages unless otherwise indicated. TESTING The properties of the polymers and blends are determined by the following test procedures. Melt Index (Mil is determined by ASTM D-1238 (1979), Condition E (190°C; 2.16 kg). Tensile strength, secant modulus, and elongation properties are measured using ASTM D 638, Type C. Elongation at break, stress at break and energy at break are measured at a strain rate of 5 min '1 . Flexural modulus is measured using ASTM D 790-95A. Hardness is measured using a Hardness Tester for Shore A and D according to DIN 53505. Tabor abrasion is measured according to ASTM F-510. Scratch testing is carried out using an Erichson Universal Scratch Tester equipped with a 90 degree to 180 μm diameter stylus. A load of 0.1 to 1.0 N is applied to this stylus, and the resulting scratch width is measured after 30 days by a Perthen Surface Profiler. Scratch width and depth is expressed in micrometers. For indentation testing. ASTM F 142-93 (Standard Test Method for Indentation of Resilient Floor-McBurney Test) and a modified test is used. In the modified test, a 140 lb. (64 kg) load is applied via a 4.5 mm diameter cylindrical foot. The load is applied for 10 minutes and the initial indentation is measured. The residual indentation is measured after 60 minutes. For the modified test, indentations are reported as a percent of initial plaque thickness. For residual indentation, the sample is given a "fail" rating if the cylindrical indent foot permanently cuts and damages the surface. Thermal transition temperatures are measured with differential scanning caiorimetry (DSC) and dynamic mechanical spectroscopy (DMS). Preparation of Ethylene/Styrene Interpolvmers ESI-1. ESI-2. ESI-4. ESI-8. ESI-9 and ESI-10 Reactor Description The single reactor used is a 6 gallon (22.7 L), oil jacketed, Autoclave continuously stirred tank reactor (CSTR). A magnetically coupled agitator with Lightning A- 320 impellers provides the mixing. The reactor runs liquid full at 475 psig (3,275 kPa). Process flow is in the bottom and out the top. A heat transfer oil is circulated through the jacket of the reactor to remove some of the heat of reaction. After the exit from the reactor a micromotion flow meter is arranged that measures flow and solution density. All lines on the exit of the reactor are traced with 50 psi (344.7 kPa) steam and insulated. Procedure Ethylbenzene solvent is supplied to the mini-plant at 30 psig (207 kPa). The feed to the reactor is measured by a Micro-Motion mass flow meter. A variable speed diaphragm pump controls the feed rate. At the discharge of the solvent pump a side stream is taken to provide flush flows for the catalyst injection line (1 Ib/hr (0.45 kg/hr)) and the reactor agitator (0.75 Ib/hr ( 0.34 kg/ hr)). These flows are measured by differential pressure flow meters and controlled by manual adjustment of micro-flow needle valves. Uninhibited styrene monomer is supplied to the mini-plant at 30 psig (207 kpa). The feed to the reactor is measured by a Micro-Motion mass flow meter. A variable speed diaphragm pump controls the feed rate. The styrene stream is mixed with the remaining solvent stream. Ethylene is supplied to the mini-plant at 600 psig (4,137 kPa). The ethylene stream is measured by a Micro-Motion mass flow meter just prior to the Research valve controlling flow. A Brooks flow meter/controllers is used to deliver hydrogen into the ethylene stream at the outlet of the ethylene control valve. The ethylene/hydrogen mixture is combined with the solvent/styrene stream at ambient temperature. The temperature of the solvent/monomer as it enters the reactor is reduced to about 5°C by an exchanger with -5°C glycol on the jacket. This stream enters the bottom of the reactor. The three-component catalyst system and its solvent flush also enter the reactor at the bottom but through a different port than the monomer stream. The composition of the three-component catalyst system is as listed below: aluminum molar ratio titanium catalyst boron/Ti molar ratio