Butene-1 polymer film and laminated film thereof

Abstract: The present invention provides a butene-1 polymer film which comprises a composition comprising 100 parts by weight of a butene-1 polymer having a melt index of 0.1-20 g/10 min, a ratio of weight-average molecular weight/number-average molecular weight of 3-12 and having a maximum melting point of 60-140°C measured by differential scanning calorimetric analysis method and 200 parts by weight or less of an olefin polymer and which has a tensile modulus of 500-8,000 kg/cm², a tear strength in TD or MD of 10 kg/cm or less and a ratio of tear strength in MD and tear strength in TD (MD/TD or TD/MD) of 4 or more. The present invention further provides a laminated film comprising the above butene-1 polymer film and a polyolefin resin layer laminated on at least one surface of the butene-1 polymer film.

Description: BACKGROUND OF THE INVENTION Field of the Invention The present invention relates to a butene-1 polymer film and a laminated film made therefrom and more particularly it relates to a butene-1 polymer film excellent in tearability and a laminated film made therefrom. Description of the Related Art Hitherto, synthetic resin films have been used for bags for packaging liquid flavoring materials, and soups. However, conventional films are difficult to tear. When a bag made of such conventional film in which liquid or pasty material is packaged is torn in an attempt to open the bag, too much force is applied thereto, resulting in inconveniences that the content is forcedly discharged from the torn part in unexpected direction to stain clothes. Therefore, the demand for an improvement in tearability of a synthetic resin film has been increased in order that application of only a slight force can tear the film as if it is cut by a knife. Under the circumstances, an easily tearable cap label comprising a film molded from a specific high-density polyethylene has been proposed for satisfying the demand. (Japanese Patent Laid-Open No.61-107378). However, this film is very low in Elmendorf tear strength, namely, 2 kg/cm or less and is insufficient in strength as bag for packing liquid flavoring materials or soups. At present, low-density polyethylene and linear low-density polyethylene are used for a sealant layer of films used for bags for packaging liquid flavoring materials or soups. However, these resins are difficult to orientate and readily form: necking and so, the film becomes difficult to tear during tearing operation. JP-A-57 051 870 discloses a self-adhesive packing film comprising two components consisting of an ethylene-propylene copolymer or an ethylene-butene-1 copolymer having a density of less than 0.930, and an ethylene-butene-1 copolymer having a density in the range of 0.930 to 0.960 and a melt index in the range of 10 to 100. The tear strength in TD (transverse direction) or MD (machine direction) and the tear strength ratio of this film are not mentioned. SUMMARY OF THE INVENTION The object of the present invention is to provide a synthetic resin film which is free from the difficulty to tear as seen in the conventional films; which one can easily start to tear without causing difficulty to tear during the tearing operation; and which can be torn as if it is cut by a knife and besides has a sufficiently high mechanical strength. In a first aspect of the invention for attaining the above object, there is provided a butene-1 polymer film, characterized by comprising a composition which comprises 100 parts by weight of a butene-1 polymer having a melt index of 0.1-20 g/10 min. a ratio of weight-average molecular weight (Mw) and number-average molecular weight (Mn) (Mw/Mn) of 3-12 and a maximum melting point of 60-140°C measured by differential scanning calorimetric analysis and 200 parts by weight or less of an olefin polymer, said film having a tensile modulus of 4,900-78,400 N/cm² (500-8,000 kg/cm²), an Elmendorf tear strength in TD (transverse direction) or MD (machine direction) of 3-10 kg/cm and a ratio of tear strength in MD and that in TD (MD/TD or TD /MD) (sometimes referred to as "tear strength ratio" hereinafter) of 4 or more. In a second aspect of the invention there is provided a laminated film comprising a butene-1 polymer film and a polyolefin resin layer laminated on at least one surface of said butene-1 polymer film, said butene-1 polymer film comprising a composition which comprises 100 parts by weight of a butene-1 polymer having a melt index of 0.1-20 g/10 