RANDOM CYCLOOLEFIN COPOLYMER COMPOSITION

Abstract: The random cycloolefin copolymer compsn. comprises: (A) a random cyclo-olefin copolymer composed of an ethylenic component and a cycloolefin component of formulae (I) and (II), respectively. In the formulae, R1-R10 are, each, H, halogen atom, or hydrocarbon group; n and m are each 0 or positive integers; l is an integer greater than or equal to 3; (B) one or more soft copolymers selected from the gp. consisting of (i) random cycloolefin copolymers composed of an ethylenic component, at least one other alpha-olefinic component and a cycloolefin component, (ii) amorphous or weakly crystalline alpha-olefinic elastic copolymers formed by at least two olefins, (iii) elastic alpha-olefin-diene copolymers formed by at least two alpha-olefins and at least one non-conjugated diene, and (iv) aromatic vinyl hydrocarbon-conjugated diene copolymers or their hydrogenation prods., and, if necessary, (C) an organic or inorganic filler. (A) has a limiting viscosity measured at 135 deg.C in decalin of 0.05 to 10 dl/g and a softening temp. (TMA) of 70 deg.C or higher. Component (i) of (B) has a limiting viscosity of 0.01-10 dl/g and a softening temp. lower than 70 deg.C.

Description: This invention relates to cycloolefin type random copolymer compositions which are excellent in heat resistance, heat ageing characteristics, chemical resistance, solvent resistance, dielectric characteristics and rigidity as well as in impact resistance. Known as synthetic resins having well-balanced properties between rigidity and impact strength are polycarbonates, ABS (acrylonitrile-butadiene-styrene compositions), etc. For instance, polycarbonates are resins which have excellent rigidity as well as good heat resistance, heat ageing characteristics and impact strength. However, polycarbonates have poor chemical resistance as they are easily attacked by strong alkali. Further, they have high water absorption. Though ABS composition are excellent in mechanical properties, they have poor chemical resistance and further, because of double bonds in their molecular structure, they have poor weather resistance and heat resistance. On one hand, polyolefins which are widely used as general-purpose resins are excellent in chemical resistance and solvent resistance. However, many polyolefins have poor heat resistance, insufficient crystallizability and poor rigidity. In general, to improve the rigidity and heat resistance of polyolefins, nucleating agents are incorporated into the polyolefins to expedite the growth of crystal, or polyolefins are gradually cooled to accelerate the growth of crystal. However, the results of these processes are not always satisfactory. Incorporating into polyolefins a third component, such as a nucleating agent, may adversely affect the properties of the polyolefins, and a gradual cooling procedure has a low production efficiency and may lower impact strength as the non-crystalline part of polyolefins is reduced. A copolymer of ethylene and 2,3-dihydroxy-dicyclopentadiene has been disclosed as an example of copolymers of ethylene and bulky comonomers, for example, in U.S.-A- 2,883,372. However, this copolymer is poor in heat resistance as it has a glass transition temperature in the vicinity of 100°C, though said copolymer is well balanced between rigidity and transparency. A similar drawback is also observed with copolymers of ethylene and 5-ethylidene-2-norbornene. JP-B- 14910/1971 proposes a homopolymer of 1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene. The proposed polymer, however, is poor in heat resistance and heat ageing characteristics. JP-A-127728/1983 further proposes a homopolymer of 1,4,5,8-dimethano-1,2,3,4,4a,6,8,8a-octahydronaphthalene or copolymers of said cycloolefin and norbornene type comonomers, which are apparently those obtained by ring opening polymerization (ring opening polymers) in light of the disclosure in said publication. These ring opening polymers which have unsaturated bonds in the polymer main chains, however, have such a drawback that they are poor in heat resistance and heat ageing characteristics. In the course of these researches, we found that cycloolefin type random copolymers of ethylene and bulky cycloolefins are synthetic resins which are excellent in heat resistance as well as in heat ageing characteristics, chemical resistance, solvent resistance, dielectric characteristics and rigidity. On the basis of the above findings, we have already made various technical proposals in JP-A-168708/1985 and JP-A-220550/1984, JP-A-236828-1984, JP-A-236829/1984, JP-A-242336/1984 and JP-A-95906/1986. In spite of their being olefin type polymers, the cycloolefin type random copolymers as proposed are excellent in heat resistance and rigidity. However, they involve such problems that they are brittle and poor in impact resistance. EP-A-156 464 discloses a random copolymer comprising ethylene, a 1, 4, 5, 8- dimethano - 1, 2, 3, 4, 4a, 5, 8, 8a octahydro-napthalene and optionally an alpha-olefin having at least three carbon atoms or cycloolefin. We have made studies to improve the rigidity and impact resistance of cycloolefin type random copolymers without detriment to their excellent heat resistance, heat ageing characteristics, chemical resistance, solvent resistance and dielectric characteristics. As a result, we have found that compositions consisting of a cycloolefin type random copolymer having a specific softening temperature (TMA) and at least one specific non-rigid copolymer or compositions obtained by blending inorganic filler and/or organic filler with said composition consisting of said random copolymer and said non-rigid copolymer have the above-described excellent characteristics. The present invention therefore provides a cycloolefin type random copolymer composition comprising (A) a cycloolefin type random copolymer containing 40 to 85 mol % ethylene component and 15 to 60 mol % cycloolefin component represented by the following general formula (I) or (II) and having an intrinsic viscosity [η] of 0.05-10 dl/g as measured at 135°C in decalin, a softening temperature (TMA) of not lower than 70°C, and a crystallinity index of 0 to 10 % as measured by X-ray diffractometry, and (B) one or more non-rigid copolymers selected from: (i) a cycloolefin type random copolymer containing 40 to 99 mol % ethylene component, at least one α-olefin component having 3 to 20 carbon atoms and present in the range of less than the equimolar amount of the ethylene component and 1 to 40 mol % of a cycloolefin component represented by formula (I) or (II) and having an intrinsic viscosity [η] of 0.01-10 dl/g as measured at 135°C in decalin and a softening temperature (TMA) of below 70°C, (ii) an ethylene/α-olefin copolymer rubber containing an ethylene component and an α-olefin component having 3-20 carbon atoms, wherein the molar ratio of ethylene/α-olefin is in the range of from 30/70-95/5, and the crystallinity index of the ethylene/α-olefin copolymer is in the range of 0-50%, an intrinsic viscosity (η) of 0.2 to 10 dl/g as measured at 135°C in decalin, and a density of 0.82 to 0.96 g/cm³, (iii) an ethylene/α-olefin/non-conjugated diene copolymer rubber containing an ethylene component, α-olefin component having 3-20 carbon atoms and non-conjugated diene component, wherein the molar ratio of ethylene/α-olefin is in the range of from 50/50-95/5, the content of the non-conjugated diene component in the ethylene/α-olefin/non-conjugated diene copolymer is in the range of 0.5 to 10 mol %, and the crystallinity index of the ethylene/α-olefin/non-conjugated diene copolymer is in the range of 0-10%, and an intrinsic viscosity (η) of 0.1 to 10 dl/g, an iodine value of 1 to 30 and a density of 0.82 to 1.00 g/cm³, and (iv) hydrogenated styrene-butadiene-styrene block copolymer rubber or hydrogenated styrene-isoprene-styrene block copolymer rubber, having a weight-average molecular weight of Mw of 500 to 2 000 000 as measured with gel permeation chromatography (GPC) ion-dichlorobenzene at 140°C and a density of 0.80 to 1.10 g/cm³. in such a proportion that the total amount of the component (B) is 5 to 100 parts by weight based on 100 parts by weight of the component (A); General formula wherein n and m are each 0 or a positive integer, ℓ is an integer of at least 3, and R¹ to R¹⁰ each represents hydrogen atom, halogen atom or hydrocarbon group. The present invention further provides a cycloolefin type random copolymer composition comprising (A) a cycloolefin type random copolymer as defined herein, (B) at least two non-rigid copolymers selected from components (i), (ii), (iii) and (iv) as defined herein and (C) an inorganic filler or organic filler, in such a proportion that the total amount of the component (B) is 1 to 100 parts by weight based on 100 parts by weight of the component (A) and the amount of the component (C) is 1 to 100 parts by weight based on 100 parts by weight of the component (A). Preferably the cyclo-olefin type random copolymer containing an ethylene component, at least one other α-olefin component and a cycloolefin component represented by formula (I) or (II) is a cycloolefin type random copolymer containing an ethylene component, a propylene component and a cycloolefin component represented by formula (I) or (II), or a cycloolefin type random copolymer containing an ethylene component, a butene component and a cycloolefin component represented by formula (I) or (II). Figure 1 is a graph showing the relationship between the amount of the cycloolefin type random copolymer [B](i) to be blended in the cycloolefin type random copolymer composition of the invention and the impact strength (IZ strength) of said composition. Figure 2 is a graph showing the relationship between the amount of the cycloolefin random copolymer [B] (i) blended in the cycloolefin type random copolymer composition of the invention and the softening temperature (TMA) of said composition. Figure 3 is a graph showing the relationship between the mount of the α-olefin type random copolymer [B](ii) blended in the cycloolefin type random copolymer composition of the invention and the impact strength (IZ strength) of said composition. Figure 4 is a graph showing the relationship between the amount of the α-olefin type random copolymer [B](ii) blended in the cycloolefin type random copolymer composition of the invention and the softening temperature (TMA) of said composition. Figure 5 is a graph showing the relationship between the amount of the α-olefin-diene type random copolymer [B](iii) blended in the cycloolefin type random copolymer composition of the invention and the impact strength (IZ strength) of said composition. Figure 6 is a graph showing the relationship between the amount of the α-olefin-diene type random copolymer [B](iii) blended in the cycloolefin type random copolymer composition and the softening temperature (TMA) of said composition. Figure 7 is a graph showing the relationship between the amount of the aromatic vinyl type hydrocarbon-conjugated diene copolymer or a hydrogenated product thereof blended in the cycloolefin type random copolymer composition of the invention and