Polymer catalyst component boron co-catalyst catalyst Al/Ti catalyst ESI-1 type 1 MMAO-3A type 1 3:1 8:1 ESI-2 type 1 MMAO-3A type 1 2:1 5:1 ESI-4 type 1 MMAO-3A type 3 2:1 5:1 ESI-8 type 1 MMAO-3A type 2 1.25:1 12:1 ESI-9 type 2 MMAO-3A type 2 1.25:1 10:1 ESI-10 type 2 MMAO-3A type 2 1.25:1 10:1 The titanium catalyst type 1 is (t- butylamido)dimethyl(tetramethylcyclopentadienyl)silanetitanium (II) 1 ,3-pentadiene. The titanium catalyst type 2 is (t-butylamido_dimethyl(3-phenyl-s-indacen-1- yl)silanetitanium (IV) dimethyl. The aluminum catalyst component is a commercially available modified methalumoxane Type 3A (MMAO-3A). The boron cocatalyst type 1 is tris(pentafluorophenyl)borane . The boron cocatalyst type 2 is bis-hydrogenated tallowalkyl methylammonium tetrakis(pentafluorophenyl)borate . The boron cocatalyst type 3 is a mixture of methyl(C 1822 -alkyl)ammonium tetrakis(pentafluorophenyl)borates and methyldi(C 18.22 -alkyl)ammonium tetrakis(pentafluorophenyl)borates. Preparation of the catalyst components has taken place in an inert atmosphere glove box. The diluted components are put in nitrogen padded cylinders and charged to the catalyst run tanks in the process area. From these run tanks the catalyst is pressured up with piston pumps and the flow is measured with Micro-Motion mass flow meters. These streams combine with each other and the catalyst flush solvent just prior to entry through a single injection line into the reactor. Polymerization is stopped with the addition of catalyst kill (water mixed with solvent) into the reactor product line after the micromotion flow meter measuring the solution density. Other polymer additives can be added with the catalyst kill. A static mixer in the line provides dispersion of the catalyst kill and additives in the reactor effluent stream. This stream next enters post reactor heaters that provide additional energy for the solvent removal flash. This flash occurs as the effluent exits the post reactor heater and the pressure drops from 475 psig (3,275 kPa) down to about 250 mm of pressure absolute at the reactor pressure control valve. This flashed polymer enters a hot oil jacketed devolatilizer. Approximately 85 percent of the volatiles are removed from the polymer in the devolatilizer. The volatiles exit the top of the devolatilizer. The stream is condensed with a glycol jacketed exchanger, enters the suction of a vacuum pump and is discharged to a glycol jacket solvent and styrene/ethylene separation vessel. Solvent and styrene are removed from the bottom of the vessel and ethylene from the top. The ethylene stream is measured with a Micro-Motion mass flow meter and analyzed for composition. The measurement of vented ethylene plus a calculation of the dissolved gasses in the solvent/styrene stream are used to calculate the ethylene conversion. The polymer separated in the devolatilizer is pumped out with a gear pump to a ZSK-30 devolatilizing vacuum extruder. The dry polymer exits the extruder as a single strand. This strand is cooled as it is pulled through a water bath. Excess water is blown from the strand with air and the strand is chopped into pellets with a strand chopper. The monomer amounts and polymerization conditions are provided in Table IA. The polymer properties are provided in Table IC further below. Table IA cc/min., standardized to 1 atm (760 torr) and 0°C. Preparation of Ethylene/Styrene Interpolymers ESI-3. ESI-5. ESI-6 and ESI-7 The Polymer is prepared in a 400 gallon (1514 liter) agitated semi-continuous batch reactor. The reaction mixture consists of about 250 gallons (946 liter) of styrene and a solvent comprising a mixture of cyclohexane (85 weight percent) and isopentane (15 weight percent). Prior to addition, solvent, styrene and ethylene are purified to remove water and oxygen. The inhibitor in the styrene is also removed. Inerts are removed by purging the vessel with ethylene. The vessel is then pressure controlled to a set point with ethylene. Hydrogen is added to control molecular