min, a ratio of weight-average molecular weight (Mw) and number-average molecular weight (Mn) (Mw/Mn) of 3-12 and a maximum melting point of 60-140°C measured by differential scanning calorimetric analysis and 200 parts by weight or less of an olefin polymer and having a tensile modulus of 4,900-78,400 N/cm² (500-8,000 kg/cm²), an Elmendorf tear strength in TD or MD of 3-10 kg/cm and a tear strength ratio as defined above of 4 or more. DESCRPTION OF THE PREFERRED EMBODIMENTS Butene-1 polymer: The film of the present invention comprises a butene-1 polymer and, if necessary, an olefin polymer. The butene-1 polymer in the present invention may be any of butene-1 homopolymer, butene-1 copolymer containing another α-olefin unit such as ethylene, propylene, pentene-1 or hexene-1 and mixtures thereof. The melt index of the butene-1 polymer in the present invention is 0.1-20 g/10 min, preferably 0.3-10 g/10 min. If the melt index of the butene-1 polymer is less than 0.1 g/10 min, ununiformity in sections of the film becomes great at molding. If it is more than 20 g/10 min, the butene-1 polymer is difficult to orientate and the ratio of tear strength in TD and MD decreases and thus, the film becomes difficult to tear. In the present invention, ratio or weight-average molecular weight and number-average molecular weight (Mw/Mn) of butene-1 polymer is 3-12, preferably 3-9. When the ratio (Mw/Mn) is less than 3, the film has surface waviness at molding into a film and when it is more than 12, mechanical strengths of the film such as impact resistance are deteriorated. In the present invention, the butene-1 polymer has a maximum melting point (DSC maximum melting point) of 60-140° C measured by differential scanning calorimetric analysis method. The maximum melting point of butene-1 polymer is a peak which appears on the highest temperature side when a dried butene-1 polymer is heated from 0°C to 200°C at a heating rate of 10°C/min to measure endothermic peak, and a peak on the lowest temperature side or shoulder is a minimum melting point. When the maximum melting point of the butene-1 polymer measured by differential scanning calorimetric analysis is lower than 60°C, tackiness of the resulting film is high and its value as a product decreases and when it is higher than 140° C, the heat-sealing temperature is high and the productivity at making of bags decreases. Among the above-mentioned butene-1 polymers, butene-1 copolymers containing an ethylene unit and a butene-1 unit are preferred. Mainly, the crystallinity of copolymers can be lowered by containing an ethylene unit. Preferable butene-1 copolymers in the present invention contain the ethylene unit and the butene-1 unit within the range of 1:99 - 15:85 in molar ratio. If the molar ratio of the ethylene unit in the butene-1 copolymer is lower than the above range, the crystallinity of the copolymer is not decreased and thus the transparency of the molded film is lowered. If the molar ratio of the ethylene unit is higher than the above range, the copolymer becomes heterogeneous or viscous. In the present invention, it is especially preferred to specify the molar ratio within the range of 1:99 - 10:90. Within this range,' it is possible to provide a copolymer which can afford a molded film of further homogeneity and higher transparency. The melt index of the butene-1 copolymer is 0.1-20 g/10 min as mentioned above. The molecular weight distribution in the butene-1 copolymer, namely, the ratio of weight-average molecular weight (Mw) and number-average molecular weight (Mn) (Mw/Mn) is 3-12 as mentioned before. When the butene-1 copolymer is subjected to analysis by a differential scanning calorimeter, two endothermic peaks which indicate the minimum melting point and maximum melting point are obtained. The maximum melting point is usually within the range of 70-120° C. In the present invention, the minimum melting point is determined by a peak or shoulder which appears on the lowest temperature side when the heat absorbing peak is measured by heating a dried butene-1 copolymer mentioned above from 0°C to 200°C at a heating rate or 10°C/min. It is desired that in the preferable butene-1 copolymer of the present invention, the difference in maximum melting point and minimum melting point measured by differential scanning calorimeter (temperature difference between the maximum value and minimum value in melting point) is within the range of 2-40°C. This difference in temperature affects especially the processing