the impact strength (IZ strength) of said composition. Figure 8 is a graph showing the relationship between the amount of the component [B] (iv) blended in the cycloolefin type random copolymer composition of the invention and the softening temperature (TMA) of said composition. Figure 9 is a graph showing the relationship between the total amount of two or more non-rigid copolymers (B) blended in the cycloolefin type random copolymer composition of the invention and the impact strength (IZ strength) of said composition. Figure 10 is a graph showing the relationship between the total amount of the non-rigid copolymer (B) blended in the cycloolefin type random copolymer composition of the invention and the softening temperature of said composition. In the cycloolefin random copolymer the cycloolefin component has the structure shown in formula III or IV. wherein n, m, ℓ and R¹ to R¹⁰ are as defined above. The cycloolefins represented by the general formula [I] can be prepared by condensation of a cyclopentadiene with an olefin by Diels-Alder reaction. Similarly, the cycloolefins represented by the general formula [II] can be prepared by condensation of cyclopentadienes with a cycloolefin by Diels-Alder reaction. The cycloolefins represented by the general formula [I] include, for example, the compounds listed in Table 1, octahydronaphthalenes such as 1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-methyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-ethyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-propyl-1,4,5,8-dimethano-1,2,3,4,4a,8,8a-octahydronaphthalene, 2-hexyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2,3-dimethyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-methyl-3-ethyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-chloro-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-bromo-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-fluoro-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2,3-dichloro-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-cyclohexyl-1,4,5,8,dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-n-butyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, 2-isobutyl-1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene, etc. and such compounds as exemplified in Table 2. The cycloolefins represented by the general formula [II] include, for example, the compounds exemplified in Tables 3 and 4. In addition to the cycloolefin component and ethylene component the cycloolefin type random copolymer [A] may optionally contain other copolymerizable unsaturated monomer components in such a range that they do not hinder the object of the present invention. Such unsaturated monomers include, for example, α-olefins of 3 to 20 carbon atoms, such as propylene, 1-butene, 4-methyl-1-pentene, 1-hexene, 1-octene, 1-decene, 1-dodecene, 1-tetradecene, 1-hexadecene, 1-octadecene, 1-eicosene, etc. in the range of less than an equimolar amount of the ethylene component in the resulting random copolymer. The cycloolefin type random copolymer [A] preferably comprises 50 to 75 mol % of repeating units (a) derived from ethylene, [A] preferably comprises 25 to 50 mol % repeating units (b) derived from the cycloolefin. The repeating units (a) are arranged substantially linearly and at random. That the cycloolefin type random copolymers [A] are substantially linear and do not contain a gel-forming cross-linked structure can be confirmed by the fact that said copolymers perfectly dissolve in decalin kept at 135°C. An intrinsic viscosity [η] as measured at 135°C in decalin of the cycloolefin type random copolymer [A] is in the range of 0.05-10 dl/g, preferably 0.08-5 dl/g. A softening temperature (TMA) as measured with a thermal mechanical analyzer of the cycloolefin type random copolymer [A] is not lower than 70°C, preferably in the range of 90-250°C, more preferably 100-200°C. Furthermore, a glass transition temperature (Tg) of said cycloolefin type random copolymer [A] is usually in the range of 50-230°C, preferably 70-210°C. A crystallinity index as measured by X-ray diffractometry of the cycloolefin type random copolymer [A] is in the range of 0-10%, preferably 0-7%, more preferably 0-5%. The cycloolefin type random copolymer [B] (i), comprises as essential components an ethylene component, a cycloolefin component and at least one α-olefin of 3 to 20 carbon atoms such as, for example, propylene, 1-butene, 4-methyl-1-pentene, 1-hexene, 1-octene, 1-decene, 1-dodecene, 1-tetradecene, 1-hexadecene, 1-octadecene or 1-eicosane, in the range of less than an equimolar amount of the ethylene component unit in the resulting random copolymer. In the cycloolefin type random copolymer [B] (i), there are present repeating units (a) derived from ethylene preferably in the range of 75 to 98 mol %, repeating units (b) derived from the cycloolefin(s) preferably in the range of 1 to 15 mol %, and repeating units (c) derived from the α-olefin preferably in the range of 1 to 35 mol %, and the repeating unit (a), (b) and (c) are arranged substantially linearly and at random. That the cycloolefin type random copolymers [B] (i) are substantially linear and do not contain a gel-forming cross-linked structure can be confirmed by the fact that said copolymers perfectly dissolve in decalin kept at 135°C. The ethylene/α-olefin elastomeric copolymers [B] (ii) are non-crystalline or low crystalline copolymers. Examples of the α-olefins which constitute said ethylene α-olefin copolymer rubber are, for example, propylene, 1-butene, 1-pentene, 1-hexene, 4-methyl-1-pentene, 1-octene, 1-decene or mixtures thereof. Among them, propylene or 1-butene is particularly preferred. The molar ratio of ethylene to α-olefin varies depending on the types of the α-olefins, but is preferably from 50/50 to 95/5. When the α-olefin is propylene, said molar ratio is preferably in the range of from 50/50 to 90/10, while when the α-olefins are those of four or more carbon atoms, said molar ratio is preferably in the range of from 80/20 to 95/5. A crystallinity index as measured by X-ray diffractometry of the α-olefin type elastomeric copolymer [B](ii) is preferably in the range of 0-50%, more preferably 0-25%. An intrinsic viscosity [η] as measured at 135°C in decalin of the α-olefin type elastomeric copolymer [B](ii) is preferably 1-5 dl/g as measured at 135°C in decalin. The density thereof is preferably in the range of -0.92 g/cm³. The α-olefin type elastomeric copolymers [B](ii) which are used in the present invention may be graft-modified copolymers which are modified with 0.01 to 5% by weight, preferably 0.1 to 4% by weight of graft monomers selected from unsaturated carboxylic acids or derivatives thereof. Examples of the unsaturated carboxylic acids and derivatives thereof which are used for the modification of the ethylene α-olefin copolymers [B] (ii) in the present invention include such unsaturated carboxylic acids as acrylic acid, maleic acid, fumaric acid, tetrahydrophthalic acid, itaconic acid, citraconic acid, crotonic acid, isocrotonic acid and nadic acid® (endocisbicyclo[2,2,1]hept-5-ene-2,3-dicarboxylic acid) and derivatives thereof such as acid halides, amides, imides, anhydrides and esters. Examples of said derivatives include malenyl chloride, maleimide, maleic anhydride, citraconic anhydride, monomethyl maleate, dimethyl maleate, glycidyl maleate, etc. Among them, unsaturated dicarboxylic acids or acid anhydrides thereof are preferred and maleic acid, nadic acid® and anhydrides thereof are particularly preferred. The modified copolymers can be produced by graft-copolymerizing a graft monomer selected from said unsaturated carboxylic acids and said derivatives onto the ethylene α-olefin copolymer [B](ii) by any of various conventional methods. For example, the modified copolymers can be produced by a method wherein said ethylene α-olefin copolymer is molten, a graft monomer is added thereto and a graft polymerization reaction is carried out, or a method wherein said ethylene α-olefin type elastomeric copolymer is dissolved in a solvent, a graft monomer is added thereto and a graft copolymerization reaction is carried out. In either case, it is preferred to carry out the graft reaction in the presence of a radical initiator to graft-copolymerize efficiently the graft monomer. The graft reaction is usually carried out at a temperature of 60 to 350°C. The amount of the radical initiator to be used is generally in the range of 0.001 to 1 part by weight based on 100 parts by weight of the ethylene-α-olefin random copolymer. Examples of the radical initiator include organic peroxides and organic peresters such as benzoyl peroxide, dichlorobenzoyl peroxide, dicumyl peroxide, di-tert-butyl peroxide, 2,5-dimethyl-2,5-di(peroxide benzoate)hexine-3, 1,4-bis(tert-butyl peroxyisopropyl)benzene, lauroyl peroxide, tert-butyl peracetate, 2,5-dimethyl-2,5-di(tert-butylperoxy)hexine-2, 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane, tert-butyl perbenzoate, tert-butyl perphenylacetate, tert-butyl perisobutyrate, tert-butyl per-sec-octoate, tert-butyl perpivalate, cumyl perpivalate and tert-butyl perdiethylacetate; and azo compounds such as azobisisobutyronitrile and dimethyl azoisobutyrate. Among them, dialkyl peroxides such as dicumyl peroxide, di-tert-butyl peroxide, 2,5-dimethyl-2,5-di(tert-butylperoxy) hexine-3, 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane and 1,4-bis(tert-butylperoxyisopropyl)benzene, are preferred. Among said α-olefin type elastomeric copolymers [B](ii), graft-modified copolymers obtained by modifying ethylene-propylene random copolymers or ethylene-α-olefin random copolymers having an ethylene content of 35 to 50 mol% and a crystallinity index of not higher than 5% with a graft monomers selected from said unsaturated carboxylic acids and derivatives thereof are the most preferred. Compositions comprising these copolymers generally have improved impact resistance. The component [B] (iii) is an ethylene/α-olefin/non-conjugated diene copolymer rubber. The α-olefin is, for example, propylene, 1-butene, 1-pentene, 1-hexene, 4-methyl-1-pentene, 1-octene, 1-decene or mixtures thereof. Among them, propylene or 1-butene is preferred. The non-conjugated diene is, for example, a linear diene such as octadiene, 2-methyl-1, 5-hexadiene, 6-methyl-1, 5-heptadiene or 7-methyl-1, 6-octadiene, or a cyclic diene such as cyclohexadiene, dicyclopentadiene, methyltetrahydroindene, 5-vinylnorbornene, 5-ethylidene-2-norbornene, 5-methylene-2-norbornene, 5-isopropyldiene-2-norbornene, 6-chloromethyl-5-isopropenyl-2-norbornene, 2,3-diisopropylidene-5-norbornene, 2-ethylidene-3-isopropyldiene-5-norbornene or 2-propenyl-2,2-norbornadiene. Among them, 1,4-hexadiene and cyclic non-conjugated dienes, particularly, dicyclopentadiene or 5-ethylidene-2-norbornene, 5-vinyl-2-norbornene, 5-methylene-2-norbornene, 1,4-hexadiene and 1,4-octadiene are preferred. The molar ratio of ethylene to α-olefin in [B] (iii) varies depending on the type of α-olefins. When the α-olefin is propylene, said molar ratio is preferably in the range of from 50/50 to 90/10. When the α-olefins are those of four or more carbon atoms, said