weight. Temperature in the vessel is controlled to set-point by varying the jacket water temperature on the vessel. Prior to polymerization, the vessel is heated to the desired run temperature and the catalyst components, that is, (tert- butylamido)dimethyl(tetramethyl-η5-cyclopentadienyl)silane dimethyltitatium(IV) catalyst, CAS# 135072-62-7, Tris(pentafluorophenyl)boron, CAS# 001109-15-5, modified methylaluminoxane Type 3A, CAS# 146905-79-5, are flow controlled, on a mole ratio basis of 1 :/3:5 respectively, combined and added to the vessel. After starting, the polymerization is allowed to proceed with ethylene supplied to the reactor as required to maintain vessel pressure. In some cases, hydrogen is added to the headspace of the reactor to maintain a mole ratio with respect to the ethylene concentration. At the end of the run, the catalyst flow is stopped, ethylene is removed from the reactor, about 1000 ppm of Irganox™ 1010 anti- oxidant is then added to the solution and the polymer is isolated from the solution. The resulting polymers are isolated from the solution by either stripping with steam in a vessel (in the case of ESI-3, ESI-6 and ESI-7) or by use of a devolatilizing extruder (in the case of ESI-5). In the case of the steam stripped material, additional processing is required in extruder like equipment to reduce residual moisture and any unreacted styrene. The monomer amounts and polymerization conditions are provided in Table 1 B. The polymer properties are provided in Table IC. Table IB Table IC na = not analyzed TABLE II: Other Materials used in Examples Δbbre- Product Name Melt Index Density viation (gm/10 min^ (gm/cc) ITP-1 AFFINITY™ DSH 8501.00 POP 1.0 0.871 (ethylene-1-octene copolymer) ITP-2 AFFINITY™ DSH 1500.00 1.0 0.902 (ethylene- 1-octene copolymer) ITP-3 AFFINITY™ SM 8400 30.0 0.871 (ethylene-1-octene copolymer) ITP-4 AFFINITY™ SM 1300 30.0 0.902 (ethylene-1-octene copolymer) MAH Dow XU-60769.04 2.5 0.955 (maleic anhydride graft polyethylene, containing 1.0% maleic acid) CaCO, for Examples 1-25, 62 and 63 obtained from Pfizer ATF-40 (Ground limestone, 40 mesh) CaCO, for Examples 26-48: Whingdale White (average particle size 6 micron) CaCO, for Examples 49-51 ,53 and 54 obtained from Omya BSH (average particle size 2.4 micron) alumina trihydrate: Martinal OL 104C (Trademark) silica commercially available as Laevisil SP (Trademark) Silitin N85 (Trademark): a 50/50 blend of dolomite and silica Talcum Owen Corning OC 187A-AA Oil SHELLFLEX™ 371 Examples 1 to 25 In Examples 1 to 25 plaques were prepared via the following steps: 1 ) Haake bowl mixing, 2) roll milling, and 3) compression molding into plaques. A Haake mixer equipped with a Rheomix 3000 bowl was used. All components of the blend were added to the mixer, and the rotor was operated at 190°C and 40 rpm for 10 to 15 minutes. The material was then dropped out of the Haake, and fed to a 6 inch diameter by 12 inch wide Farrel two-roll mill set at 175°C surface temperature. The sheet was either taken off after a 180 degree wrap or was allowed to wrap 540 degrees before release. The sheet was then cut and compression molded into 3.175 mm thick by 101.6 mm by 101.6 mm plaques with a Pasadena Hydraulics Incorporated (PHI) press. The press was operated at 205°C in a preheat mode at minimal pressure for 3 minutes, and was then pressured up to 15 tons for 2 minutes. Plaques were then removed from the heat and cooled at 15 tons for 3 minutes. Properties of the compression molded plaques were measured as indicated above. Tables III and IV list the compositions and resulting physical properties of Examples 1 to 23 according to the present invention and of Comparative Examples 24 and 25 for 60 percent filled and 85 percent filled formulations, respectively. COMPOSITION - weight percent CaC03 60 60 60 60 60 60 60 60 60 60 ESI-1 40 36 ESI-3 40 32 36 28 20 36 ESI-4 40 20 Oil ITP-1 12 20 20 ITP-2 ITP-3 ITP-4 MAH PROPERTIES I N ) Tensile Strength (MPa) 1.90 5.81 3.83 2.54 5.23 4.55 3.62 2.71 3.77 7.52 I 2% Secant