characteristics and temperature (heat-sealing temperature) for laminating molded films by pressing and heating. That is, if the difference is less than 2°C, the heat-sealing temperature increases to deteriorate the heat sealability of molded films and when the difference is more than 40° C, the butene-1 copolymer becomes viscous and the moldability is reduced. Especially when the maximum melting point is lower than 70° C, the copolymer may have tackiness at room temperature and such a copolymer cannot be normally used as molding raw materials. When the maximum melting point is higher than 120°C, the heat-sealing temperature is high and sometimes a good heat sealing cannot be attained. Furthermore, the heat of fusion (determined by a straight line connecting base lines of peak or shoulder which appears by differential scanning calorimetric analysis) of the preferred butene-1 copolymer of the present invention is within the range of 8.37-104.67 J/g (2-25 cal/g). When the heat of fusion is less than 8.37 J/g (2 cal/g), the copolymer may become tacky and when it is more than 104.67 J/g (25 cal/g), the transparency of the molded films may decrease. The blocking degree (X) of ethylene in the main chain of the butene-1 copolymer can be measured by measuring ¹³C-NMR of the copolymer and identifying each triad using the method disclosed in "Macromolecules", 15 , 353, (1982) and in accordance with the following formula. X = I/E In the above formula, I is a rate of block polymerization of the ethylene chain in the copolymer and normally expressed by the following formula. E is the content of ethylene in the copolymer and is normally expressed by the following formula. In the above formulas, for example, I EEE indicates mol number of ethylene unit-ethylene unit-ethylene unit existing in the butene-1 copolymer. Similarly, I BBE , I EBE and I BEB indicate the kind of unit which comprises three monomer units in the copolymer. The blocking degree (X) of ethylene in the butene-1 copolymer which is preferred in the present invention is required to be 0.015 or less and is preferably as low as possible and thus most preferred is 0. That is, when the three monomer units in the copolymer are considered, the crystallinity of the copolymer becomes higher with an increase in the mol number of the unit which consists of only three ethylene units. Therefore, when the blocking degree (X) of ethylene is higher than 0.015, the transparency of, for example, a molded film decreases. The amount of boiling diethyl ether soluble matter in the preferred butene-1 copolymer is 3-25% by weight. In general, the solubility in boiling diethyl ether decreases with an increase in the polymerization degree of the copolymer and decreases with an increase in the crystallinity. The limitation of the content of boiling diethyl ether soluble matter of the preferred butene-1 copolymer to the above range means to limit the amount of a component of low polymerization degree in the butene-1 copolymer and crystallinity of the copolymer. Therefore, if the content of boiling diethyl ether soluble matter is less than 3% by weight, the transparency of a molded film is reduced and if it is more than 25% by weight, the content of a component of low polymerization degree increases resulting in tackiness. The butene-1 polymer of the present invention can be produced by known polymerization methods such as vapor phase polymerization, bulk polymerization or slurry polymerization. Especially, the above-mentioned preferred butene-1 copolymer can be easily produced, for example, by reacting ethylene and butene-1 in vapor phase using as a catalyst a specific solid catalyst component obtained by using as a starting material a magnesium compound which is represented by the formula MgR¹R² or Mg(OR¹) m X n (wherein R¹ and R² each represents an alkyl group, m satisfies 0≦m≦2 and n satisfies 0≦n≦2 and X represents a halogen atom), an organoaluminum compound and a specific electron donating compound. Specifically, it can be produced by experimentally setting the production conditions in the production methods disclosed in Japanese Patent Application Nos. 61-144093, 61-196255, 61-196256 61-196722 considering the above-mentioned characteristics of the copolymer. The production of the preferred butene-1 copolymer is explained referring to the method disclosed in Japanese Patent Application No. 61-196266, but the copolymer should no be limited by this method. The above-mentioned preferable butene-1 copolymer can be easily