molar ratio is preferably in the range of from 80/20 to 95/5. The content of the diene component in the copolymer rubber is preferably 0.5 to 5 mol %. A crystallinity index as measured by X-ray diffractometry of the α-olefin-diene type elastomeric copolymer [B](iii) is preferably in the range of 0-10%, more preferably 0-5%. An intrinsic viscosity [η] as measured at 135°C in decalin of the α-olefin-diene type elastomeric copolymers [B] (iii) is preferably 1-5 dl/g. The iodine value thereof is preferably 5-25, and the density thereof is preferably 0.85-0.90 g/cm³. The component [B] (iv) is a hydrogenated styrene-butadiene-styrene block copolymer rubber or a hydrogenated styrene-isoprene-styrene block copolymer rubber. The hydrogenated styrene-butadiene-styrene block copolymer rubbers are copolymer rubbers wherein double bonds left in said styrene-butadiene-styrene block copolymer rubbers are partially hydrogenated and the weight ratio of styrene to rubber moiety is preferably in the range of from 0/100 to 50/50. The hydrogenated styrene-isoprene-styrene block copolymer rubbers are copolymer rubbers wherein double bonds left in said styrene-isoprene-styrene block copolymers are partially hydrogenated and the weight ratio of styrene to rubber moiety is preferably in the range of from 0/100 to 50/50. A weight-average molecular weight Mw as measured with GPC (gel permeation chromatography, solvent: o-dichlorobenzene, 140°C) of the aromatic vinyl type hydrocarbon-conjugated diene block copolymer is preferably 10000 to 1000000, and the density thereof is preferably 0.88-0.96 g/cm³. In the present invention, the aforementioned non-rigid copolymers [B](i) to [B](iv) are used either alone or in combination of two or more of them and incorporated into the cycloolefin type random copolymer compositions. When said non-rigid copolymers are used in combination, any of the combinations of the non-rigid copolymers (i) to (iv) can be used. In the cycloolefin type random copolymer compositions of the present invention, the total amount of the non-rigid copolymer (B) used is preferably 7 to 80 parts by weight, particularly preferably 10 to 70 parts by weight based on 100 parts by weight of the cycloolefin type random copolymer [A]. When the total amount of the non-rigid copolymer [B] is less than 5 parts by weight based on 100 parts by weight of the cycloolefin type random copolymer [A], the compositions are poor in impact resistance, though they are excellent in rigidity, while when the total amount of the non-rigid copolymer [B] is more than 100 parts by weight, the rigidity of the compositions is low and the balance between rigidity and impact strength becomes poor. It is apparent from Fig. 1 that when the cycloolefin type random copolymer [B] is blended with the cycloolefin type random copolymer [A], the impact resistance of the resulting cycloolefin type random copolymer composition is remarkably improved. It is apparent from Fig. 2 that even when up to 30 wt.% of the cycloolefin type random copolymer [B] is blended with the cycloolefin type random copolymer [A], it is surprisingly found that the softening temperature (TMA) of the cycloolefin type random copolymer composition is not lowered at all. The impact resistance of the cycloolefin type copolymer composition is greatly improved and heat resistance is not lowered, when up to about 30 wt.% of the cycloolefin type random copolymer [B] is blended with the cycloolefin type random copolymer [A]. In Figs. 1 and 2, the mark o represents values for Examples 1 to 3 and Comparative Example 1, the mark  represents values for Example 4 and Comparative Example 2, the marks □ represents values for Examples 5 to 7 and Comparative Example 3, the mark ▪ represents values for Examples 8 and 9 and Comparative Example 4, the mark Δ represents values for Examples 10 and 11 and Comparative Example 5, the mark ▴ represents values for Examples 12 and 13, and the mark ▿ represents values for Examples 14 and 15 and Comparative Example 6. It is apparent from Fig. 3 that the impact strength of the cycloolefin type random copolymer composition is remarkably improved, when the α-olefin type elastomeric copolymer [B] is blended with the cycloolefin type random copolymer [A]. It is apparent from Fig. 4 that it is surprisingly found that the softening temperature (TMA) of the cycloolefin type random copolymer composition is scarcely lowered, when up to 30 wt.% of the α-olefin type elastomeric copolymer [B] is blended with the cycloolefin type random copolymer [A]. The impact resistance of the cycloolefin type random copolymer composition is greatly improved and heat resistance is not lowered, when up to about 30 wt.% of the α-olefin type elastomeric copolymer [B] is blended with the cyclolefin type random copolymers [A]. In Figs. 3 and 4, the mark o represents values for Examples 16 to 20 and Comparative Example 7, the mark □ represents values for Examples 21 to 23 and Comparative Example 8, the mark  represents values for Examples 26 and 27 and Comparative Example 10, and the mark Δ represents values for Examples 28 and 29 and Comparative Example 11. It is apparent from Fig. 5 that the impact resistance of the resulting cycloolefin type random copolymer composition is remarkably improved, when the olefin-diene type elastomeric copolymer [B] is blended with the cycloolefin type random copolymer [A]. It is apparent from Fig. 6 that the softening temperature (TMA) of the cycloolefin type random copolymer composition is surprisingly not lowered at all, even when up to about 30 wt.% of the α-olefin-diene type elastomeric copolymer [B] is blended with the cycloolefin type random copolymer [A]. As stated above, the impact resistance of the cycloolefin type random copolymer composition is remarkably improved and heat resistance is not lowered, when up to about 30 wt.% of they α-olefin-diene type elastomeric copolymer [B] is blended with the cycloolefin type random copolymer [A]. In Figs. 5 and 6, the mark o represents values for Examples 35 to 41 and Comparative Example 13, the mark □ represents values for Examples 42 to 44 and Comparative Example 14, the mark  represents values for Examples 45 and 46 and Comparative Example 15, the mark ▪ represents values for Examples 47 and 48 and Comparative Example 16, and the mark Δ represent values for Examples 49 and 50 and Comparative Example 17. It is apparent from Fig. 7 that the impact resistance of the resulting cycloolefin type random copolymer composition is remarkably improved, when the aromatic vinyl type hydrocarbon-conjugated diene copolymer or a hydrogenated product thereof [B] is blended with the cycloolefin type random copolymer [A]. It is apparent from Fig. 8 that the softening temperature (TMA) of the cycloolefin type random copolymer composition is surprisingly not lowered at all, even when up to about 30 wt.% of the component [B](iv) is blended with the cycloolefin type random copolymer [A]. As stated above, the impact resistance of the cyloolefin type random copolymer composition is remarkably improved and heat resistance is not lowered, when up to about 30 wt.% of the aromatic vinyl type hydrocarbon-conjugated diene copolymer or hydrogenated product thereof [B] is blended with the cycloolefin type random copolymer [A]. In Figs. 7 and 8, the mark o represents values for Examples 51 to 57 and Comparative Example 18, the mark □ represents values for Examples 58 to 60, the mark  represents values for Examples 61 and 62 and Comparative Example 20, the mark ▪ represents values for Examples 65 and 66 and Comparative Example 21, and the mark Δ represents values for Examples 65 and 66 and Comparative Example 22. It is apparent from Fig. 9 that the impact resistance of the cycloolefin type random copolymer composition is remarkably improved, when the non-rigid copolymers [B] are blended with the cycloolefin type random copolymer [A]. It is apparent from Fig. 10 that the softening temperature (TMA) of the cycloolefin type random copolymer composition is surprisingly not lowered at all, even when up to about 30 wt.% of the non-rigid copolymer [B] is blended with the cycloolefin type random copolymer [A]. As stated above, the impact resistance of the cycloolefin type random copolymer composition is remarkably improved and heat resistance is not lowered, when up to about 30 wt.% of the non-rigid copolymer [B] is blended with the cycloolefin type random copolymer [A]. In Figs. 9 and 10, the mark o represents values for Examples 67 to 72 and Comparative Example 23, the mark □ represents values for Examples 73 to 77 and Comparative Example 24, the mark  represents values for Examples 78 to 80 and Comparative Example 25, the mark ▪ represents values for Examples 81 and 82 and Comparative Example 26, and the mark Δ represents values for Examples 83 and 84 and Comparative Example 27. According to a further embodiment of the invention, the compositions may contain an inorganic or organic filler component (C) in addition to said cycloolefin type random copolymer (A) and said non-rigid copolymer (B). Examples of the inorganic fillers include silica, silica-alumina, alumina, glass powder, glass bead, glass fiber, glass fiber cloth, glass fiber mat, asbestos, graphite, carbon fiber, carbon fiber cloth, carbon fiber mat, titanium oxide, molybdenum disulfide, magnesium hydroxide, talc, sellaite, metallic powder and metallic fiber. Examples of the organic fillers include fibrous materials of wholly aromatic polyamides such as polyterephthaloyl-p-phenylenediamine, polyterephthaloylisophthaloyl-p-phenylenediamine, polyisophthaloyl-p-phenylenediamine and polyisophthaloyl-m-phenylenediamine, or fibrous materials of polyamides such as nylon 66, nylon 6 and nylon 10. The fibrous materials may be in any form of single fiber, strand, cloth or mat. These inorganic or organic fillers may be used either alone or in combination of two or more of them. The inorganic or organic fillers are incorporated into the cycloolefin type random copolymer compositions for various purposes. For example, they are used for purposes of improving the heat resistance or flame retardance of the compositions, coloring said compositions, improving their rigidity, or inhibiting mold shrinkage factor. They are used in an appropriate amount which meets requirements according to the intended uses of the compositions. In the second cycloolefin type random copolymer compositions of the present invention, the total amount of the non-rigid copolymer (B) is preferably 5 to 100 parts by weight, more preferably 5 to 50 parts by weight based on 100 parts by weight of the cycloolefin type random copolymer (A) and the amount of the inorganic or organic filler (C) is preferably 5 to 100 parts by weight, more prefeably 5 to 50 parts by weight based on 100 parts by weight of the cycloolefin type random copolymer (A). Impact resistance is lowered, when the total amount of the non-rigid copolymer (B) is less than one part by weight based on 100 parts by weight of the cycloolefin type random copolymer (A), while rigidity is lowered, when the total amount of the non-rigid copolymer (B) is more than 100 parts by weight. The moldability of the compositions