Mod (MPa) 19.50 87.45 32.12 15.12 58.50 61.83 60.83 38.94 26.94 502.62 Flex Modulus (MPa) 30.88 514.69 41.34 40.20 196.90 198.41 139.48 45.69 37.43 111.04 Elongation at break (%) 460 24.25 196 309.6 68.35 36.6 244 212 100.2 31.9 Hardness-Shore D 35.6 75.2 56.2 50.6 71.6 86.4 48 36.6 40.6 70.6 Hardness-Shore A 86 97.6 91.4 81.2 97.8 96.6 95 78.8 90.4 98 lndentation-14 kg - 1 min (mil) 24 13 14 19 15 18 20 14 21 14 lndentation-14 kg - 10 min (mil) 53 26 23 40 28 31 34 23 47 26 lndentation-64 kg 76 19.8 61 68 31 41 74 67 78 24 (% of thickness) Residual lndentation-64 kg 21 5 8 1.5 5.1 5.8 20.7 14 fail 7.3 (% of thickness) Scratch width (micron) nt nt nt nt nt 48 nt nt nt 102 Scratch depth (micron) nt nt nt nt nt 2.37 nt nt nt 2.77 Taber Abrasion (mg/100 rev) 0.60 3.92 2.88 1.46 4.98 5.86 6.88 5.88 1.12 7.52 nt = not tested Examples 1 to 8 illustrate that no additive or polymeric coupling agent was required to achieve good filler holding and solid state properties. The products of Examples 1 to 10 were useful as filled homogeneous sheets, such as floor coverings, or as an individual layer in a heterogeneous structure. The products of Examples 1 to 10 are especially suited for floor sheeting products. I O I Table IV continued Elongation at break 2.45 0.15 5.9 8.7 2.05 5.4 0.65 9.2 3.6 6.3 3.65 0.05 1.7 (%) Hardness-Shore D 87 85 82 63 83 73 65 74 53 66 63 70 78 57 70 Hardness-Shore A 96 98 96 92 98 99 98 98 95 98 96 98 99 97 98 lndentation-14 kg 12 14 10 14 1 min (mil) lndentation-14 kg 21 10 29 13 15 19 13 12 11 10 min (mil) I— • lndentation-64 kg 71 4.1 61 4.8 nt 28 5.2 89 9.9 30 15.5 7.5 91 5.8 I (% of thickness) Residual lndentation- fail 1.7 0.7 11.8 2.1 2.5 6.9 0.8 fail 2.3 7.5 7.4 2.8 fail 1.6 64 kg (% of thickness) Scratch width (micron) 77 77 59 64 56 73 80 79 69 nt nt 82 66 105 101 Scratch depth (micron) 4.80 2.51 1.89 5.26 2.05 5.65 4.97 5.16 12.41 nt nt 7.93 3.46 9.07 6.19 jTaber Abrasion 12.72 14.86 12.72 12.38 15.8 19.98 21.48 nt 18.66 17.48 21.76 18.22 nt 17.86 15.72 (mg/100 rev) * Comparative Example nt = not tested The plaques of Examples 11 to 23 have a considerably higher high scratch resistance than the plaques of Comparative Examples 24 and 25. Examples 11 to 21 illustrate that no additive or polymeric coupling agent was required to achieve good filler holding and solid state properties. The plaque of Example 13 showed an exceptional combination of flexibility and indentation resistance, and was particularly useful in or as a floor tile product with good installation ability and good conformability to uneven and contoured surfaces. The products of Examples 11 to 23 were useful as a filled homogeneous sheets, such as floor coverings, or as an individual layer in a heterogeneous structure. The products of Examples 11 to 23 were especially suited for floor tile products. Examples 26 to 48 In Examples 26 to 48 plaques were produced as described above in Examples 1 to 27 except that no roll milling process was applied and the dimensions of the plaques were 5 inches by 5 inches by 0.08 inches (127 mm by 127 mm by 2.03 mm). COMPOSITION • weight percent CaC03 50 20 20 50 80 talc 50 20 20 50 glass fibers 50 20 20 50 ESI-5 100 50 50 50 80 80 80 ESI-6 100 80 50 20 80 50 80 50 I I PROPERTIES Tensile Strength (MPa) 2% Secant Mod (MPa) Flex Modulus (MPa) 20 69.6 233.7 804 33.8 64.8 293.1 7.6 9.7 17.9 168.9 15.9 75.2 246.8 1228 Yield stress (MPa) 11 16 Elongation (%) at break 378 320 102 341 347 178 147 581 581 21 602 503 25 Stress at break (MPa) 34.3 17.1 12.2 11.4 30.2 32.7 12 2.9 15 8.8 7.7 16.2 8.6 5.8 19 Energy at break (Nm) 145.1 158.7 59.7 3.5 162.7 179 84.1 12.2 105.8 93.6 6.8 154.6 153.2 5.4 5.4 * Comparative Example nt = not tested Table V (continued) nt = not tested Examples 49 to 63 Plaques are prepared by 1) mixing, 2) roll milling, and 3) pressing into plaques. In the mixing step the polymers were molten and the desired amount of filler was added in small portions. The mixing time was 10 to 15 minutes. In the roll milling step the following conditions