produced by reacting butene-1 and ethylene under vapor phase polymerization conditions in the presence of a catalyst comprising the following solid catalyst component (A), an organoaluminum compound (B) and an electron donating compound (C). The solid catalyst component (A) can be prepared by chlorinating at least one organomagnesium compound represented by the formula: MgR¹⁰R²⁰ (wherein R¹⁰ and R²⁰ which may be identical or different each represents an alkyl group of 1-20 carbon atoms) with at least one chlorinating agent to obtain a carrier and contacting this carrier with a halide of tetravalent titanium in the presence of an electron donating: compound at -25°C to +180°C. As the organomagnesium compound, mention may be made of, for example, alkylmagnesium compounds such as diethylmagnesium, ethylbutylmagnesium, ethylhexylmagnesium, ethyloctylmagnesium, dibutylmagnesium, butylhexylmagnesium, butyloctylmagnesium and dicyclohexylmagnesium. Examples of the chlorinating agent are chlorine gas and alkyl chloride, and it is preferred in the present invention to use chlorine gas and butyl chloride in combination. Chlorination is normally effected at 0-100° C (preferably 20-60° C, especially preferably 20-40° C). By this chlorination, a part of the alkyl group attached to the magnesium atom is substituted with chlorine atom. Since a part of the alkyl group remains, this remaining alkyl group inhibits the production of a normal crystal lattice to give a non-layerous product of very small crystal diameter having a suitable surface area and pore volume. The thus obtained non-layerous product is, if necessary, subjected to a treatment with alcohol and then, is treated with a halide of tetravalent titanium in the presence of an electron donor. The treatment with a halide of tetravalent titanium is normally effected at -25° C to +180° C. As the halide of tetravalent titanium, mention may be made of, for example, titanium tetrahalide, alkoxytitanium trihalide, alkoxytitanium dihalide and trialkoxytitanium monohalide. Titanium tetrachloride is especially preferred. As the electron donor, there may be used organic compounds containing oxygen, nitrogen, phosphorus or sulfur. As examples of the electron donor, mention may be made of amines, amides, ketones, nitriles, phosphines, phosphoamides, esters, ethers, thioethers, thioesters, acid anhydrides, acid halides, acid amides, aldehydes, organic acids and esters. Among them, preferred are esters, ethers, ketones and acid anhydrides and examples thereof are ethyl benzoate, ethyl p-methoxybenzoate, ethyl p-ethoxybenzoate, methyl toluylate, diisobutyl phthalate, benzoquinone and benzoic anhydride. It is desirable that the resulting solid catalyst component (A) has a ratio of halogen/titanium (molar ratio) of 3-200 (preferably 4-100) and a ratio of magnesium/titanium (molar ratio) of 1-90 (preferably 5-70). The organoaluminum compound (B) has no special limitation, but a trialkylaluminum is especially preferred. As the electron donating compound (C), there may be used a heterocyclic compound represented by the formula (2). (wherein R³ and R⁶ each represents a hydrocarbon group, preferably a substituted or unsubstituted saturated or unsaturated hydrocarbon of 2-5 carbon atoms and R⁴,R⁵ and R⁷ each represents a hydrogen atom or a hydrocarbon group, preferably a hydrogen atom or a substituted or unsubstituted saturated or unsaturated hydrocarbon of 1-5 carbon atoms. As the heterocyclic compound, mention may be made of, for example, 1,4-cineole, 1,8-cineole, m-cineole, pinol, benzofuran, 2,3-dihydrobenzofuran (coumarane), 2H-chromene, 4H-chromene, chroman, isochroman, dibenzofuran and xanthene. These hetorocyclic compounds may be used alone or in combination of 2 or more. Among them, 1,8-cineole is especially preferred. The composition of the catalyst used in the preparation of the above-mentioned preferable butene-1 copolymer is that the organoaluminum compound (B) is normally in an amount or 0.1-1000 times (preferably 1-500 times) the mol of titanium atom in the tetravalent titaniun compound in the solid catalyst component (A). The electron donating compound (C) is used in an amount of 0.1-500 times (preferably 0.5-200 times) the mol of titanium atom in the tetravalent titanium compound in the solid catalyst component (A). The vapor phase polymerization temperature is normally 45-80° C (preferably 50-70° C). The polymerization pressure can be optionally set within the range where a liquefaction of the starting materials