is reduced, when the amount of the inorganic or organic filler (C) is more than 100 parts by weight based on 100 parts by weight of the cycloolefin type copolymer (A). Methods for preparing the cycloolefin type random copolymers (A) and (B)(i) are described in JP-Al168708/1985, JP-A-120816/1986, JP-A-115912/1986, JP-A-115916/1986, JP-A-95905/1986, JP-A-95906/1986, JP-A-271308/1986 and JP-A-272216/1986. Suitable processes for preparing the cyloolefin type random copolymer compositions of the present invention include, for example, a process wherein the cycloolefin type random copolymers (A) and the non-rigid copolymers (B) are prepared separately, and the copolymers (A) and (B) thus prepared are blended by means of an extruder to obtain a desired composition, a solution blending process wherein the copolymers (A) and (B) are thoroughly dissolved separately in suitable solvents, for example, saturated hydrocarbons such as heptane, hexane, decane and cyclohexane, or aromatic hydrocarbons such as toluene, benzene and xylene, and the respective solutions are subjected to solution blending to obtain a desired composition, or a process wherein the copolymers (A) and (B) are prepared individually by means of separate polymerization reactors, and the resulting polymers are blended with a third vessel to obtain a desired composition. An intrinsic viscosity [η] as measured at 135°C in decalin of the cycloolefin type random copolymer compositions of the present invention is in the range of 0.05-10 dl/g, preferably 0.2-3 dl/g, and a softening temperature (TMA) as measured with a thermal mechanical analyzer of said compositions is in the range of 80-250 °C, preferably 100-200°C, and a glass transition temperature (Tg) of said compositions is in the range of 70-230°C, preferably 90-210°C. The cycloolefin type random copolymer compositions contain the aforesaid cycloolefin type copolymer (A) and the aforesaid non-rigid copolymer (B), and optionally said inorganic or organic filler. In addition to the above-mentioned components, however, the present compositions may be incorporated with heat stabilizers, weathering stabilizers, antistatic agents, slip agents, anti-blocking agents, anti-fogging agents, lubricants, dyes, pigments, natural oil, synthetic oil or wax. For instance, the stabilizers which may be optionally incorporated include, for example, phenolic antioxidants such as tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate] methane, β-(3,5-di-t-butyl-4-hydroxyphenyl)propionic acid alkyl ester and 2,2'-oxamidobis[ethyl-3-(3,5-di-t-butyl-4-hydroxyphenyl)] propionate, metallic salts of fatty acid such as zinc stearate, calcium stearate and calcium 12-hydroxystearate, and fatty esters of polyhydric alcohol such as glycerin monostearate, glycerin monolaurate, glycerin distearate, pentaerythritol distearate and pentaerythritol tristearate. These compounds may be incorporated into the present compositions either singly or in combination. For instance, there may be used such a combination of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate] methane with zinc stearate or glycerin monostearate. The present invention is illustrated below in more detail with reference to examples. Various physical properties indicated in the examples were measured or evaluated according to the following procedures. (1) Softening temperature (TMA): Using Thermomechanical Analyser TMA 10 (manufactured by Seiko Denshi K.K.), the softening temperature was measured in terms of heat deformation behavior of a test sheet of a 1 mm thick. That is, to a quartz needle placed vertically on the test sheet was applied a load of 50 g, while elevating the temperature at a rate of 5°C/min of the test sheet, and an elevated temperature at which the needle penetrated 0.1 mm into the test sheet was taken as the softening temperature (TMA). (2) Impact strength: Using Izod impact tester (manufactured by Toyo Seiki KK), a test piece (length: 63.8 mm, width: 12.7 mm) punched out of a 2 mm thick pressed sheet and notched (0.25 mm®) was tasted at 23°C. (3) Modulus of rigidity (flexural modulus): Using Instron tensile tester, a test piece (length: 63.8 mm, width: 12.7 mm) punched out of a 2 mm thick pressed sheet was tasted under conditions including a compression rate of 5 mm/min, a distance between supports of 32 mm and a temperature of 23°C. The IZ impact test and the flexural test were conducted after 3 days from pressing. Polymerization Example 1a Preparation of copolymer (A) having a softening temperature of at least 70°C With a 2-litre glass polymerization reactor equipped with a stirring blade, there was carried out continuously a copolymerization reaction between ethylene and 1,4,5,8-dimethano-1,2,3,4,4a,5,8,8a-octahydronaphthalene (structural formula: hereinafter abbreviated to DMON). That is, into the polymerization reactor were continuously charged a solution of DMON in cyclohexane so that the DMON concentration in the polymerization reactor became 60 g/l, a solution of VO(OC₂H₅)Cl₂ as a catalyst in cyclohexane so that the vanadium concentration in the polymerization reactor became 0.9 mmol/l, and a solution of ethylaluminum sesquichloride (Al(C₂H₅) 1.5 Cl 1.5 ) in cyclohexane so that the aluminum concentration in the polymerization reactor became 7.2 mmol/l, while continuously withdrawing from the bottom of the polymerization reactor the polymerization liquid so that the volume of the polymerization liquid in the polymerization reactor was constantly 1 litre. Simultaneously, into the polymerization reactor from the top of the polymerization reactor ethylene was fed at a rate of 85 l/h, hydrogen was fed at a rate of 6 l/hr and nitrogen was fed at a rate of 45 l/h. The copolymerization reaction was carried out at 10°C by circulating a refrigerant through a jacket fitted externally to the polymerization reactor. The copolymerization was carried out under the conditions as illustrated above, whereupon a polymerization reaction mixture containing an ethylene DMON random copolymer was obtained. The polymerization reaction was stopped by adding a small amount of isopropyl alcohol to the polymerization liquid withdrawn from the bottom of the reactor. Thereafter, the polymerization liquid was poured into a household mixer containing acetone of about three times the volume of the polymerization liquid, while rotating the mixer, thereby depositing the resulting copolymer. The deposited copolymer was collected by filtration, dispersed in acetone so that the polymer concentration became about 50 g/l, and the copolymer was treated at the boiling point of acetone for 2 hours. After the treatment as above, the copolymer was collected by filtration and dried at 120°C overnight (12 hours) under reduced pressure. The thus obtained ethylene DMON-random copolymer (A) had an ethylene unit of 59 mol% as measured by ¹³C-NMR analysis, an intrinsic viscosity [η] of 0.42 dl/g as measured at 135°C in decalin, and a softening temperature (TMA) of 154°C. Polymerization Example 1b Preparation of copolymer (A) having a softening temperature of at least 70°C In Example 1b, a copolymerization reaction was continuously carried out in the same manner as in Example la. After the completion of the copolymerization reaction, the resulting copolymer was precipitated out, recovered and dried at 120°C overnight under reduced pressure. The thus obtained ethylene DMON copolymer (A) had an ethylene unit of 59 mol% as measured by 13C-NMR analysis, an intrinsic viscosity [η] of 0.60 dl/g as measured at 135°C in decalin and a softening temperature (TMA) of 111°C. Polymerization Example 2 Preparation of copolymer (A) having an intrinsic viscosity [η] different from that of the copolymer (A) of Polymerization Example 1a The same copolymerization reaction as in Polymerization Example 1a was continuously carried out except that the concentrations of DMON, VO(OC₂H₅)Cl₂ and ethylaluminum sesquichloride in the polymerization reactor and the feed rates of ethylene, hydrogen and nitrogen were those given in Table 5. After the completion of the copolymerization, the resulting copolymer was deposited, recovered and dried at 120°C under reduced pressure for 12 hours as in polymerization Example 1a. The thus obtained ethylene DMON copolymer (A) had an ethylene unit of 58 mol% as measured by ¹³C-NMR analysis, an intrinsic viscosity [η] of 0.94 dl/g as measured at 135°C in decalin and softening temperature of 170°C. Polymerization Example 3 Preparation of copolymer (A) having an intrinsic viscosity [η] different from that of the copolymer (A) of Polymerization Example 1a The same copolymerization reaction as in Polymerization Example 1a was continuously carried out except that the concentrations of DMON, VO(OC₂H₅)Cl₂ and ethylaluminum sesquichloride in the polymerization reactor and the feed rates of ethylene, hydrogen and nitrogen were those given in Table 5. After the completion of the copolymerization, the resulting copolymer was deposited, recovered and dried at 120°C overnight (12 hours) under reduced pressure as in polymerization Example 1a. The thus obtained ethylene DMON copolymer (A) had an ethylene unit of 67 mol% as measured by ¹³C-NMR analysis, an intrinsic viscosity [η] of 0.60 dl/g as measured at 135°C in decalin and a softening temperature (TMA) of 111°C. Polymn. Ex. 2 Polymn. Ex. 3 VO(DC₂H₅)Cl₂ (mmol/l) 0.9 0.9 Ethylaluminum sesquichloride (mmol/l) 7.2 7.2 DMON (g/l) 60 30 Ethylene (l/h) 100 85 Hydrogen (l/h) 0.2 0.2 Nitrogen (l/h) 45 45 Polymerization Example 4 Preparation of copolymer (B) having a softening temperature of below 70°C The same copolymerization reaction as in Polymerization Example 1a was carried out except that DMON, VO(OC₂H₅)Cl₂ and ethylaluminum sesquichloride were fed into the polymerization reactor so that the concentrations of DMON, VO(OC₂H₅)Cl₂ and ethylaluminum sesquichloride in the polymerization reactor became 15 g/l, 0.5 mmol/l and 4 mmol/l, respectively, and that ethylene, propylene, hydrogen and nitrogen were fed into the polymerization reactor at rates of 45 l/hr, 15 l/hr, 0.2 l/hr and 25 l/hr, respectively, and the polymerization temperature was 10°C. After the completion of the copolymerization, the resulting copolymer was deposited, collected and dried at 120°C under reduced pressure for 12 hours as in polymerization Example 1a. The thus-obtained ethylene propylene DMON copolymer (B) had an ethylene unit of 76 mol% and a propylene unit of 17 mol% as measured by ¹³C-NMR analysis, an intrinsic viscosity [η] of 0.89 dl/g as measured at 135°C in decalin and a softening temperature (TMA) of -10°C. Polymerization Example 5 Preparation of copolymer (B) having an intrinsic viscosity [η] different from that of the copolymer (B) of Polymerization Example 4 The same copolymerization reaction as in Example 4 was carried out except that the concentrations of DMON, VO(OC₂H₅)Cl₂ and ethylaluminum sesquichloride in the polymerization reactor and the feed rates of ethylene, propylene, hydrogen and nitrogen were those given in Table 6. After the completion of the copolymerization, the resulting copolymer was deposited, collected and dried at 120°C under reduced pressure for 12 hours as in Polymerization