were applied: The sheet produced by roll milling was then cut and filled into a mold consisting of a steel plate covered with a tetrafluoroethylene fluorocarbon polymer material (TEFLON™) and a frame of 28 cm by 28 cm by 0.2 cm. The mass of the cut sheet filled into the frame was the volume of the mold, that is 156.8 cm 3 , by density of the composition + 10 percent. The mold was closed with a plate of steel and pressed at an elevated temperature. The material was pre-pressed for 5 minutes at 8 bar and for 3 minutes at 200 bar machine pressure at a temperature of 175° C (Examples 49-60) or 190° C (Example 61) or 160° C (Example 62 and 63). The mold was placed between a water-cooled steel bottom plate and top plate and cooled to room temperature within 5 minutes. Sheets of 2 mm thickness were produced. Table VI I I Examples 49 to 63 illustrate that no additive or polymeric coupling agent was required to achieve good filler holding and solid state properties. The comparison between Comparative Example 52 and Examples 53-60 illustrate the high ultimate tensile elongation of filled polymer compositions of the present invention.

Claims: CLAIMS: 1. A filled polymer composition comprising: (A) from 5 to 90 percent of one or more thermoplastic substantially random interpolymers prepared by polymerizing one or more α-olefin monomers with one or more vinylidene aromatic monomers and/or one or more hindered aliphatic or cycloaliphatic vinylidene monomers, and optionally with other polymerizable ethylenically unsaturated monomer(s), and (B) from 10 to 95 percent of one or more inorganic fillers, the amounts of (A) and (B) being based on the total weight of (A) and (B). 2. The filled polymer composition of Claim 1 wherein said one or more interpolymers contain interpolymerized from 0.5 to 65 mole percent of one or more α-olefin monomers and from 99.5 to 35 mole percent of one or more vinylidene aromatic monomers and/or one or more hindered aliphatic or cycloaliphatic vinylidene monomers, and optionally other polymerizable ethylenically unsaturated monomer(s). 3. The filled polymer composition of Claim 1 or Claim 2 wherein said interpolymer is an interpolymer of ethylene and styrene. 4. The filled polymer composition of any one of Claims 1 to 3 comprising from 40 to 90 percent of one or more inorganic fillers, based on the total weight of the interpolymer(s) and the filler(s). 5. The filled polymer composition of any one of Claims 1 to 4 comprising one or more ionic inorganic fillers. 6. The filled polymer composition of Claim 5 wherein the filler is talc, calcium carbonate, barium sulfate, alumina trihydrate, glass fibers or a mixture thereof. 7. The filled polymer composition of any one of Claims 1 to 6 wherein the total amount of the interpolymer(s) (A) and the inorganic filler(s) (B) is at least 50 percent, based on the total weight of the filled polymer composition. 8. The filled polymer composition of any one of Claims 1 to 7 comprising up to 50 weight percent of one or more additional polymeric component(s), based on the total weight of the filled polymer composition. 9. A fabricated article made from the polymer composition of any one of Claims 1 to 8. 10. The fabricated article of Claim 9 in the shape of a film or sheet. 11. The fabricated article of Claim 9 in the shape of a floor, wall or ceiling covering. 12. The fabricated article of Claim 9 in the form of a foam or in the shape of fibers. 13. The fabricated article of Claim 9 made by injection molding, compression molding, extrusion or blow molding. 14. A multilayered structure wherein at least one layer is made from the polymer composition of any one of Claims 1 to 8.

Inventors: BIESER JOHN O, CHEUNG YUNWA W, GATHERS JOHN J, GUEST MARTIN J, THOEN JOHAN A, BIESER, JOHN, O., CHEUNG, YUNWA, W., GATHERS, JOHN, J., GUEST, MARTIN, J., THOEN, JOHAN, A.
Applicants: DOW CHEMICAL CO, THE DOW CHEMICAL COMPANY
Application year: 1998
Main classification: C08K3
IPC codes: B32B27, C08F212, C08J5, C08J9, C08K3, C08K5, C08L23, C08L25