does not substantially occur and is normally 98-1,470 kPa (1-15 kg/cm²). Furthermore, the molar ratio of ethylene and butene-1 introduced can be optionally set within the range of molar ratio of them in the copolymer to be obtained (namely, 1:99-15:85). Moreover, a molecular weight modifier such as hydrogen may coexist for adjustment of the molecular weight. Furthermore, an inert gas having a boiling point lower than that of butene-1 (for example, nitrogen, methane, ethane, propane) may also coexist for preventing agglomeration of the copolymer. Olefin polymer: The olefin polymers in the present invention may be homopolymers of an α-olefin other than butene-1 such as ethylene, propylene, pentene-1, hexene-1, copolymers thereof and mixtures thereof. Polypropylene is preferred. Resin composition: The butene-1 polymer film of the present invention is formed from a composition comprising 100 parts by weight of the above butene-1 polymer and 200 parts by weight or less of an olefin polymer. The olefin polymer may be 0 part by weight. When the amount of the olefin polymer is more than 200 parts by weight, the property of an easy orientation of polybutene-1 is difficult to exhibit. In the present invention, the polybutene-1 polymer and, if necessary, at least one of the olefin polymers can be blended by ordinary blending methods such as dry blending methods, and various mixing machines, kneading machines and extruders may be used therefor. Butene-1 polymer film: The butene-1 polymer film of the present invention can be produced from a material containing butene-1 polymer and olefin polymer obtained as above by known film-molding methods such as inflation molding method, T-die extrusion method and stretching method. For the thus obtained butene-1 polymer films, it is important in the present invention that they have the following properties. That is, the tensile modulus is 4,900-78,400 N/cm² (500 kg/cm² - 8,000 kg/cm²), preferably 7,840-73,500 N/cm² (800-7,500 kg/cm²), the tear strength in TD or MD is 10-3 kg/cm and the tear strength ratio (MD/TD or TD/MD) defined here is 4 times or more, preferably 4-30. If the tensile modulus is less than 4,900 N/cm² (500 kg/cm²), the stiffness of the film decreases and sometimes troubles occur in making of bags. If it is more than 78,400 N/cm² (8,000 kg/cm²), the film becomes too hard and is not preferred as bags for packing liquid If the Elmendorf tear strength of the film in TD or MD is more than 10 kg/cm, the film cannot be easily torn by fingers. When the Elmendorf tear strength of the film is less than 4 times in terms of the tear strength ratio in TD and MD, there may occur a phenomenon that the film tears obliquely and this is undesired. The thickness of the butene-1 polymer film of the present invention can be optionally determined depending on its use and normally is 10-150 µm. Polyolefin resin: The butene-1 polymer film per se is a film excellent in tearability, but when a polyolefin resin is laminated on at least one surface of the film, a laminated film superior in transparency of the present invention can be obtained. In the laminated film of the present invention, the polyolefin resin may be any of homopolymers of other α-olefins such as ethylene, propylene, pentene-1 and hexene-1, copolymers thereof and mixtures of these polymers. Low-density polyethylene, linear low-density polyethylene and polypropylene are preferred and a random polypropylene is especially preferred. Laminated film: In the laminated film of the present invention, the thickness of the butene-1 polymer film as a substrate layer is normally 7-100 µm, preferably 10-80 µm. The ratio of the thickness of the butene-1 polymer film as a substrate layer to the thickness of the polyolefin resin layer as a surface layer is 0.5-20, preferably 1-10. Within the above range, the strength of the laminated film can be sufficiently maintained and besides the characteristic of the excellent tearability of the butene-1 polymer film can be sufficiently exhibited. The method for the production of the laminated film of the present invention has no special limitation and can be optionally chosen from those customarily used for the production of laminated films. Ordinarily, there may be employed a method which comprises laminating a heat-melted film using an extruder by an extrusion laminate method, cooling and setting the laminate and then monoaxially or biaxially stretching it. The laminated film off the present invention has a tensile modulus of 