Example 1a. The thus obtained ethylene propylene DMON copolymer (B) had an ethylene unit of 69 mol% and a propylene unit of 21 mol% as measured by ¹³C-NMR analysis, an intrinsic viscosity [η] of 1.44 dl/g as measured at 135°C, in decalin and a softening temperature (TMA) of - 4°C. Polymerization Example 6 Preparation of copolymer (B) having an intrinsic viscosity [η] different from that of the copolymer (B) of Polymerization Example 4 The same copolymerization reaction as in Polymerization Example 4 was carried out except that the concentrations of DMON, VO(OC₂H₅)Cl₂ and ethylaluminum sesquichloride in the polymerization reactor and the feed rates of ethylene, propylene, hydrogen and nitrogen were those given in Table 6. After the completion of the copolymerization, the resulting copolymer was deposited, collected and dried at 120°C under reduced pressure for 12 hours as in Polymerization Example 1a. The thus obtained ethylene propylene DMON copolymer (B) had an ethylene unit of 76 mol% and a propylene unit of 16 mol% as measured by ¹³C-NMR analysis, an intrinsic viscosity [η] of 0.98 dl/g as measured at 135°C in decalin and a softening temperature (TMA) of -8°C. Polymn. Ex. 5 Polymn. Ex. 6 VO(DC₂H₅)Cl₂ (mmol/l) 0.5 0.5 Ethylaluminum sesquichloride (mmol/l) 4 4 DMON (g/l) 20 15 Ethylene (l/h) 45 45 Propylene (l/h) 30 15 Hydrogen (l/h) 0.1 0.1 Nitrogen (l/h) 25 25 Example 1 In 2 litres of cyclohexane were poured 85 g of the copolymer (A) obtained in Polymerization Example 3 and 15 g of the copolymer (B) obtained in Polymerization Example 5 (weight ratio: (A)/(B) = 85/15), and dissolved at about 70°C while thoroughly stirring to obtain a homogeneous solution. The thus obtained homogeneous solution was poured in 2 litres of acetone to deposit an (A)/(B) blend. The thus obtained blend was dried at 120°C under reduced pressure overnight. The (A)/(B) blend thus obtained was incorporated with 0.5%, based on the total weight of the resins [A] and [B], of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate] methane as stabilizer. The resulting blend was kneaded at 190°C by using Brabender Plastograph and compression molded at 240°C to obtain a pressed sheet of 2 mm in thickness. Test pieces were punched out of the sheet, and impact test, flexural test and TMA measurement were carried out. It was found that the blend had an Izod impact strength of 40.0 kg.cm/cm, flexural modulus of 22100 kg/cm², stress at flexural yield point of 830 kg/cm² and a TMA of 108°C. There could be obtained a blend excellent in rigidity and heat resistance as well as in impact strength. Comparative Example 1 The copolymer (A) prepared in Polymerization Example 3 was compression-molded at 240°C to obtain a pressed sheet of 2 mm in thickness. Test pieces punched out of the sheet were subjected to impact test, flexural test and TMA measurement in the same manner as in Example 1. The sample was found to have an Izod impact strength of 2.0 kg.cm/cm, a flexural modulus of 28900 kg/cm², stress at flexural yield point of 870 kg/cm² and a TMA of 110°C. Therefore, the sample was low in impact resistance and brittle, though it was excellent in rigidity and heat resistance. Examples 2 to 4 The copolymers (A) prepared in Polymerization Examples 1a and 3 were blended with the copolymers (B) prepared in Polymerization Examples 4 and 5 as in Example 1 in weight ratios indicated in Table 7 and evaluated in the same manner as in Example 1. The results are shown in Table 7. Comparative Examples 2 and 3 The copolymers (A) prepared in Polymerization Examples 1a and 2 were evaluated in the same manner as in Comparative Example 1. The results are shown in Table 7. The samples were low in impact resistance and brittle, though the samples were excellent in rigidity and heat resistance. Example 5 A blend composed of 80 g of the copolymer (A) prepared in Polymerization Example 2 and 20 g of the copolymer (B) prepared in Polymerization Example 6 (weight ratio: (A)/(B) = 80/20) was incorporated with 0.5%, based on the total weight of the resins (A) and (B), of tetrakis-[methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate] methane as stabilizer. The blend was kneaded at 190°C by using Brabender Plastograph and evaluated in the same manner as in Example 1. The results are shown in Table 7. There could be obtained a composition excellent in rigidity and heat resistance as well as in impact resistance. Examples 6 and 7 The copolymer (A) prepared in Polymerization Example 2 was blended with the copolymer (B) prepared in Polymerization Example 6 in the manner as in Example 5 in weight ratios indicated in Table 7, and evaluated in the manner as in Example 5. The results are shown in Table 7. Examples 8 to 15 Copolymers (A) indicated in Table 8 which had been prepared substantially following the procedure of Polymerization Example 1a were blended with copolymers (B) indicated in Table 8 which had been prepared substantially following the procedure of Polymerization Example 4 in the following the procedure of Polymerization Example 4 in the manner as in Example 5 in weight ratios indicated in Table 8, and evaluated in the manner as in Example 5. Comparative Examples 4 to 6 Copolymers (A) indicated in Table 9 which had been prepared substantially following the procedure of Polymerization Example la were tested as in Comparative Example 1. The results are shown in Table 9. The samples were low in impact resistance and brittle, though they were excellent in rigidity and heat resistance. Example 16 90 g of the copolymer (A) prepared in Polymerization Example 3 and 10 g of an ethylene-propylene random copolymer (B) (ethylene/propylene = 80/20 mol%) (weight ratio: (A)/(B) = 90/10) were poured in two litres of cyclohexane and dissolved at about 70°C while thoroughly stirring. The resulting homogeneous solution was poured in two litres of acetone to deposit an (A)/(B) blend. The thus obtained blend was dried at 120°C under reduced pressure overnight. The (A)/(B) blend was incorporated with 0.5%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate] methane as stabilizer. The blend was kneaded at 190°C by using Brabender Plastograph and compression-molded at 240°C to obtain a pressed sheet of 2 mm in thickness. Test pieces were punched out of the sheet and subjected to impact test, flexural test and TMA measurement. The blend was found to have an Izod impact strength of 9.4 kg.cm/cm, a flexural modulas of 23000 kg/cm², a stress at flexural yield point of 840 kg/cm² and a TMA of 110°C. There was obtained a blend excellent in rigidity and heat resistance as well as in impact strength. Comparative Example 7 The copolymer (A) prepared in Polymerization Example 3 was compression-molded at 240°C to obtain a pressed sheet of 2 mm in thickness. Test pieces punched out of the sheet were tested in the same manner as in Example 16. The test pieces were found to have an Izod impact strength of 2.0 kg.cm/cm, a flexural modulus of 28900 kg/cm², stress at flexural yield point of 870 kg/cm² and a TMA of 110°C. Hence, the sample was low im impact strength and brittle, though it was excellent in rigidity and heat resistance. Examples 17 and 18 The copolymer (A) prepared in Polymerization Example 3 and the ethylene propylene copolymer (B) were processed and evaluated as in Example 16 except that the copolymers were blended in weight ratios indicated in Tabel 10. The results are shown in Table 10. There could be obtained compositions excellent in rigidity and heat resistance as well as in impact resistance. Example 19 The polymer (A) prepared in Polymerization Example 3 and an ethylene-1-butene copolymer (B) indicated in Table 10 were blended together in a weight ratio given in Table 10, processed and evaluated in the same manner as in Example 16. The results are shown in Table 10. There could be obtained a composition excellent in rigidity and heat resistance as well as high in impact resistance. Example 20 A blend of 80 g of the copolymer (A) prepared in Polymerization Example 3 and 20 g of an ethylene-1-butene copolymer (B) indicated in Table 10 (weight ratio: (A)/(B) = 80/20) was incorporated with 0.5%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate] methane as stabilizer. The blend was kneaded at 190°C by using Brabender Plastograph and evaluated in the same manner as in Example 16. The results are shown in Table 10. There could be obtained a composition excellent in rigidity and heat resistance as well as in impact resistance. Comparative Example 8 The copolymer (A) prepared in Polymerization Example 2 was compression-molded at 240°C to obtain a pressed sheet of 2 mm in thickness. The evaluation thereof was made in the same manner as in Example 16. The results are shown in Table 10. The test sample was found to be low in impact resistance and to be brittle, though it was excellent in rigidity and heat resistance. Examples 21 and 23 Blends of the copolymer (A) prepared in polymerization Example 2 and an ethylene propylene copolymer (B) indicated in Table 10 in weight ratios given in Table 10 were processed and evaluated in the same manner as in Example 16. The results are shown in Table 10. There could be obtained compositions excellent in rigidity and heat resistance as well as high in impact resistance. Examples 24, 25, 28 and 29 Copolymers (A) indicated in Table 11 which had been prepared substantially following the procedure of Polymerization Example 2 and α-olefin type random copolymers indicated in Table 11 were blended in the manner as in Example 20 in weight rations indicated in Table 11, and evaluated in the manner as in Example 20. Comparative Examples 9 to 11 Copolymers indicated in Table 12 which had been prepared substantially following the procedure of Polymerization Example 2 were tested as in Comparative Example 7. The results are shown in Table 12. Samples were found to be low in impact strength and to be brittle, though they were excellent in rigidity and heat resistance. Example 30 90% by weight of the ethylene polycyclic olefin copolymer obtained in Polymerization Example la was mixed with 10% by weight of an ethylene propylene random copolymer (hereinafter abbreviated to EPC-I) having a crystallinity index of 5% as measured by X-rays, an ethylene content of 80 mol%, an MFR of 4.6 g/10 min and a density of 0.865 g/cm³ in Henshel mixer. The mixture was melt-kneaded and extruded by means of a 40 mm single screw extruder (preset temperature: 230°C), and pelletized. The pellets were injection-molded (cylinder temperature: 240°C, mold temperature: 70°C) to obtain test pieces for use in the evaluation of physical properties. The thus obtained test pieces were subjected to a flexural test (ASTM D 790) and an Izod impact test (ASTM D 256, not notched). The results are shown in Table 13. Example 31 The procedure of Example 30 was repeated except that 70% by weight of the ethylene polycyclic olefin copolymer and 30% by weight of EPC-I were used. In the same way as in Example 30, test pieces for the evaluation of the physical properties were obtained and the flexural test and the Izod impact test were conducted. The results are shown in Table 13. Example 32 The procedure of Example 30 was repeated