4,900-117,600 N/cm² (500-12,000 kg/cm²), an Elmendorf tear strength of 12 kg/cm or less in TD or MD and a tear strength ratio as defined herebefore of at least 3.5. The laminated film of the present invention can exhibit further superiority in the tensile modulus and tear strength by additionally laminating a polyolefin resin, a polyester resin, or a polyamide resin on the polyolefin resin layer. For such laminated films of 3-5 layers, the polyolefin resin is preferably a low density polyethylene or polypropylene, the polyester resin is preferably polyester terephthalate and the polyamide resin is preferably nylon 66. Since the film or laminate of the present invention is superior in tearability and has a sufficient strength for use as containers for a liquid, they can be suitably used as containers for a liquid and troubles at the opening of the containers containing a liquid can be avoided. Furthermore, they can be utilized as a sealant layer of the film of containers for a liquid. The present invention will be explained in more detail by the following examples. Preparation Example 1 (Preparation of butene-1 homopolymer). (1) Preparation of solid catalyst component (a): 300 ml of butyloctylmagnesium (20% heptane solution) was charged in a five necked flask equipped with a mechanical stirrer, reflux condenser, a dropping funnel, a gas supplying valve and a thermometer and a solid catalyst component was prepared in the following manner. That is, nitrogen was passed through the suspension to keep an inert atmosphere in the flask. 5 liters of butyl chloride was added to the suspension from the dropping funnel at room temperature. Then, the suspension was chlorinated by adding thereto chlorine gas at a rate of 5 ml/min. Then, to the mixture was added 2.5 liters of silicone oil at 25-35° C and subsequently, thereto was added dropwise 113 ml of ethanol. During the addition of ethanol, a chlorinated precipitate was settled as a thick layer. Then, the mixture was stirred at 40° C for 1 hour. Thereafter, the temperature was raised to 75-80° C and the solution was left to stand at this temperature overnight. This solution of high temperature was gently added, by a syphon, to an excess amount of TiCl₄ (-25° C) cooled to low temperature containing diisobutyl phthalate as an electron donor to precipitate a reaction intermediate product in the low temperature TiCl₄. Then, the mixture was heated to room temperature. Thereafter, thereto was added diisobutyl phthalate as an electron donor and the temperature was raised to 100-110° C and the mixture was kept at this temperature for 1 hour. After the precipitate settled, the mixture was washed 5-6 times with heptane of 85°C and the solution was transferred to another flask by a syphon. An excess amount of TiCl₄ was further added thereto and the mixture was stirred at 110° C for 1 hour. The resulting precipitate was settled and the supernatant liquid was transferred by a syphon. Then, the resulting catalyst component was washed with heptane several times (5-6 times at 80° C) and dried under lowly reduced pressure. Thus, solid catalyst component (a) having a Ti content of 3.0% by weight was obtained. (2) Preparation of catalyst: The solid catalyst component (a) obtained in the above (1) was diluted to 2 mmols Ti/l and introduced into a catalyst supplying tank. To this tank were fed 10 mmols/l of triisobutylaluminum and 4 mmols/l of 1,8-cineole. Thereafter, 4-methylpentene-1 was fed thereto in an amount of 50 g per 1 mmol of titanium. The content in the tank was heated to 55° C and reaction was allowed to proceed for 15 minutes. Then, the reaction product was collected by filtration and dried to obtain a catalyst. (3) Preparation of butene-1 homopolymer: A fluidized bed type polymerizer of 300 mm in diameter and 100 liter in capacity was used. The catalyst obtained in the above (2) was fed from the catalyst supplying tank to the polymerizer at a feed rate of 0.3 mmols/hour in terms of Ti atom and triisobutylaluminum and 1,8-cineole were also fed at a flow rate of 30 mmols/hour and 24 mmols/hour, respectively to said polymerizer (60° C) . Butene-1, hydrogen gas and nitrogen gas were fed thereto at a gas superficial velocity in column of 35 cm/sec with adjusting partial pressure of butene-1 and nitrogen to 294 kPa (3 kg/cm²) and 392 kPa (4 kg/cm²), respectively. The discharging of the polymer was controlled so as to keep the amount of the polymer in the polymerizer at constant. The obtained butene-1 homopolymer had a melt