except that an ethylene 1-butene random copolymer having a crystallinity index of 25% as measured by X-rays, an ethylene content of 92 mol%, an MFR of 18 g/10 min and a density of 0.895 g/cm³ was used in place of EPC-I. In the same way as in Example 30 test pieces for the evaluation of physical properties were prepared and the flexural test and the Izod impact test were conducted. The results are shown in Table 13. Example 33 The procedure of Example 30 was repeated except that an ethylene propylene random copolymer having a crystallinity index of 1% as measured by X-rays, an ethylene content of 40 mol%, an MFR of 1.0 g/10 min and a density of 0.858 g/cm³ was used in place of EPC-I. In the same way as in Example 30 test pieces for the evaluation of physical properties were prepared and the flexural test and the Izod impact test were conducted. The results are shown in Table 13. Example 34 The procedure of Example 30 was repeated except that a modified ethylene 1-butene random copolymer (crystallinity index as measured by X-rays; 15%, MFR: 5 g/10 min) obtained by graft-copolymerizing 0.5 parts by weight of maleic anhydride onto 100 parts by weight of an ethylene 1-butene random copolymer having a crystallinity index of 17% as measured by X-rays, an ethylene content of 89 mol%, an MFR of 4.0 g/10 min and a density of 0.885 g/cm³ was used in place of EPC-I. In the same way as in Example 30 test pieces for the evaluation of physical properties were prepared and the flexural test and the Izod impact test were conducted. The results are shown in Table 13. Comparative Example 12 The procedure of Example 30 was repeated except that only the ethylene polycyclic olefin copolymer was used in place of the composition of Example 30 and injection-molded to prepare test pieces. The flexural test and the Izod impact test were conducted. The results are shown in Table 13. Example 35 80 g of the copolymer (A) obtained in polymerization Example 3 and 20 g of an ethylene propylene 2-ethylidene-2-norbornene random copolymer (B) (ethylene/propylene/diene = 66/31/3 mol%) (weight ratio: (A)/(B) = 80/20) were poured in 2 litres of cyclohexane and dissolved at about 70°C while thoroughly stirring. The resulting homogeneous solution was poured in 2 litres of acetone to deposit an (A)/(B) blend. The blend was dried at 120°C under reduced pressure overnight. The thus obtained (A)/(B) blend was incorporated with 0.5%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate] methane as stabilizer. The blend was then kneaded at 190°C by using Brabender Plastograph and compression-molded at 240°C to obtain a pressed sheet of 2 mm in thickness. Test pieces were punched out of the sheet and impact test, flexural test and TMA measurement were conducted. The blend was found to have an Izod impact strength of 53.4 kg.cm/cm, a flexural modulus of 16000 kg/cm², stress at flexural yield point of 590 kg/cm² and a TMA of 110°C. Hence, there could be obtained a blend excellent in rigidity and heat resistance as well as in impact strength. Comparative Example 13 The copolymer (A) prepared in Polymerization Example 3 was compression-molded at 240°C to obtain a pressed sheet of 2 mm in thickness. In the same way as in Example 35, test pieces were punched out of the sheet and tests were conducted. The test pieces were found to have an Izod impact strength of 2.0 kg.cm/cm, a flexural modulus of 28900 kg/cm², stress at flexural yield point of 870 kg/cm² and a TMA of 111°C. Hence, the sample was found to be low in impact resistance and to be brittle, though it was excellent in rigidity and heat resistance. Examples 36 and 37 Blends of the copolymer (A) prepared in Polymerization Example 3 and the ethylene propylene 5-ethylidene-2-norbornene random copolymer (B) (ethylene/ propylene/ diene = 66/31/3 mol% ) in weight ratios given in Table 14 were processed and evaluated in the same manner as in Example 35. The results are shown in Table 14. There could be obtained compositions excellent in rigidity and heat resistance as well as in impact resistance. Examples 38 to 39 Blends of the copolymer (A) obtained in Polymerization Example 3 and an ethylene propylene 5-ethylidene-2-norbornene random copolymer (B) (ethylene/ propylene/ diene = 67/31/2 mol% ) in weight ratios given in Table 14 were processed and evaluated in the same manner as in Example 35. The results are shown in Table 14. There could be obtained compositions excellent in rigidity and heat resistance as well as high in impact resistance. Examples 40 and 41 Blends of the copolymer (A) prepared in Polymerization Example 3 and an ethylene propylene dicyclopentadiene random copolymer (B) (ethylene/ propylene/ diene = 67/32/1 mol%), in weight rations indicated in Table 14 were processed and evaluated in the same manner as in Example 35. The results are shown in Table 14. Example 42 A blend of 80 g of the copolymer (A) prepared in Polymerization Example 2 and 20 g of the ethylene propylene 5-ethylidene-2-norbornene random copolymer (B) (ethylene/propylene/diene = 66/31/3 mol%) (weight ratio : (A)/(B) = 80/20) was incorporated with 0.5%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate] methane as stabilizer. The blend was kneaded at 190°C by using Brabender Plastograph and evaluated in the same manner as in Example 35. The results are shown in Table 14. There could be obtained a composition excellent in rigidity and heat resistance as well as in impact resistance. Comparative Example 14 The copolymer (A) prepared in polymerization Example 2 was compression-molded at 240°C to obtain a pressed sheet of 2 mm in thickness. In the same way as in Example 35, test pieces were prepared, evaluated and found to be low in impact strength and to be brittle, though they were excellent in rigidity and heat resistance. Examples 43 and 44 The copolymer (A) prepared in Polymerization Example 2 was blended with α-olefin diene copolymers (B) given in Table 14 in the same manner as in Example 42. The evaluation of the blends was made. The results are shown in Table 14. Examples 45 to 50 Blends of copolymers (A) indicated in Table 15 and α-olefin-diene elastomers (B) indicated in Table 15 were processed and evaluated in the same way as in Example 42. The results are shown in Table 15. There could be obtained compositions excellent in rigidity and heat resistance as well as in impact resistance. Comparative Examples 15 to 17 Copolymers (A) indicated in Table 16 were processed and evaluated in the same way as in Comparative Example 14. The results are shown in Table 16. Comparative Example 17a A dry blend of 90 g of the copolymer (A) obtained in Polymerization Example 3 and 10 g of a styrene-butadiene-styrene block copolymer (B) (density: 0.94 g/cm³, Cariflex TR1102, a product of Shell Kagaku KK) (weight ratio: (A)/(B) = 90/10) was incorporated with 0.5% and 0.3%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate] methane and dilauryl thiodipropionate as stabilizers, respectively. The resulting blend was kneaded at 190°C by using Brabender Plastograph and compression-molded at 240°C to prepare pressed sheets of 1 mm in thickness and a pressed sheet of 2 mm in thickness, respectively. Test pieces were punched out of these sheets and impact test, flexural test and TMA measurement were conducted. The blend was found to have an Izod impact strength of 5.0 kg.cm/cm, a flexural modulus of 23000 kg/cm² and a TMA of 111°C. Hence, there could be obtained a blend excellent in rigidity and heat resistance as well as in impact strength. Comparative Example 18 The copolymer (A) prepared in Polymerization Example 3 was compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Tests were conducted in the same way as in Comparative Example 17a. The sample was found to have an Izod impact strength of 2.0 kg.cm/cm, a flexural modulus of 28900 kg/cm², a stress at flexural yield point of 870 kg/cm² and a TMA of 111°C. Therefore, it was found that the sample was low in impact resistance and brittle, though it was excellent in rigidity and heat resistance. Example 54 The evaluation of a blend of the copolymer (A) obtained in Polymerization Example 3 and a hydrogenated styrene-butadiene-styrene block copolymer (B) (density: 0.90 g/cm³, Clayton G1657, a product of Shell Kagaku KK) (weight ratio of (A)/(B) being given in Table 17) was made in the same manner as in Comparative Example 17a. The results are shown in Table 17. There could be obtained a composition excellent in rigidity and heat resistance as well as in impact resistance. Comparative Example 19 The copolymer (A) prepared in Polymerization Example 2 was compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces obtained from the sheets were tested. The results are shown in Table 17. The sheets were found to be low in impact resistance and to be brittle, though they were excellent in rigidity and heat resistance. Examples 59 and 60 The evaluation of blends of the copolymer (A) prepared in Polymerization Example 2 and a hydrogenated styrene-butadiene-styrene block copolymer (B) (density: 0.90 g/cm³ , Clayton G 1657, a product of Shell Kagaku KK) in weight ratios of (A)/(B) given in Table 17 was conducted in the same manner as in Comparative Example 17a. The results are shown in Table 17. There could be obtained compositions excellent in rigidity and heat resistance as well as in impact resistance. Comparative Examples 20 to 22 The evaluation of copolymers (A) (composition being given in Table 17) prepared substantially following the procedure of polymerization Example 1b was conducted in the same way as in Comparative Example 19. The results are shown in Table 17. Example 67 A dry blend of 40 g of the copolymer (A) obtained in Polymerization Example 1b, 5 g of the cycloolefin type random copolymer prepared in Polymerization Example 5 (hereinafter abbreviated to TDR) (B1) and 5 g of ethylene-propylene random copolymer (hereinafter abbreviated to EPR) (B2) containing 80 mol% of ethylene units and having a crystallinity index of 15%, a density of 0.88 g/cm³ and an intrinsic viscosity [η] of 2.2 dl/g (weight ratio = 80/10/10) was incorporated with 0.5% and 0.3%, based on the total weight of the resins (A) and (B), of tetrakis[methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate]methane and dilauryl thiodipropionate, respectively. The blend was kneaded at 190°C by using Brabender Plastograph and compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were punched out of these sheets and impact test, flexural test and TMA measurement were conducted. The blend was found to have an Izod impact strength of 40.2 kg.cm/cm, a flexural modulus of 19000 kg/cm² and a TMA of 110°C. There could be obtained a blend excellent in rigidity and heat resistance as well as in impact strength. Comparative Example 23 The copolymer (A) prepared in Polymerization Example 3 was compression-molded at 240° C to prepare pressed sheets of 1 mm and 2 mm in thickness. The sheets were tested in the same manner as in Example 67. The sample was found to have an IZ impact strength of 2.0 kg.cm/cm, a flexural modulus of 28900 kg/cm², stress at flexural yield point of 870 kg/cm² and a TMA of 110°C. The sample was found to be low in impact