index of 2.1 g/10 min and a density of 0.910 g/cm³. This butene-1 homopolymer had a ratio of weight-average molecular weight/number-average molecular weight of 4.8 and a heat of fusion of 64.89 J/g (15.5 cal/g) determined by differential scanning calorimetric analysis. Since this was a homopolymer, the blocking degree of ethylene was 0. Preparation Example 2 (Preparation of butene-1-ethyleme copolymer). A butene-1-ethylene copolymer (ethylene content 2.2 mols) was prepared in the same manner as in Preparation Example 1 except that butene-1 and ethylene were fed at the polymerization step. This copolymer had a melt index of 1.0 g/10 min and a density of 0.902 g/cm³. Further, this butene-1-ethylene copolymer had a ratio of weight-average molecular weight/number-average molecular weight of 5.2 and a heat of fusion of 38.09 J/g (9.1 cal/g) determined by differential scanning calorimetric analysis. The blocking degree of ethylene in this butene-1-ethylene copolymer was 0 as a result of measurement of ¹³C-NMR. This copolymer contained 12% by weight of boiling diethyl ether soluble matter. Example 1 The polymer obtained in Preparation Example 1 was subjected to inflation molding to obtain a film of 400 mm in spread width and 30 µm in thickness. An extruder manufactured by Placo Co. was used at the conditions of die diameter: 120 mm, die clearance: 1.0 mm, discharging amount: 30 kg/hour and take-up speed: 22.6 m/min. The results of measurement are shown in Table 1. Examples 2-3 and Comparative Examples 1-4 In these Examples, starting materials as shown below were used and molding was effected under the same conditions as in Example 1. Example 2 The polymer obtained in Preparation Example 2 was used. Example 3 A blend comprising 50% by weight of the polymer obtained in Preparation Example 2 and 50% by weight of polypropylene (F200S manufactured by Idemitsu Petrochemical Co.) was used. Comparative Example 1 A linear low-density polyethylene (0128N manufactured by Idemitsu Petrochemical Co.) was used. Comparative Example 2 A low-density polyethylene (F222 manufactured by Ube Industries Ltd.) was used. Comparative Example 3 A blend comprising 30% by weight of a copolymer prepared according to Preparation Example 1 using hexene-1 as a comonomer (hexene-1 content: 12% by weight) and 70% by weight of an ethylene-propylene copolymer (Tafmer A A-4090 produced by Mitsui Petrochemical Industries Ltd.) was used. Comparative Example 4 A blend comprising 3% by weight of the polymer obtained in Preparation Example 2 and 97% by weight of polypropylene (F200S manufactured by Idemitsu Petrochemical Co.) was used. The results of measurements in these Examples and Comparative Examples are shown in Table 1. Comparative Example 5 A film was obtained in the same manner as in Example 1 except that the polymer obtained in Preparation Example 2 was used and the dischaging amount was 15 kg/hr and the take-up speed was 11.3 m/min. The properties of this film were measured and the results are shown in Table 1. Comparative Example 6 A film was obtained in the same manner as in Example 1 except that the polymer obtained in Preparation Example 2 was used and die diameter was 40 mm. The properties of this film were measured and the results are shown in Table 1. Example 4 A laminated film of three layers was prepared by sandwich-laminating the film obtained in Example 2 on one surface of a LDPE film of 7 µm thickness and a nylon-66 stretched film of 20 µm thickness on another surface of the LDPE film by a laminate molding machine. This film had a tensile modulus of 102,900 N/cm² (10,500 kg/cm²) and an Elmendorf tear strength ratio of 8.6 and was excellent in tearability. Comparative Example 7 Sandwich lamination was carried out in the same manner as in Example 4 except that the film obtained in Comparative Example 1 was used in place of the film obtained in Example 2. The resulting film was elongated when it was torn and tearing could not smoothly be performed. Example 5 A three-layer laminate film of PP/PB-1/PP=2 µm/11 µm/2 µm was prepared by extrusion from a three-layer die. PP was a random polypropylene (F730N manufactured by Idemitsu Petrochemical Co.) and PB-1 was the polymer used in Example 2. This three-layer laminate film had a tensile modulus of 53,900 N/cm² (5,500 kg/cm²) and an Elmendorf tear strength ratio of 11 and was superior in tearability. A three-layer cast molding machine manufactured by Modern Machinery Co. was used and molding was effected at a draw ratio of 60 times.

Claims: A butene-1 polymer film which comprises a composition comprising 100 parts by weight of a butene-1 polymer having a melt index of 0.1-20 g/10 min, a ratio of weight-average molecular weight/number-average molecular weight of 3-12 and having a maximum melting point of 60-140 °C measured by differential scanning calorimetric analysis method and 200 parts by weight or less of an olefin polymer and which has a tensile modulus of 4,900-78,400 N/cm² (500-8,000 kg/cm²), an Elmendorf tear strength in TD (transverse direction) or MD (machine direction) of 3-10 kg/cm and a ratio of tear strength in MD and tear strength in TD (MD/TD or TD/MD) of 4 or more. A butene-1 polymer film according to claim 1 wherein the butene-1 polymer is at least one member selected from the group consisting of a butene-1 homopolymer and butene-1 ethylene copolymer. A butene-1 polymer film according to claim 2 wherein the butene-1 ethylene copolymer contains ethylene units and butene-1 units at a molar ratio of 1:99 - 15:85. A butene-1 polymer film according to claim 2 wherein the butene-1-ethylene copolymer has a blocking degree of ethylene of 0.015 or less measured by ¹³C-NMR. A butene-1 polymer film according to claim 2, wherein the butene-1 ethylene copolymer has a boiling diethyl ether soluble matter content of 3-25% by weight. A butene-1 polymer film according to claim 1 wherein the olefin polymer is a homopolymer of ethylene, propylene, pentene-1 or hexene-1, a copolymer thereof or a mixture of these polymers. A butene-1 polymer film according to claim 1 wherein the olefin polymer is polypropylene. A butene-1 polymer film according to claim 1 wherein the thickness of the butene-1 polymer film is 10-150 µm. A laminated film which comprises a butene-1 polymer film which comprises a composition comprising 100 parts by weight of a butene-1 polymer having a melt index of 0.1-20 g/10 min, a ratio of weight-average molecular weight/number-average molecular weight of 3-12 and having a maximum melting point of 60-140°C measured by differential scanning calormetric analysis method and 200 parts by weight or less of an olefin polymer and which has a tensile modulus of 4,900-78,400 N/cm² (500-8,000 kg/cm²), an Elmendorf tear strength in TD (transverse direction) or MD (machine direction) of 3-10 kg/cm and a ratio of tear strength in MD and tear strength in TD (MD/TD or TD/MD) of 4 or more and a polyolefin resin layer laminated on at least one surface of said butene-1 polymer film. A laminated film according to claim 9 wherein the butene-1 polymer is at least one member selected from the group consisting of butene-1 homopolymer and butene-1-ethylene copolymer. A laminated film according to claim 10 wherein the butene-1-ethylene copolymer contains ethylene units and butene-1 units at a molar ratio of 1:99 - 15:85. A laminated film according to claim 10 wherein the butene-1-ethylene copolymer has a blocking degree of ethylene of 0.015 or less measured by ¹³C-NMR. A laminated film according to claim 10 wherein the butene-1-ethyllene copolymer has a boiling diethyl ether soluble matter content of 3-25% by weight. A laminated film according to claim 9 wherein the polyolefin resin film comprises a homopolymer of ethylene, propylene, pentene-1 or hexene-1. a copolymer thereof or a mixture of these polymers. A laminated film according to claim 9 wherein the polyolefin resin comprises a polypropylene. A laminated film according to claim 9 wherein the thickness of the butene-1 polymer film is 7-100 µm and the ratio of the thickness of the butene-1 polymer film to that of the polyolefin resin layer is 0.5-20. A laminated film according to claim 9 wherein at least one layer selected from the group consisting of polyolefin resin layer, polyester resin layer and polyamide resin layer is additionally laminated on the polyolefin resin layer.

Inventors: YAMAWAKI TAKASHI IDEMITSU PETR, YAMAWAKI, TAKASHI IDEMITSU PETROCHEMICAL COMP. LTD
Applicants: IDEMITSU PETROCHEMICAL CO, NESTE OY, IDEMITSU PETROCHEMICAL CO. LTD.
Application year: 1988
Main classification: C08J5
IPC codes: C08J5, C08L23, B32B27