resistance and to be brittle, though it was excellent in rigidity and heat resistance. Example 68 The evaluation of a blend of the copolymer (A) obtained in Polymerization Example 3, TDR (B1) and a styrene-butadiene-styrene block copolymer (hereinafter abbreviated to SBS) (B2) (density: 0.94 g/cm² , Cariflex TR1102, a product of Shell Kagaku KK) (weight ratio being given in Table 18) was conducted in the same manner as in Example 67. The results are shown in Table 18. There could be obtained a composition excellent in rigidity and heat resistance as well as high in impact resistance. Example 69 The evaluation of a blend of the copolymer (A) prepared in Polymerization Example 3, an ethylene-propylene-diene copolymer (hereinafter abbreviated to EPDM) (B2) (ethylene/propylene/5-ethylidene-2-norbornene = 66/31/3 mol%, [η] = 2.1 dl/g, iodine value : 22, density : 0.87 g/cm²) was conducted in the same manner as in Example 67, the weight ratio of (A)/(B1)/(B2) being given in Table 18. The results are shown in Table 18. The results are shown in Table 18. There could be obtained a composition excellent in rigidity and heat resistance as well as in impact resistance. Examples 70 to 72 The evaluation of blends of the copolymer (A) prepared in Polymerization Example 3, EPR (B1) and SBS (B2) in weight ratios given in Table 18 was conducted in the same manner as in Example 67. There could be obtained compositions excellent in rigidity and heat resistance as well as in impact strength. Examples 73 to 77 The evaluation of blends of the copolymer (A) prepared in Polymerization Example 2, EPDM (B1) and SBS (B2) in weight ratios given in Table 18 was conducted in the same manner as in Example 67. The results are shown in Table 18. There were obtained compositions excellent in rigidity and heat resistance as well as in impact strength. Comparative Example 24 The evaluation of the copolymer (A) prepared in Polymerization Example 2 was made in the same manner as in Comparative Example 23. The results are shown in Table 18. The sample was found to be low in impact resistance and to be brittle, though it was excellent in rigidity and heat resistance. Examples 78 to 80 The evaluation of blends of a copolymer (A) indicated in Table 18 which had been prepared substantially following the procedure of Polymerization Example 1b, EPR (B1) and EPDM (B2) in weight ratios given in Table 18 was conducted in the same manner as in Example 67. The results are shown in Table 18. There were obtained compositions excellent in rigidity and heat resistance as well as high in impact resistance. Examples 81 and 82 The evaluation of blends of a copolymer (A) indicated in Table 18 which had been prepared substantially following the procedure of Polymerization Example 1b, EPDM (B1) and SBS (B2) in weight ratios given in Table 18 was conducted in the same way as in Example 67. The results are shown in Table 18. There were obtained compositions excellent in rigidity and heat resistance as well as high in impact resistance. Examples 83 and 84 The evaluation of blends of a copolymer (A) indicated in Table 18 which had been prepared substantially following the procedure of Polymerization Example 1b, TDR (B1) and SBS (B2) in weight ratios given in Table 18 was conducted in the same way as in Example 67. The results are shown in Table 18. There were obtained compositions excellent in rigidity and heat resistance as well as high in impact resistance. Comparative Examples 25 to 27 The evaluation of copolymers (A) indicated in Table 18 which had been prepared substantially following the procedure of Polymerization Example 1b was conducted in the same manner as in Comparative Example 23. The results are shown in Table 18. They were found to be low in impact strength and to be brittle, though they were excellent in rigidity and heat resistance. In the following examples, (1) Asahi Fiber Glass glass roving chopped strand GR-S-3A (GF) or (2) Fujimi white alumina #4000 (WA) was used as the filler (C). Example 85 The copolymer (A) prepared in Polymerization Example 3 was dry-blended with a copolymer (B) given in Table 19, prepared substantially following the procedure of Polymerization Example 3 in a weight ratio of 80/10. The dry blend was incorporated with 0.5% and 0.3%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate]methane and dilauryl thiodipropionate as stabilizers, respectively. The dry blend was kneaded at 220°C in a 30 mm twin-screw extruder and dry-blended with 10% by weight, based on the total amount of the resins (A) and (B), of GF. The resulting blend was kneaded at 220°C in a 30 mm twin-screw extruder and compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were punched out of these sheets and subjected to impact test, flexural test and TMA measurement. The blend was found to have a notched Izod impact strength of 6 kg.cm/cm, an initial flexural modulus of 31000 kg/cm² and a TMA of 113°C. There was obtained a blend excellent in rigidity, heat resistance and impact strength. Comparative Example 28 The copolymer (A) obtained in Polymerization Example 3 was compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were prepared from these sheets and subjected to impact test, flexural test and TMA measurement. The test pieces were found to have a notched Izod impact strength of 2 kg.cm/cm, an initial flexural modulus of 28900 kg/cm² and a TMA of 111°C. Therefore, the sample was inferior in impact strength, initial flexural modulus and heat resistance as compared with the blend of Example 85. Examples 86 and 87 The evaluation of blends of copolymers (A) and (B) and filler(C) given in Table 19 in blending ratios given in Table 19 was conducted in the same manner as in Example 85. The results are shown in Table 19. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Examples 88 to 90 The evaluation of blends of copolymers (A) and (B) and filler(C) given in Table 19 in blending ratios given in Table 19 was conducted in the same manner as in Example 85. The results are shown in Table 19. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Comparative Example 29 The evaluation of the copolymer (A) given in Table 19 was conducted in the same manner as in Comparative Example 28. The results are shown in Table 19. The sample was inferior to the blends of Examples 88 to 90 in rigidity, heat resistance and impact strength. Examples 91 to 93 The evaluation of blends of copolymers (A) and (B) and filler (C) given in Table 19 in blending ratios given in Table 19 was conducted in the same manner as in Example 85. The results are shown in Table 19. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Comparative Example 30 The evaluation of the copolymer (A) given in Table 19 was conducted in the same manner as in Comparative Example 28. The results are shown in Table 19. The sample was inferior to the compositions of Examples 91 to 93 in rigidity, heat resistance and impact strength. Example 94 The copolymer (A) obtained in Polymerization Example 3 was dry-blended with an ethylene propylene random copolymer (B) (ethylene/propylene = 80/20 mol%) in a weight ratio of 80/10. The dry blend was incorporated with 0.5% and 0.3%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate] methane and dilauryl thiodipropionate as stabilizers, respectively. The resulting blend was kneaded at 220°C in a 30 mm twin-screw extruder and dry-blended with 10% by weight, based on the total amount of the resins (A) and (B), of GF. The resulting blend was kneaded at 240°C in a 30 mm twinscrew extruder and compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were prepared from these sheets and subjected to impact test, flexural test and TMA measurement. The blend was found to have a notched Izod impact strength of 7 kg.cm/cm, an initial flexural modulus of 30600 kg/cm² and a TMA of 114°C. There was obtained a blend excellent in rigidity, heat resistance and impact strength. Comparative Example 31 The copolymer (A) prepared in Polymerization Example 3 was compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were cut out of these sheets and subjected to impact test, flexural test and TMA measurement. The test pieces were found to have a notched Izod impact strength of 2 kg.cm/cm, an initial flexural modulus of 28900 kg/cm² and a TMA of 110°C. The sample was inferior to the blend of Example 94 in impact strength, initial flexural modulus and heat resistance. Examples 95 and 96 The evaluation of blends of copolymers (A) and (B) and filler (C) given in Table 20 in blending ratios given in Table 20 was conducted in the same manner as in Example 94. The results are shown in Table 20. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Examples 97 to 99 The evaluation of blends of copolymers (A) and (B) and filler (C) given in Table 20 blending ratios given in Table 20 was conducted in the same manner as in Example 94. The results are shown in Table 20. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Comparative Example 32 The evaluation of copolymer (A) given in Table 20 was conducted in the same manner as in Comparative Example 31. The results are shown in Table 20. The sample was inferior to the blends of Examples 97 to 99 in rigidity, heat resistance and impact strength. Comparative Example 33 The evaluation of copolymer (A) given in Table 20 was conducted in the same manner as in Comparative Example 31. The results are shown in Table 20. The sample was inferior to the blends of Examples 100 to 102 in rigidity, heat resistance and impact strength. Example 103 The copolymer (A) obtained in Polymerization Example 3 was dry-blended with an ethylene propylene 5-ethylidene-2-norbornene random copolymer (B) (ethylene/ propylene/diene = 66/31/3 mol%) in a weight ratio of 80/10. The dry blend was incorporated with 0.5% and 0.3%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl) propionate] methane and dilauryl thiodipropionate as stabilizers, respectively. The resulting blend was dry-blended with 10% by weight, based on the total amount of the resins (A) and (B), of GF. The thus-formed dry blend was kneaded at 220°C in a 30 mm twin-screw extruder and compression molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were cut out from these sheets and subjected to impact test, flexural test and TMA measurement. The blend was found to have a notched Izod impact strength of 8 kg.cm/cm, an initial flexural modulus of 31100 kg/cm² and a TMA of 114°C. There was obtained a blend excellent in rigidity, heat resistance and impact strength. Comparative Example 34 The copolymer (A) obtained in Polymerization Example 3 was compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were prepared from these sheets and subjected to impact test, flexural test and TMA measurement. The sample was found to have a notched Izod impact strength of 2 kg.cm/cm, an initial flexural modulus of 28900 kg/cm² and a TMA of 111°C. The sample was inferior to the blend of Example 103 in rigidity, initial flexural modulus and heat resistance. Examples 104 and 105 The evaluation of blends of copolymers (A) and (B) and filler (C) given in Table 21 in weight ratios given in Table 21 was conducted in the same manner as in Example 103. The results are shown in Table 21. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Examples 106 to 108 The evaluation of blends of copolymers (A) and (B) and filler (C) given in Table 21 in weight ratios given in Table 21 was conducted in the same manner as in Example 103. The results are shown in Table 21. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Comparative Example 35 The evaluation of the copolymer (A) given in Table 21 was conducted in the same manner as in Comparative Example 34. The results are shown in Table 21. The sample was inferior to the compositions of Examples 106 to 108 in rigidity, heat resistance and impact strength. Examples 109 to 111 The evaluation of blends of copolymers (A) and (B) and filler (C) given in Table 21 in blending ratios given in Table 21 was made in the same manner as in Example 103. The results are shown in Table 21. There were obtained compositions excellent in rigidity, heat resistance and impact strength. Comparative Example 36 The evaluation of the copolymer (A) given in Table 21 was conducted in the same manner as in Comparative Example 34. The results are shown in Table 21. The sample was inferior to the compositions of Examples 109 to 111 in rigidity, heat resistance and impact strength. Example 112 The copolymer (A) having the composition shown in Table 22 was dry-blended with a hydrogenated styrene butadiene styrene copolymer (B) (density: 0.90 g/cm³, Clayton G1657, a product of Shell Kagaku KK) in a weight ratio of 80/10. The dry blend was incorporated with 0.5% and 0.3%, based on the total weight of the resins (A) and (B), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)-propionate] methane and dilauryl thiodipropionate as stabilizers, respectively. The resulting blend was kneaded at 220°C in a 30 mm twin-screw extruder and dry-blended with 10% by weight, based on the total amount of the resins (A) and (B), of GF. The thus formed dry blend was then kneaded at 220°C in a 30 mm twin-screw extruder and compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were cut out from these sheets and subjected to impact test, flexural test and TMA measurement. The composition was found to have a notched Izod impact strength of 8 kg.cm/cm, an initial flexural modulus of 31000 kg/cm² and a TMA of 115°C. There was obtained a composition excellent in rigidity, heat resistance and impact strength. Comparative Example 37 The copolymer (A) obtained in Polymerization Example 3 was compression-molded at 240 °C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were cut out of these sheets and subjected to impact test, flexural test and TMA measurement. The test pieces were found to have a notched Izod impact strength of 2 kg.cm/cm, an initial flexural modulus of 28900 kg/cm² and a TMA of 111°C. The sample was inferior to the blend of Example 112 in impact strength, initial flexural modulus and heat resistance. Comparative Example 38 The evaluation of the copolymer (A) given in Table 22 was conducted in the same manner as in Comparative Example 37. The results are shown in Table 22. The sample was inferior to the compositions of Examples 115 to 117 in rigidity, heat resistance and impact strength. Example 118 A dry blend of the copolymer (A) obtained in Polymerization Example 3, the cycloolefin type random copolymer (B1) obtained in Polymerization Example 5 (hereinafter abbreviated to TDR) and an ethylene-propylene random copolymer (B2) (hereinafter abbreviated to EPR) containing an ethylene unit of 80 mol% and having a crystallinity index of 5%, a density of 0.88 g/cm³ and an intrinsic viscosity [η] of 2.2 dl/g (weight ratio = 80/5/5), was incorporated with 0.5% and 0.3%, based on the total weight of the resins (A), (B1) and (B2), of tetrakis [methylene-3-(3,5-di-t-butyl-4-hydroxyphenyl)propionate]methane and dilauryl thiodipropionate as stabilizers, respectively. The dry blend was dry-blended with 10% by weight, based on the total amount of the resins (A), (B1) and (B2), of GF. The resulting blend was kneaded at 220°C in a 30 mm twin-screw extruder and compression-molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were cut out from these sheets and subjected to impact test, flexural test and TMA measurement. The composition was found to have a notched Izod impact strength of 6 kg.cm/cm, an initial flexural modulus of 30900 kg/cm² and a TMA of 114°C. There was obtained a composition excellent in rigidity, heat resistance and impact resistance. Comparative Example 39 The evaluation of the copolymer (A) obtained in Polymerization Example 3 was compression molded at 240°C to prepare pressed sheets of 1 mm and 2 mm in thickness. Test pieces were punched out of these sheets and subjected to impact test, flexural test and TMA measurement. The sample was found to have a notched Izod impact strength of 2kg.cm/cm, an initial flexural modulus of 28900 kg/cm² and a TMA of 111°C. The sample was inferior to the blend of Example 118 in impact strength, initial flexural modulus and heat resistance. Example 119 A blend of the copolymer (A) obtained in Polymerization Example 3 and given in Table 23 TDR (B1), a styrene-butadiene-styrene block copolymer (hereinafter abbreviated SBS) (B2) (density: 0.94 g/cm³, Cariflex TR1102, a product of Shell Kagaku KK) and GF in a ratio given in Table 23 was processed and evaluated in the same manner as in Example 118. The results are shown in Table 23. There was obtained a composition excellent in rigidity, heat resistance and impact resistance. Example 120 A blend of the copolymer (A) obtained in Polymerization Example 3, an ethylene-propylene-diene copolymer (hereinafter abbreviated to EPDM) (B1) (ethylene/propylene/5-ethylidene-2-norbornene = 66/31/3 mol%, [η] = 2.1 dl/g, iodine value: 22, density: 0.87 g/cm³), SBS (B2) and GF in a blending ratio given in Table 23 was processed and evaluated in the same manner as in Example 118. The results are shown in Table 23. There was obtained a composition excellent in rigidity, heat resistance and impact resistance. Examples 121 to 123 Blends of a copolymer (A) given in Table 23, which had been prepared substantially following the procedure of Polymerization Example 3, copolymers (B1) and (B2) given in Table 23 and filler (C) in blending ratios given in Table 23 were processed and evaluated in the same manner as in Example 118. The results are shown in Table 23. There were obtained compositions excellent in rigidity, heat resistance and impact resistance. Comparative Example 40 The evaluation of the copolymer (A) given in Table 23 was conducted in the same manner as in Comparative Example 39. The results are shown in Table 23. The sample was inferior to the compositions of Examples 121 to 123 in rigidity, heat resistance and impact strength.

Claims: A cycloolefin type random copolymer composition comprising (A) a cycloolefin type random copolymer containing 40 to 85 mol % ethylene component and 15 to 60 mol % cycloolefin component represented by the following general formula (I) or (II) and having an intrinsic viscosity [η] of 0.05-10 dl/g as measured at 135°C in decalin, a softening temperature (TMA) of not lower than 70°C, and a crystallinity index of 0 to 10 % as measured by X-ray diffractometry, and (B) one or more non-rigid copolymers selected from: (i) a cycloolefin type random copolymer containing 40 to 99 mol % ethylene component, at least one α-olefin component having 3 to 20 carbon atoms and present in the range of less than the equimolar amount of the ethylene component and 1 to 40 mol % of a cycloolefin component represented by formula (I) or (II) and having an intrinsic viscosity [η] of 0.01-10 dl/g as measured at 135°C in decalin and a softening temperature (TMA) of below 70°C, (ii) an ethylene/α-olefin copolymer rubber containing an ethylene component and an α-olefin component having 3-20 carbon atoms, wherein the molar ratio of ethylene/α-olefin is in the range of from 30/70-95/5, and the crystallinity index of the ethylene/α-olefin copolymer is in the range of 0-50%, an intrinsic viscosity (η) of 0.2 to 10 dl/g as measured at 135°C in decalin, and a density of 0.82 to 0.96 g/cm³, (iii) an ethylene/α-olefin/non-conjugated diene copolymer rubber containing an ethylene component, α-olefin component having 3-20 carbon atoms and non-conjugated diene component, wherein the molar ratio of ethylene/α-olefin is in the range of from 50/50-95/5, the content of the non-conjugated diene component in the ethylene/α-olefin/non-conjugated diene copolymer is in the range of 0.5 to 10 mol %, and the crystallinity index of the ethylene/α-olefin/non-conjugated diene copolymer is in the range of 0-10%, and an intrinsic viscosity (η) of 0.1 to 10 dl/g, an iodine value of 1 to 30 and a density of 0.82 to 1.00 g/cm³, and (iv) hydrogenated styrene-butadiene-styrene block copolymer rubber or hydrogenated styrene-isoprene-styrene block copolymer rubber, having a weight-average molecular weight of Mw of 500 to 2 000 000 as measured with gel permeation chromatography (GPC) o-dichlorobenzene at 140°C and a density of 0.80 to 1.10 g/cm³. in such a proportion that the total amount of the component (B) is 5 to 100 parts by weight based on 100 parts by weight of the component (A); General formula wherein n and m are each 0 or a positive integer, ℓ is an integer of at least 3, and R¹ to R¹⁰ each represents hydrogen atom, halogen atom or hydrocarbon group. A composition according to claim 1, wherein the cycloolefin type random copolymer (B)(i) containing an ethylene component, at least one other α-olefin component and a cycloolefin component represented by formula (I) or (II) is a cycloolefin type random copolymer containing an ethylene component, a propylene component and a cycloolefin component represented by formula (I) or (II), or a cycloolefin type random copolymer containing an ethylene component, a butene component and a cycloolefin component represented by formula (I) or (II). A composition according to claim 1 or 2, wherein the ethylene/α-olefin copolymer rubber (B)(ii) is ethylene/propylene copolymer rubber or ethylene/butene-1 copolymer rubber. A composition according to claim 1, 2 or 3 wherein the ethylene/α-olefin/non-conjugated diene copolymer rubber (B)(iii) is an ethylene/propylene/non-conjugated diene copolymer rubber. A cycloolefin type random copolymer composition comprising (A) a cycloolefin type random copolymer as defined in any one of the preceding claims, (B) at least two non-rigid copolymers selected from (i), (ii), (iii) and (iv) as defined in any one of the preceding claims, and (C) an inorganic filler or organic filler, in such a proportion that the total amount of the component (B) is 1 to 100 parts by weight based on 100 parts by weight of the component (A) and the amount of the component (C) is 1 to 100 parts by weight based on 100 parts by weight of the component (A).

Inventors: AKANA YOSHINORI, IKEJIRI FUMITOSHI, ISHIMOTO AKIO, KISHIMURA KOTARO, MORIYA SATORU, YAMAMOTO YOZO, AKANA, YOSHINORI, IKEJIRI, FUMITOSHI, ISHIMOTO, AKIO, KISHIMURA, KOTARO, MORIYA, SATORU, YAMAMOTO, YOZO
Applicants: MITSUI PETROCHEMICAL IND, MITSUI PETROCHEMICAL INDUSTRIES, LTD.
Application year: 1988
Main classification: C08L23
IPC codes: C08L23, C08L65